Seidman David N CV

DAVID N. SEIDMAN, Ph.D. Walter P. Murphy Professor Department of Materials Science and Engineering Northwestern University Robert R. McCormick School of Engineering and Applied Science 2220 Campus Drive Evanston IL 60208-3108 USA OFFICE TEL: (847) 491-4391 CELL: (847) 636-7072 FAX: (847) 491-7820 E-Mail: d-seidman@northwestern.edu Home Page: http://arc.nucapt.northwestern.edu CURRENT POSITIONS Walter P. Murphy Professor of Materials Science and Engineering, Northwestern University, since 1996 to present Founding Director, August 2004, and current director, Northwestern University Center for Atom-Probe Tomography (NUCAPT) Member of the National Science Foundation Funded Materials Research Science and Engineering Center Member of the Department of Energy Funded Superconducting Quantum Materials and System (SQMS) Center Member of the International Institute for Nanotechnology (IIN) at Northwestern University Co-Founder and Co-Chief Scientific Officer of NanoAl LLC, http://nanoal.com/: Founded June 2013 and sold on September 18th, 2018 to Unity Aluminum LLC (previously Braidy Industries LLC). https://www.unityal.com/leadership/ . NanoAl LLC is now located at 260 Eliot St Suite 4A, Ashland, MA 01721. It was previously located in Skokie, IL. EDUCATION Post-doctoral fellow, Cornell University, October 1964 to December 1965 Ph.D. Physical Metallurgy (major) and Physics (minor), University of Illinois at Urbana-Champaign, 1965 M.S. Physical Metallurgy, New York University, January 1962 B.S. Physical Metallurgy (major) and Physics (minor), New York University, 1960 Brooklyn Technical High School, Brooklyn, NY, 1952-1956, College Preparatory diploma with honors PROFESSIONAL SOCIETIES Member National Academy of Engineering, 2018 Member EU Academy of Sciences (EUAS), 2018 Honorary AIME Honorary Member Award 2014; nominated by the TMS (Minerals•Metals•Materials) Fellow American Academy of Arts & Sciences, 2010 Fellow American Association for the Advancement of Science, 2014 Fellow American Physical Society, Division of Condensed Matter Physics, 9/1/1983 Fellow ASM International, 2005, Fellow Inaugural class of fellows, International Field-Emission Society, 2016 Fellow John Simon Guggenheim Memorial Foundation, 1980-81 Fellow John Simon Guggenheim Memorial Foundation, 1972-73 Fellow Materials Research Society, 2010 Fellow Microscopy Society of America, 2012 Fellow TMS (Minerals•Metals•Materials), 1997; only 100 living fellows <75. Member Alexander von Humboldt Association of America Member Böhmische Physical Society Member Microanalysis Society HONORS AND AWARDS 2021 TMS (Minerals•Metals•Materials) Light Metals Subject Award-Aluminum Alloys, with David C. Dunand, Anthony De Luca, Shipeng Shu: Awarded at TMS annual meeting, March 14-18, 2021, Orlando, Florida, 2020 Microscopy Society of America (MSA) recipient of the Society’s “Distinguished Scientist - Physical for 2020,” which is the highest award of the MSA. August 2020. 2019 Microanalysis Society (MAS), “Peter Duncumb Award for Excellence in Microanalysis”; this is the highest award of the MAS. 2019 A. Frank Golick Lecturer, two invited lectures, Missouri University of Science & Technology, Department of Materials Science and Engineering, March 20th & 21st, 2019. 2019 ASM International Gold Medal award for quantitative applications of field-ion microscopy and atom-probe tomography “For solving a very broad range of materials problems in conjunction with other characterization tools.” (highest honor from the world’s largest materials science and technology society) 2018 Member, National Academy of Engineering (NAE) “For contributions to the understanding of materials at the atomic scale, leading to advanced materials and processes.” 2018 Member, EU Academy of Sciences (EUAS) 2016 Fellow of the Inaugural Class, International Field-Emission Society (for atom-probe tomography, atom-probe field-ion microscopy, field-ion microscopy and their development and numerous applications to materials science and engineering). 2015 ASM International Edward DeMille Campbell Memorial Lectureship, presented at MS&T meeting, October 7th, 2015, Columbus, Ohio, highest award from this society, which was founded in 1913. 2014 AIME Honorary Member Award; nominated by the TMS (Minerals•Metals•Materials) 2014 Fellow, American Association for the Advancement of Science 2012-2013 Sackler Lecturer, 2012-2013, of the Mortimer and Raymond Sackler Institute of Advanced Studies, Tel-Aviv University 2012 Fellow of Microscopy Society of America 2011 TMS (Minerals•Metals•Materials) Institute of Metals Lecture and the Robert Franklin Mehl Award for 2011; 2010 Fellow of the American Academy of Arts & Sciences, founded May 4th, 1780 2010 Fellow of the Materials Research Society 2010-2011 IBM Faculty Research Award 2009 Structural Materials Division Symposium: Advanced Characterization and Modeling of Phase Transformations in Metals in Honor of David N. Seidman on the occasion of his 70th birthday: TMS (Minerals•Metals•Materials) 2009 Annual Meeting, San Francisco, California; February 15th to 19th, 2009. 2008 David Turnbull Lecturer Award, Materials Research Society. Awarded, December 3rd, 2008: Boston MRS Fall meeting 2008 Presented the David Turnbull Lecture, 12-03-2008, at Boston MRS meeting 2006 Albert Sauveur Achievement Award, ASM International 2005 Fellow of ASM International National Science Foundation Creativity Extension Award 2000 Microscopy of Society of America award for Best Materials Papers appearing in Microscopy and Microanalysis, see publication numbers 218 and 219. 1997 Fellow of the TMS (Minerals•Metals•Materials); there are only 100 living fellows permitted 1996 Walter P. Murphy Professor of Materials Science and Engineering at Northwestern University 1993 Max Planck Research Prize of the Max-Planck-Gesellschaft and the Alexander Von Humboldt Stiftung awarded jointly with the late Prof. Dr. Peter Haasen, (July 21, 1927 to October 18, 1993) 1993-2002 Special Editions Editor and member of the Editorial Board of Interface Science (Kluwer Academic Publishers) 1992 Alexander Von Humboldt Stiftung Prize 1988 Teacher of the Year Award, Department of Materials Science & Engineering, Northwestern University 1988 Alexander Von Humboldt Stiftung Prize 1983 Fellow of the American Physical Society, Division of Condensed Matter Physics 1982 Chairman of the Physical Metallurgy Gordon Conference on the special topic of interfacial segregation 1982 Elected member of the Böhmische Physical Society 1980-1981 Lady Davis Visiting Professor, The Hebrew University of Jerusalem 1980-1981 Fellow of the John Simon Guggenheim Memorial Foundation 1968-1977 MITRE evaluative study of Materials Research Laboratory Programs (MTR 7764) rated my research program for the years 1968-1977 among the top twenty most highly rated major achievements sponsored by the National Science Foundation in the area of materials science. 1978 Lady Davis Visiting Professor, The Hebrew University of Jerusalem 1972-1973 Fellow of the John Simon Guggenheim Memorial Foundation 1966 Robert Lansing Hardy Gold Medal of the American Institute of Metallurgical Engineers [now the TMS (Minerals•Metals•Materials)] 1959 Tau Beta Pi, Engineering Honor Society, New York University 1959 Alpha Sigma Mu, Metallurgy Honor Society, New York University 1955 Order of the Arrow, Vigil rank, Boy Scouts of America 1952 Eagle Scout, Boy Scouts of America, February 15th, 1952 I was inducted as a member of troop number 167 in 1952, which was associated with Congregation Tifereth Israel, Jackson Heights, Queens, New York City, 31–36 88th Street; the rabbi of this synagogue was the late Samuel Berliant (1905-1972). EDITORIAL SERVICES 2012 to present Editorial Board of Review of Scientific Instruments (American Institute of Physics) 2012 to present Advisory board of Materials Research Letters (Taylor & Francis Publishers) 2012 to present Member of the scientific advisory board of NANO Science and NANO Technology series (World Scientific Publishers) 2012 Guest Editor of a volume of Annual Review of Materials Research, volume 42, 2012, with Prof. Manfred Ruehle and Prof. David R. Clarke on the subject of Three-Dimensional Tomography of Materials. 2011 to present Advisory Editor for Materials Today 2009 to present Principal Editor of NanoLIFE , www.worldscinet.com/nl Bulletin 2007 to 2013 Member of the Editorial Board of MRS Bulletin (Materials Research Society) 2004 to 2006 Editorial Board, Journal of Materials Science (Springer Publisher) 2002 to 2004 Editor-in-Chief, Interface Science (Kluwer Academic Publishers) 1996 to present Advisory Board of Materials Science Forum (Trans Tech Publications) 1993 to 2002 Special Editions Editor and member of the Editorial Board of Interface Science (Kluwer Academic Publishers) PROFESSIONAL EXPERIENCES AND SERVICES 2021 Materials Research Society (MRS), member of the committee to choose the winner of the Von Hippel award for 2021 2021 Co-organizer, with Dr. Brian Rosen, (Tel Aviv University), of the fourth workshop between Northwestern University’s and Tel Aviv University’s Departments of Materials Science and Engineering and Electrical Engineering and Computer Sciences, Tel Aviv University, January 2022 2020 Materials Research Society (MRS), member of the committee to choose the winner of the Von Hippel award for 2020 2019 to present Elected a governor of the Board of Governors of Tel Aviv University: Inauguration ceremony and meeting, May 15th to 20th, 2019 to present 2018 Naval Research Laboratory, member of external review committee, June 20th to 22nd, 2018, to evaluate their research program on structural materials 2018 Chair of the Edward DeMille Campbell Memorial Lecture Committee, ASM International for 2020 2018 Co-organizer, with Prof. Noam Eliaz (Tel Aviv University), of the third workshop between Northwestern University’s and Tel Aviv University’s Departments of Materials Science and Engineering and Electrical Engineering and Computer Sciences, July 16th to 18th, 2018 https://www.mccormick.northwestern.edu/nu-tau-workshop/ 2017 Member of the committee to choose an ASM International Edward DeMille Campbell Memorial Lecturer for 2019 2017 to Member of the advisory board of a National Center for Atom-Probe Tomography, to be located at the Technion-Israel Institute of Technology when and it is funded. 2016 Co-organizer, with Prof. Noam Eliaz (Tel Aviv University), of the second workshop between Northwestern University’s and Tel Aviv University’s Departments of Materials Science and Engineering and Electrical Engineering and Computer Sciences: September 20-22, 2016 at Northwestern University, on the themes “Energy, Sustainability, and Biomaterials,” with a sub-focus on “Water and Materials.” https://www.mccormick.northwestern.edu/news/articles/2016/09/tel-aviv-researchers-visit-for-collaborative-workshop.html 2015 Co-organizer, with Prof. Noam Eliaz (Tel Aviv University), of the inaugural workshop between Northwestern University’s and Tel Aviv University’s Departments of Materials Science and Engineering and Electrical Engineering and Computer Sciences: February 22nd to 25th, 2015 at Tel Aviv University, Ramat Aviv, Israel http://www3.tau.ac.il/tau-nu/ 2014 Member of a committee of the Council of Higher Education of Israel to evaluate three undergraduate programs in materials science and engineering in Israel. https://en.wikipedia.org/wiki/Council_for_Higher_Education_in_Israel 2013 to present Member of the International Advisory Board of the Department of Materials Science and Engineering, Tel Aviv University, Ramat Aviv, Israel https://en-engineering.tau.ac.il/materials/Committee 2013 to 2018 Co-Founder and Co-Chief Scientific Officer of NanoAl LLC, 8025 Lamon Ave, Suite 446, Skokie, IL 60077 http://nanoal.com/about.html Sold to Braidy Industries LLC on September 18th, 2018 2011 Chair of the Albert Sauveur Achievement Award Selection Committee of ASM International 2010 to 2013 Member, Materials Research Society Awards Committee 2010, and David Turnbull Lecturer Award Committee, Materials Research Society 2010 Vice Chair of the Albert Sauveur Achievement Award Selection Committee of ASM International 2010 Visiting Professor Tel Aviv University, 13-28 December 2010 under Northwestern University-Tel Aviv Program sponsored by the National Science Foundation 2009 to 2012 Member of ASM International 2009 Albert Sauveur Achievement Award Selection Committee 2009 Visiting Professor Tel Aviv University, 16 to 30 March 2009 under Northwestern University-Tel Aviv Program sponsored by the National Science Foundation. 2006 to 2012 Member of the Washington Award Commission of the Western Society of Engineers (http://www.wsechicago.org/washington_award.asp ) 2006 to 2007 ASM International Selection Committee for Fellows 2005 to 2007 ASM International Selection Committee for Henry Marion Howe Medal and Marcus A. Grossmann Young Author Award 2006 to 2008 Chair, TMS (Minerals•Metals•Materials) Fellows Award Sub-Committee 2002 to 2004 TMS (Minerals•Metals•Materials) Fellows Award Sub-Committee 2000 to 2002 President of International Field-Emission Society 1997 to 2002 Member of steering committee of the International Field-Emission Society 1996 to present Walter P. Murphy Professor of Materials Science and Engineering at Northwestern University 1989 to 1992 Member of the Executive Committee of the Materials Research Center at Northwestern University 1989 Visiting Scientist, Centre d’Etudes Nucléaires de Saclay, Section de Recherche de Métallurgie Physique, Gif sur Yvette, France 1989 & 1992 Alexander von Humboldt Senior Fellow at Institut für Metallphysik der Universität Göttingen, Göttingen, Germany 1985 to 1996 Professor, Dept. of Materials Science & Engineering, Northwestern 1985 to 1994 Scientific Consultant, Materials Science Division, Argonne National Laboratory 1984 & 1985 Summers, Visiting Scientist, Materials Science Division, Argonne National Laboratory, Argonne, Illinois 1983-1984: Head of the Division of Materials Science, The Hebrew University of Jerusalem, Israel 1981: Visiting Scientist, Departement de Recherche Fondamentale, Centre d'Etude Nucléaires de Grenoble, France 1981: Visiting Scientist, Centre National d'Etudes des Telecommunication, Meylan 1980-1981: Lady Davis Visiting Professor, The Hebrew University of Jerusalem 1976-1985: Professor, Department of Materials Science & Engineering, Cornell University 1978: Lady Davis Visiting Professor, The Hebrew University of Jerusalem 1972: Visiting Associate Professor, Physics Department, Tel-Aviv University 1970-1976: Associate Professor, Dept. of Materials Science & Engineering, Cornell University 1969-1970: Visiting Senior Lecturer, Technion-Israel Institute of Technology, Fall semester: this corresponded to the fall semester at Cornell University 1966-1970: Assistant Professor, Dept. of Materials Science & Engineering, Cornell University 1964-1965: Post-Doctoral Associate, Department of Materials Science & Engineering Cornell University, Ithaca, New York, Prof. R. W. Balluffi, mentor 1962-1964: Research assistant, Department of Mining, Metallurgical and Petroleum Engineering, University of Illinois Urbana-Champaign, Ph.D. student with Prof. R. W. Balluffi, thesis advisor, 1924 to 202? 1960-1962 Research assistant, Department of Metallurgical Engineering, New York University, M.S. student with Prof. Irving B. Cadoff, thesis advisor, 1928-2014, deceased at age 86; and Prof. Kurt L. Komarek, 1926-2016, deceased at age 90. 1960 Summer research student with Prof. I. B. Cadoff, New York University 1959 Summer research student with Prof. I. B. Cadoff, New York University 1958 Summer junior engineer, Radiation Research Corp., Manhattan, NY 1957 Summer junior engineer, Radiation Research Corp., Brooklyn, NY CONFERENCES, WORKSHOPS AND SYMPOSIA ORGANIZED 2022 Co-Organizer of the fourth Northwestern University/Tel Aviv University Workshop at Tel-Aviv University, June 20th to 23rd, 2022: With Dr. Brian Rosen of Tel-Aviv University’s department of materials science and engineering. 2020 Co-Organizer of a symposium titled “Atom-Probe Tomography,” TMS Annual Meeting: February 23-27, 2020, San Diego, CA, With Haiming Wen, Keith Knipling, Gregory Thompson, Emmanuelle Marquis, Simon Ringer, et al. 2019 iib2013 International Scientific Advisory Board Member, Paris, France, July 1-5, 2019 2019 Co-Organizer of a symposium titled “Atom-Probe Tomography,” TMS Annual Meeting: March 10-14, San Antonio, Texas, With Haiming Wen, Keith Knipling, Gregory Thompson, Emmanuelle Marquis, Simon Ringer, et al. 2018-20 Chair of ASM International Committee for Edward DeMille Campbell Memorial Lecturer Award 2018 Co-Organizer of the third Northwestern University/Tel Aviv University Workshop at Northwestern University, Evanston, Illinois, July 16th to 18th, 2018: With Prof. Noam Eliaz of Tel-Aviv University. 2018 Co-Organizer of a symposium titled “Atom-Probe Tomography,” TMS Annual Meeting, March 11th to 15th, 2018 at Phoenix, Arizona: With Haiming Wen, Chantal Sudbrack, Keith Knipling, Gregory Thompson, etc. 2016 Co-Organizer of the second Northwestern University/Tel Aviv University Workshop at Northwestern University, Evanston, Illinois, September 20th to 22nd, 2016: With Prof. Noam Eliaz of Tel-Aviv University. 2015 International Scientific Committee member of PTM 2015, the International Conference on Solid-Solid Phase Transformations in Inorganic Materials: June 28 – July 3, 2015, Whistler, British Columbia, Canada 2015 Co-Organizer of the first Northwestern University/Tel Aviv University Workshop on the subjects of semiconductors, electronic materials, thin films, and photonic materials: February 22nd to 25th, 2015, Tel Aviv University, Ramat Aviv, Israel: with Prof. Noam Eliaz of Tel-Aviv University. 2014 Scientific committee of the 2014 International Conference on Chemical Engineering and Materials Science, Venice, Italy, March 15-17, 2014 2014 Co-Organizer of the TMS (Minerals•Metals•Materials) 2014 symposium on “Gamma/Gamma-Prime Cobalt Superalloys,” San Diego, California: February 17 and 18th, 2014. 2013 iib2013 International Scientific Advisory Board Member, Halkidiki, Greece, June 23-28, 2013 2012 Member of the International Advisory Committee, 53rd International Field-Emission Symposium, University of Alabama, Tuscaloosa, Alabama, May 21-25, 2012 2012 Member of the International Advisory Committee of the First International Conference on 3D Materials Science, July 8th to 12th, 2012 2012 Member of International Advisory Board of the International Conference on Aluminum Alloys (ICAA13), Pittsburgh, PA, June 3rd to 7th, 2012 2012 Co-Organizer of Symposium titled “Solid-State Interfaces II: Toward an Atomistic-Scale Understanding of Structure, Properties, and Behavior through Theory and Experiment.” 2012 TMS Annual Meeting & Exhibition, March 11 to 15, 2012 • Orlando, FL: Co-Organizers, Xiang-Yang (Ben) Liu, Douglas E. Spearot, Guido Schmitz 2011 Co-Organizer of Materials Research Society Symposium PP on “Three-Dimensional Tomography of Materials,” with Manfred Rühle, Paul Midgely, Frank Mücklich, Yuichi Ikuhara, MRS Fall Meeting, Boston, Massachusetts, November 28th to December 2nd, 2011. 2011 Co-Organizer of Symposium titled “Phase Transformations at the Atomic Level” a symposium sponsored by the TMS Phase Transformations Committee, presently, 2011 TMS Annual Meeting, San Diego, CA, February 27 to March 3, 2011. 2009-2010 Member of International Scientific Committee of International Conference on Solid-Solid Phase Transformations in Inorganic Materials, PTM 2010, Avignon, France, June 6 to June 10, 2010. 2009-2010 iib 2010 International Scientific Advisory Board Member, Japan 2009 Co-Organizer of Symposium titled “Symposium NN: Advanced Microscopy and Spectroscopy Techniques for Imaging Materials with High Spatial Resolution,” MRS Fall Meeting, Boston, Massachusetts, November 30th to December 4th, 2009 2007 Member of the International Advisory Committee of iib2007 (Interfaces and Intergranular Boundaries 2007), Barcelona, Spain 2006 Co-Organizer of Symposium titled, “Symposium HH: Thermodynamics and Kinetics of Phase Transformations in Inorganic Materials” MRS Fall Meeting, Boston, Massachusetts, November 2006 2006 Co-Organizer of Symposium titled “Developments in 3-Dimensional Materials Science,” TMS Annual Meeting, San Antonio, Tex 2006 Co-Organizer of Symposium titled “The David G. Brandon Symposium: Advanced Materials and Characterization,” TMS Annual Meeting, San Antonio, TX 2006 Co-Organizer of Symposium titled “Point Defects in Materials,” TMS Annual Meeting, San Antonio, Texas 2005 International Organizing Committee, 6th International Workshop on Interfaces, “Interfaces by Design,” Santiago de Compostela, Spain, June 2005 2005 Co-Organizer of Symposium titled “New Insights On Solid-Solid Interfaces From Combined Observation and Modeling” at Materials Research Society Meeting, Boston, Massachusetts, November 2005. 2004 Co-Organizer of a session titled “Interfacial Segregation on an Atomic Scale: Experiments and Simulation” at American Physical Society Meeting, Montreal, Canada, March 2004 2004 Member of the International Advisory Committee, 49th International Field-Emission Symposium, Graz, Austria, July 7-12, 2004 2004 Member of the International Advisory Committee of iib2004 (Interfaces and Intergranular Boundaries 2004) Queen’s University Belfast, Northern Ireland, July 26-30, 2004 2001 Member of the International Advisory Committee, 48th International Field-Emission Symposium, Lyon, France, July 7-12, 2002 Chairman with Prof. P. W. Voorhees and Dr. D. Chatain of the Franco-American Workshop on “Nanoparticles in Materials Science,” December 2-5, 2001, Northwestern University, Evanston, Illinois 2001 Member of the International Advisory Committee, 47th International Field-Emission Symposium, July 29 to August 3, 2001, Berlin, Germany 2001 Member of the International Advisory Committee of iib2001, July 22 to 26, 2001, Haifa, Israel: this occurred during the second intifada, which resulted in a low attendence 2000 46th International Field-Emission Symposium organized with A. J. Melmed, J. Wiezorek, and W. Soffa, July 23 to 27, 2000, Pittsburgh, Pennsylvania Member of the International Advisory Committee of the Fifth International Conference on Diffusion in Materials, July 17 to 21, 2000, Paris France 1998 Member of the International Organizing Committee of Acta Materialia Workshop, “Materials Science of Interfaces: The Last Frontier?” October 26 to 30, 1998 1998 Member of the International Scientific Advisory Committee for iib98 (Interfaces and Intergranular Boundaries, 6 to 9 July 1998, Prague, Czech Republic) 1993 Co-Chairman with Richard W. Siegel and Paul D. Bristowe , “Atomic Scale Imperfections in Materials: R. W. Balluffi Fest,” Fall 1993 Meeting, Materials Research Society, November 29 to December 3. 1991 Member of the International Scientific Advisory Committee, International Conference on Diffusion and Defects in Solids DD-91- USSR: 1988 Co-Chairman with B. C. Larson and M. Rühle, Symposium on “Characterization of the Structure and Chemistry of Defects in Materials,” Materials Research Society, Boston Meeting, 1988 1986 Member of the International Scientific Advisory Committee for “Vacancies and Interstitials in Metals and Alloys,” Berlin, July 1986 1982 Chairman and organizer, Gordon Research Conference on Physical Metallurgy on the topic of “Segregation Effects” 1977 Chairman and organizer of a United States-Japan workshop on the “Applications of Field-Ion Microscopy to Materials Science,” June 1977, Cornell University, Ithaca, New York LISTINGS American Men and Women of Science Who's Who in Science and Engineering Who’s Who in the World Who's Who in America Who's Who in the Mid-West Who's Who in Engineering Who’s Who in Technology Google Scholar indices on February 11th, 2023, 32,148 citations; h-index = 83; i10-index = 401; Number of citations since 2018 = 15,246; h-index = 56; i10-index = 238 https://scholar.google.com/citations?user=xx80td4AAAAJ&hl=en\ EDUCATIONAL MISSION 20 M.S. students 53 Ph.D. students 51 Post-doctoral students and research associates Research associate professor: Dr. Dieter Isheim Research associate professor Dieter Isheim is the founding manager, 2004, and current manager of the Northwestern University Center for Atom-Probe Tomography (NUCAPT). I first met Dieter Isheim during a stay, as a von Humboldt prize awardee, at the University of Goettingen in the spring of 1989, and got to know him better during a second stay in the spring of 1992. My von Humboldt prize application was initiated by the late Prof. Peter Haasen (1927-1993), who was an extremely important physical metallurgist in Germany and the world, and he was also a mensch in the best Yiddish sense of this word. Haasen was the Ph.D. thesis advisor of Dieter Isheim and he introduced me to Dieter in the spring of 1989 in Goettingen. We initially spoke with one another in high school level French as Dieter was not used to conversational English 2 European Union Marie Curie Fellows: Professors Yaron Amouyal (currently associate professor of materials science and engineering at Technion-Israel Institute of Technology) and James A. Coakley (currently assistant professor of mechanical and aerospace engineering at University of Miami, College of Engineering) 41 plus: Visiting professors, researchers, students and professional colleagues from: Austria, Brazil, Bulgaria, Canada, England (UK), Ethiopia, Former Soviet Union, France, Germany, Greece, Hong Kong, India, Islamic Republic of Iran, Israel, Japan, Mexico, Mongolian People’s Republic, Morocco, Netherlands, People’s Republic of China, Poland, Republic of Ireland, Republic of Turkey, Socialist Republic of Vietnam, South Korea, Spain, Sweden, Switzerland, Taiwan, Thailand. Numerous undergraduate students (male, female, Caucasian, African-American, Hispanic, Asian-American), African, and high school students have worked in my laboratory since I first commenced performing research as an assistant professor at Cornell University, department of materials science and engineering, in early January 1966. I didn’t, unfortunately, keep track of this class of students until fairly recently; hence, my records are incomplete with respect to this point. Northwestern University Center for Atom-Probe Tomography I founded the Northwestern University Center for Atom-Probe Tomography (NUCAPT) in August 2004. NUCAPT is a unique university core facility at Northwestern University and the US, which has had and will have major significant impacts on the research efforts of undergraduate work-study students, senior theses, research experiences for undergraduates (REU), M.S., Ph.D. and postdoctoral students. Additionally, since 2005 underrepresented groups of students have employed the services of NUCAPT. In the department of materials science and engineering at Northwestern six professors and their graduate students (MS, PhD and postdoctoral) make extensive use of NUCAPT. Additionally, NUCAPT has users from other US universities, national laboratories, US companies, as well as international universities and companies. As of September 15th, 2015, NUCAPT is part of the NSF National Nanotechnology Coordinated Infrastructure (NNCI), which brings it into contact with an even wider range of researchers who are interested in performing APT experiments. NUCAPT has educated a large number of people in the US and abroad in the application of APT to a wide range of materials and materials science and engineering problems, which is extremely important for characterizing materials at the subnano- to nanoscale. There is no other university APT core facility in the US providing outreach to the extent that we are accomplishing this objective. My former Ph.D. students have established atom-probe tomographic laboratories at the University of Michigan, Ann Arbor, Michigan (Prof. E. A. Marquis); Naval Research Laboratory (Dr. Keith Knipling), Washington, DC; Pacific Northwest National Laboratory (Dr. Daniel Perea Dr. Daniel Perea was Prof. Lincoln Lauhon’s Ph.D. student, but he learned how to perform atom-probe tomography in NUCAPT, which has determined the successful trajectory of his research career to this date.), Richland, Washington; Sandia National Laboratory, Livermore (Dr. E. A. Marquis); and the Swiss Federal Institute of Technology (Dr. Stefan Gerstl), Zurich, Switzerland. NUCAPT serves as both a research and educational facility, continuing and extending a series of 120 Ph.D. theses, 49 postdoctoral studies, 32 undergraduate research projects, seven high school students from Evanston Township H.S., and external research projects from academia and industry, who have utilized NUCAPT since 2005. NUCAPT originally employed a conventional 3D-APT and since January 4th, 2005 it operates a LEAP tomograph, which has been upgraded four times since then to include the newest technologies: the last upgrade includes a state-of-the art ultraviolet (wavelength = 355 nm) picosecond laser system installed in 2012 Our LEAP4000X Si was upgraded in mid-October/early-November 2017 to a LEAP5000XS, which makes it the complete equivalent of a brand-new LEAP5000XS; it is manufactured by Cameca Instruments Inc, Madison, Wisconsin. It has a straight time-of-flight mass-spectrometer and a detection efficiency of 80%, which is 60% greater than that of the LEAP4000X Si, and it also has an increased field-of-view as well as improved software for data collection. The source of funding for this upgrade is an ONR DURIP grant for $1,210,000, including Northwestern University’s contribution of $310,000. This upgraded instrument has been a game-changer for NUCAPT.. Additionally, we are continuously broadening the user base to serve the needs of academicians, postdoctoral and Ph.D. students, and industrial users in both the US and internationally. Because of the significant technical advantages of the UV laser-enhanced LEAP with high specimen-throughput and ultrafast data acquisition, we are able to serve the needs of a continuously growing user base. NUCAPT provides LEAP tomography instrument time, technical support, and analytical services to researchers from academia, national laboratories, and industry, in the US and internationally. Cooperative research projects have been performed with graduate and postgraduate students from the following institutions and are we are currently continuing and expanding these collaborations: Lehigh University; Washington University in St. Louis; University of Chicago; Akron University; University of Illinois at Urbana Champaign; Illinois Institute of Technology (IIT); Massachusetts Institute of Technology (MIT); University of California – Davis; Drexel University; Missouri University of Science and Technology; University of Tennessee-Knoxville; Florida State University (FSU); The Field Museum of Natural History, Chicago, IL; Argonne National Laboratory; Fermilab (FNAL); NASA Glenn Research Laboratory; Pacific Northwest National Laboratory (PNNL); Knolls Atomic Power Laboratory; Technion: Israel Institute of Technology; Ben-Gurion University of the Negev; Tel-Aviv University; the Hebrew University of Jerusalem, École Polytechnique, Montréal; Simon-Fraser University, British Columbia; Tohoku University (Japan); Max-Planck Institute for Microstructure Physics (Germany); and the following companies: NanoAl LLC; QuesTek Innovations LLC; AO Smith; EADS Germany (Airbus); Apple; First Solar; and Toyota Research Laboratories, Japan. Additionally, more than 17 international students have performed research in NUCAPT since 2012. European Union Marie Curie Fellow J. A. Coakley spent two years (2014 to 2016) in Seidman’s group at NUCAPT to conduct advanced studies of Ti- and Co-based alloys and he is currently an assistant professor at University of Miami, Fl; and European Union Marie Curie Fellow Prof. Yaron Amouyal (currently a tenured associate professor at the Technion, Israel Institute of Technology, Haifa, Israel) spent three years working with me on nickel-based superalloys addressing the problem of “freckles” caused by problems associated with castings. As of 2015/09, NUCAPT is part of the newly created SHyNE (Soft and Hybrid Nanotechnology Experimental) research resource at Northwestern University with support from the NSF National Nanoscience Coordinated Infrastructure (NNCI) program. SHyNE provides researchers from academia, small businesses, and industry researchers access to cutting-edge nanotechnology instrumentation and expertise, which includes NUCAPT. Our participation in SHyNE are helping with our outreach activities to the USA research community for cutting-edge nanotechnology research. The education of high school, undergraduate, M.S., Ph.D., postdoctoral students, professional researchers, and underrepresented minority and women students is facilitated via workshop style training units. The training units extend over 3-4 hours per session and cover: (1) theoretical background of atom-probe tomography; (2) practical use of the ultraviolet-laser-assisted LEAP tomograph; (3) analysis of data recorded using IVAS data analysis code; and (4) preparation of specimens using electropolishing and/or a dual-beam focused-ion beam (FIB) microscope. The IVAS software package is continuously being developed by Cameca, Madison, WI. We are interacting strongly with Cameca by providing their software developers with feedback, discussing new applications, and also providing them data analysis code we have developed. We are currently beta-testing version 4.0 of IVAS for Cameca. Cameca has agreed to co-sponsor these workshops by providing personnel to help run instruments and instructors to help teach the subject of APT. NUCAPT has developed cutting-edge techniques for correlative studies that combine multiple characterization techniques, such as TEM, EBSD, EDS and EELS, and properties measurements with APT on the very same specimen. NUCAPT has developed substantial know-how and expertise for these correlative APT studies. Fig. 1. A diagram showing the multiple interactions and outreach activities at the NUCAPT research facility. At Northwestern University the NSF funded Nanoscience and Engineering Center and the Materials Research Science and Engineering Center have REU (Research Experience for Undergraduates) programs, which are aimed at women and underrepresented minority students, USA and Puerto Rico. Seidman and his research group have and will continue to supervise women and underrepresented groups of REU students from these programs and teach them how to perform LEAP tomography. In addition to supervising research projects for these diverse groups we have and will continue to conduct lessons for REU/Materials Research Institute (MRI) students to teach them LEAP tomography and how it is employed for various research projects at Northwestern University and elsewhere. In terms of undergraduate education and research projects, NUCAPT has attracted a number of students through the NSF-REU programs, in addition to work-study and senior project students from the Department of Materials Science and Engineering, who perform their thesis projects in NUCAPT. Since 2008, the following undergraduate students have performed research at NUCAPT: T. Gyger; Ms. A. Werber; N. Kim; Y. Mao; X. Yin; A. Kuo, D. Cecchetti; M. Diaz (Hispanic); J. Johnson (African-American); Ms. Lillian Novak (Brown University); L. Crosby; V. Kulkarni; R. Schuld (Northwestern), J. Finamore (Colorado School of Mines); E. Hunt; P. Maris; J. Lin; Ms. Jennie Wang (Yale University.); and pre-doctoral students Ms. Ashley (Yanyan) Huang, M. Yildirim. Ms. I-Wen Hsieh, J. McKinney, D. Cecchetti, X. Yin, J. Lin and F. Cui performed research for their M.S. theses at NUCAPT. The NSF Materials Research Institute (MRI) at Northwestern collaborates with underrepresented colleges and universities; Morehouse College, Fisk University, Hampton College, University of Texas at El Paso and Alabama A&M University. The MRI has support to develop and establish a cyber-infrastructure called the International Virtual Institute (IVI), which has a number of capabilities for information dissemination and outreach activities. NUCAPT will use this feature to provide these colleges and universities with remote access for visualizing LEAP tomographic data. Additionally, the IVI is establishing a global research gallery, where the research posters are available for viewing. These will enhance further collaborative interaction for NUCAPT with IVI for the dissemination of information concerning APT and its use for studying phenomena on a nanoscale with atomic resolution. Additionally, we will contribute to outreach programs to science teachers and college professors throughout the US via the Materials Word Modules (MWM) program at Northwestern – see http://Materialsworldmodules.org. Figure 1 summarizes the interactions and outreach programs at NUCAPT to educate and collaborate nationally and internationally on the topic of nanoscale materials characterization and development employing atom-probe tomography. SOME RESEARCH AREAS AND INTERESTS – PAST AND PRESENT Research topics: relatively recent and ongoing As part of an Energy Frontier Research Center (EFRC) on the subject of thermoelectricity --http://www.energyfrontier.us/sites/all/themes/basic/pdfs/RMSSEC.pdf -- we worked on bulk semiconducting thermoelectric materials whose nanostructures are optimized to increase the electrical conductivity and decrease the thermal conductivity. The thermal conductivity is decreased by precipitating a high number density of nanometer size precipitates, which increases the surface-to-volume ratio of matrix/precipitate interfaces and thereby enhances significantly the scattering of phonons. The electrical conductivity is increased by adding a dopant, for example, sodium in the PbTe-PbS system. We have applied atom-probe tomography to study the nanostructure: specifically, the compositions of the matrix and precipitates and the Gibbsian interfacial excesses of solute at matrix/precipitate interfaces as this affects phonon scattering compared to clean matrix/precipitate interfaces. Some journal articles are: I. D. Blum, D. Isheim, D. N. Seidman, Jiaqing He, J. Androulakis, K. Biswas, V. P. Dravid, and M. G. Kanatzidis, “Dopant Distribution in PbTe-Based Thermoelectric Materials,” Journal of Electronic Materials, 41(6), 1583-1588 (2012). K. Biswas, J. He, I. D. Blum, C.-I. Wu, T. P. Hogan, D. N. Seidman, V. P. Dravid and M. G. Kanatzidis, “Hierarchically Architectured High-Performance Bulk Thermoelectrics,” Nature 489, 414-418 (2012). J. He, I. D. Blum, H.-Q. Wang, S. N. Girard, J.-C. Zheng, G. Casillas-Garcia, M. Jose-Yacaman, D. N. Seidman, M. G. Kanatzidis, V. P. Dravid, “Morphology Control of Nanostructures: Na-doped PbTe-PbS System,” Nanoletters,12(11), 5979-5984 (2012). R. J. Korkosz, T. Chasapis, S.-H. Lo, J. W. Doak, Y.-J. Kim, C.-I. Wu, E. Hatzikraniotis, T. P. Hogan, D. N. Seidman, C. Wolverton, V. P. Dravid, M. Kanatzidis, “High ZT in p-type (PbTe)1-2x(PbSe)x(PbS)x Thermoelectric Materials,” Journal of the American Chemical Society, 136, 3225-3237 (2014). Y.-J. Kim, I. D. Blum, M. G. Kanatzidis, V. P. Dravid, and D. N. Seidman, “Three-Dimensional Atom-Probe Tomographic Analyses of Lead-Telluride Based Thermoelectric Materials,” JOM Journal, 66(11), 2288-2297 (2014). Y.-J. Kim, L.-D. Zhao, M. Kanatzidis, D. N. Seidman, “The Evolution of Nanoprecipitates in a Na-Doped PbTe-SrTe Alloy with a High Thermoelectric Figure of Merit,” ACS Applied Materials & Interfaces, 9(26), 21791-21797 (2017). ______________________________________________________________________________ Scientific studies are being performed of model nickel-based superalloys, which are used to fabricate turbine blades for commercial and military aircraft jet engines, and for turbine blades in land-based natural gas turbines used to generate electrical power. We are studying the temporally evolving microstructures on both nanometer and mesoscopic length scales. This research yields a scientific understanding of the kinetic trajectories leading to the development of the nano- and microstructures. We are basically studying the kinetics of a first-order phase transformation, which involves the decomposition of a face-centered-cubic (FCC) single-phase solid-solution into a two-phase alloy consisting of an ordered phase L12 (Ni3AlxCr1-x) phase and a disordered FCC matrix. The alloys being studied are Ni-Al, Ni-Al-Mo, Ni-Al-Cr, Ni-Al-Cr-Re, Ni-Al-Cr-W, Ni-Al-Cr-Re-W, Ni-Al-Cr-Ta, Ni-Al-Cr-Ru, Ni-Al-Cr-Ru, and Ni-Al-Cr-Re-W-Ru. The approach involves adding systematically one refractory element (Re, Ru, W, Ta) at a time to a base ternary reference alloy, Ni-Al-Cr, to understand how each elemental addition affects the ultimate microstructures. These alloys are studied using atom-probe tomography (APT), transmission electron microscopy (TEM), high-resolution electron microscopy (HREM), scanning electron microscopy (SEM), optical microscopy, and microhardness measurements. An important result of these studies is that the mechanism of coarsening is via a coagulation-coalescence mechanism and not the classic Lifshitz-Slyozov-Wagner (LSW) mechanism, which is demonstrated to be controlled by vacancy-solute binding energies out to fourth-nearest neighbor distances utilizing vacancy-mediated lattice kinetics Monte Carlo (LKMC) simulations. See the following short review articles for some details: D. N. Seidman, C. K. Sudbrack, and K. E. Yoon, “The Use of 3-D Atom-Probe Tomography to Study Nickel-Based Superalloys,” JOM 58 (12), 34-39 (2006). D. N. Seidman, “Three-Dimensional Atom-Probe Tomography: Advances and Applications,” Annual Review of Materials Research 37, 127-158 (2007). Lattice kinetic Monte Carlo (LKMC) simulations, where diffusion is mediated by a monovacancy mechanism, of the temporal kinetics of the evolution of the nano- and microstructures of Ni-Al-Cr alloys, with detailed comparisons to the experimental data acquired employing atom-probe tomography, permits us to explain the detailed kinetic trajectories and the morphological evolution of nanometer size gamma-prime precipitates. We have recently (2017) implemented the use of two mono-vacancies in the simulation cell, which permits us to extend the simulated aging time to 400 hours, thus resulting in more detailed comparisons with the experimental atom-probe tomographic results: this was accomplished in cooperation with Dr. Enrique Martinez, Los Alamos National Laboratory. Additionally, we are presently developing pair-wise interatomic potentials, to fourth nearest-neighbors, for the Ni-Al-Mo system and to perform vacancy-mediated LKMC simulations of the temporal evolution of the nanostructure. The interaction terms in the pair-wise interatomic potentials are determined from first-principles calculations using the Vienna ab initio simulation program (VASP). This research also requires the calculation of the Ni-Al-Mo phase diagram using Grand Canonical Monte Carlo simulations and parameterizing the kinetics for this system. For some detailed results on the Ni-Al-Cr, Ni-Al-Cr-RE (RE = Re, Ru, W and Ta) and Ni-Al and systems see: C. K. Sudbrack, K. E. Yoon, R. D. Noebe and D. N. Seidman, “Temporal Evolution of the Nanostructure and Phase Compositions in a Model Ni-Al-Cr Superalloy,” Acta Materialia 54, 3199-3210 (2006). C. K. Sudbrack, R. D. Noebe, and D. N. Seidman, “Compositional Pathways and Capillary Effects of Isothermal Precipitation in a Nondilute Ni-Al-Cr Superalloy,” Acta Materialia 55, 119-130 (2007). Z. Mao, C. K. Sudbrack, K. E. Yoon, G. Martin, and D. N. Seidman, “The Mechanism of Morphogenesis in a Phase Separating Concentrated Multi-Component Alloy.” Nature Materials 6, 210-216 (2007). C. Booth-Morrison, J. Weninger, C. K. Sudbrack, Z. Mao, R. D. Noebe, and D. N. Seidman, “Effects of Solute Concentrations on Kinetic Pathways in Ni-Al-Cr Alloys,” Acta Materialia, 56 3422-3438 (2008). C. Booth-Morrison, Z. Mao, and D. N. Seidman, “Tantalum and Chromium Site Substitution Patterns in the Ni3Al (L12) ’-Precipitate Phase of a Model Ni-Al-Cr-Ta Superalloy,” Applied Physics Letters, 93, 033103-1 to 033103-3 (2008). C. Booth-Morrison, R. D. Noebe, and D. N. Seidman, “Effects of a Tantalum Addition on the Temporal Evolution of a Model Ni-Al-Cr Superalloy During Phase Decomposition,” Acta Materialia, 57, 908-919 (2009). C. Booth-Morrison, Y. Zhou, R. D. Noebe, and D. N. Seidman, “On the Nanoscale Phase Decomposition of a Low-Supersaturation Ni-Al-Cr Alloy,” Philosophical Magazine, 90(1), 219-235 (2010). Z. Mao, C. Booth-Morrison, C. K. Sudbrack, G. Martin, and D. N. Seidman, “Kinetic Pathways for Phase Separation: An Atomic-Scale Study in Ni-Al-Cr Alloys,” Acta Materialia, 60(4), 1871–1888 (2012). Z. Mao, C. Booth-Morrison, E. Plotnikov, D. N. Seidman, “The Effects of Temperature and Ferromagnetism on the-Ni/’-Ni3Al Interfacial Free-Energy Calculated from First-Principles,” Journal of Materials Science, 47, 7653-7659 (2012). E. Y. Plotnikov, Z. Mao, R. D. Noebe, D. N. Seidman, “Temporal Evolution of the γ(fcc)/γ’(L12) Interfacial Width in Binary Ni-Al Alloys,” Scripta Materialia, 70, 51–54 (2014). Y. Huang, Z. Mao, R. D. Noebe, D. N. Seidman, “The Effects of Refractory Elements (Re, Ru, W and Ta) on Ni Excesses and Depletions at γ'/γ Interfaces in Ni-based Superalloys: Atom-Probe Tomographic Experiments and First-Principles Calculations,” Acta Materialia, 121, 288-298 (2016). _____________________________________________________________________________ Turbine blades in commercial and military jet engines and land-based natural gas turbines are fabricated from nickel-based superalloys and are two-phase single-crystal alloys containing as many as 10 elements. The turbine blades are produced by a highly sophisticated casting process that often results in so-called “freckles,” which are produced in the mushy zone during the solidification process and are defects that need to be eliminated to improve the performance of jet engines. “Freckles” appear on the surfaces of turbine blades and are deleterious to their high-temperature performance. Toward understanding the mechanism(s) of the formation of freckles in the mushy zone, which appear during solidification processing we studied the crystallography and chemistry of “freckles” at all length scales, from the sub-nanometer to millimeter using a wide range of experimental techniques: optical microscopy, scanning electron microscopy, transmission electron microscopy, electron-back scattering diffraction patterns in conjunction with a dual-beam focused-ion beam microscope, and atom-probe tomography. Y. Amouyal, Z. Mao, and D. N. Seidman, “Phase Partitioning and Site-Preference of Hafnium in the γ’(L12)/γ(f.c.c.) System in Ni-Based Superalloys: An Atom-Probe Tomographic and First-Principles Study,” Applied Physics Letters, 95, 161909 (2009). Y. Amouyal and D. N. Seidman, “An Atom-Probe Tomographic Study of Freckle Formation in a Nickel-Based Superalloy,” Acta Materialia, 59 (2011) 6729–6742. ______________________________________________________________________________ Temporal evolution of the nanostructures of Al-Zr and Al-Zr-Ti base alloys and their relationships to high-temperature creep properties (0.6 to 0.7 of the absolute melting point of aluminum) are investigated in detail in cooperation with Prof. D. C. Dunand since 1998. This research is aimed at the development of an aluminum alloy for use at higher temperatures than all existing aluminum alloys. We have learned a great deal about the nucleation, growth and coarsening of precipitates in systems that involve a peritectic reaction as opposed to a eutectic reaction; the latter is much simpler. This research involves the use of the following characterization tools: APT, TEM, SEM, optical microscopy, secondary ion mass-spectroscopy (SIMS), microhardness and AC electrical conductivity. Temporal evolution of the nanostructures of Al(Sc,X,) alloys, where X = Mg, Zr, Ti, and/or X = rare earth (RE) elements, or Li, and the relationships of the nanostructures to high temperature creep properties (0.6 to 0.7 of the absolute melting point of aluminum). This research is also dedicated to the development of an aluminum alloy for use at higher temperatures than all existing aluminum alloys; that is, greater than 0.6 of the absolute melting point of Al. We have learned and are learning a great deal about the nucleation, growth, and coarsening of Al3(Sc1-xXx) precipitates in these relatively simple alloys, where the decomposition of the alloy is also a first-order phase transformation. The experimental tools are atom-probe tomography, transmission electron microscopy, high resolution electron microscopy, scanning electron microscopy, microhardness measurements, AC electrical conductivity measurements, and creep measurements (in cooperation with Prof. D. C. Dunand). See the articles below concerning the search for a castable high-temperature creep resistant Al-based alloy, which can be commercialized. Initially, Al-Sc-based alloys, E. A. Marquis and D. N. Seidman, “Nanoscale Morphological Evolution of Al3Sc Precipitates in Al(Sc) Alloys,” Acta Materialia, 49, 1909-1919 (2001). were studied because of all the metallic elements in the periodic table that are soluble in aluminum Sc (Z = 21) results in the highest increment of strength per Sc atom. J. Roeyset and N. Ryum, “Scandium in Aluminum Alloys,” International Materials Review, 50, 19-44 (2005)., C. B. Fuller, D. N. Seidman, and D. C. Dunand, “Creep Properties of Coarse-Grained Al (Sc) Alloys at 300˚C,” Scripta Materialia, 40, 691-696 (1999). The reason for this is that aging a Sc-supersaturated Al-Sc alloy at, for example, 300 oC (~0.6 of the absolute melting point of Al, Tmp), in the two-phase Al plus Al3Sc(L12-structure) phase-field, one obtains a high number-density of Al3Sc(L12-structure) nanoprecipitates, with small edge-to-edge distances between them, which results in Orowan strengthening, that is, dislocation looping. The Al3Sc nanoprecipitates have a melting point of approximately 1300 oC and hence they do not readily dissolve at 300 oC as is the case for precipitates in commercial Al-Cu-based alloys, which have the highest usable operating temperatures, ~225 to ~250 oC (~0.53 to ~0.56 Tmp). The next key step in this research was the addition of zirconium to Al-Sc alloys; Zr has a significantly smaller diffusivity than does Sc and it forms a Zr-rich shell around an Al3Sc-core, albeit with some substitution of Zr on the Sc-sublattice of Al3Sc, yielding Al3(Sc1-xZrx) core-shell precipitates as demonstrated utilizing atom-probe tomography (APT). C. B. Fuller, J. L. Murray, and D. N. Seidman, “Temporal Evolution of the Nanostructure of Al(Sc,Zr) Alloys: Part I-Chemical Compositions of Al3(Sc1-XZrX) Precipitates,” Acta Materialia, 53, 5401-5413 (2005)., C. B. Fuller and D. N. Seidman, “Temporal Evolution of the Nanostructure of Al(Sc,Zr) Alloys: Part II-Coarsening of Al3(Sc1-XZrX) Precipitates,” Acta Materialia, 53, 5415-5428 (2005). It is noted that all of the Al-Sc based alloys are microalloys with ~1000 plus atomic parts per million of solute atoms. These Al3(Sc1-xZrx) core-shell nanoprecipitates coarsen slower at 375 oC (~0.7 Tmp) than do the Al3Sc nanoprecipitates, thereby demonstrating the importance of the chemically and structurally tailored Al3(Sc1-xZrx) nanoprecipitates in determining the coarsening kinetics. The basic building block of this new class of Al-superalloys are Al3(Sc1-xZrx) nanoprecipitates, which were further chemically and structurally tailored to decrease the Sc concentration A. De Luca, D. C. Dunand, D. N. Seidman, “Mechanical Properties and Optimization of the Aging of a Dilute Al-Sc-Er-Zr-Si Alloy with a High Zr/Sc Ratio,” Acta Materialia, 119, 35-42 (2016)., 8 C. Booth-Morrison, D. N. Seidman, and D. C. Dunand, “Effect of Er Additions on Ambient and High-Temperature Strength of Precipitation-Strengthened Al-Si-Zr-Sc Alloys,” Acta Materialia, 60, 3643-3654 (2012) and to increase their strength and high-temperature creep resistance C. B. Fuller, D. N. Seidman, and D. C. Dunand, “Mechanical Properties of Al(Sc,Zr) Alloys at Ambient and Elevated Temperatures,” Acta Materialia, 51(16) 4803-4814 (2003).. Additionally, the elements from groups VB (V, Nb, Ta) and VIB (Cr, Mo, W) are being utilized; for example, vanadium was incorporated into Al-Er-Sc-Zr-Si alloys D. Erdeniz, W. Nasim, J. Malik, A. R. Yost, S. Park, A. De Luca, N. Q. Vo, I. Karaman, B. Mansour, D. N. Seidman, D. C. Dunand, “Effect of Micro-Alloying Additions of Vanadium on the Microstructural Evolution and Creep Behavior of Al-Er-Sc-Zr-Si Alloys,” Acta Materialia, 124, 501-512 (2017). The basic scientific research, which utilizes the principles of physical metallurgy, lead to the development of a new class of aluminum superalloys as described briefly above. The Ford-Northwestern-Boeing Alliance, commenced 2005, and the Ford-Northwestern Alliance permitted further development and improvement of aluminum superalloys for two main industrial topics: (1) the replacement of titanium brackets that hold auxiliary power motors in place in the rear of Boeing’s airplanes with an aluminum superalloy, with an emphasis on weldability; and (2) the replacement of front-end cast-iron brake-rotors in automotive vehicles, for example, Ford Focus and Ford Fusion, with an aluminum-alloy brake-rotor; this is an Al alloy developed by NanoAl LLC, Skokie, IL 60077, for commercial use by Ford Motors. Boeing wanted an aluminum superalloy with an additional metric to the one required by Ford Motors, specifically friction-stir weldability. The aluminum alloy for Boeing, to replace titanium, is Al-Mg-Sc and its weldability was demonstrated. N. Q. Vo, D. C. Dunand, D. N. Seidman, “Atom-Probe Tomographic Study of a Friction-Stir-Welded Al-Mg-Sc alloy,” Acta Materialia, 60, 7078-7089 (2012). Seidman’s contribution has been to develop a series of microalloyed aluminum alloys that have higher temperature capabilities.  These alloys have been able to extend the operating temperature of aluminum from approximately 250 to 425 oC.  This temperature range opens up potential applications for these microalloyed aluminum alloys to include components such as brake rotor substrates and pistons. Thus, he has been able to translate successfully fundamental research utilizing basic physical metallurgy concepts concerning strengthening mechanisms in these microalloyed aluminum alloys into alloys with a practical implementation path. This has been recognized by the awarding of US Patent No. 9,551,050B2; patents for new aluminum alloys are not easily granted, and this patent is a recognition of the new and unique technology his research was able to create. K. Knipling, D. C. Dunand, and D. N. Seidman, “Criteria for Developing Castable, Creep Resistant Aluminum-Based Alloys – A Review,” Zeitschrift für Metallkunde 97, 246-265 (2006). K. E. Knipling, D. C. Dunand, and D. N. Seidman, “Nucleation and Precipitation Strengthening in Dilute Al-Ti and Al-Zr Alloys,” Metallurgical and Materials Transactions A, 38(10), 2552–2563 (2007). K. E. Knipling, D. C. Dunand, and D. N. Seidman, "Precipitation evolution in Al-Zr and Al-Zr-Ti alloys during aging at 450-600°C,” Acta Materialia, 56, 1182-1195 (2008). C. Booth-Morrison, D. C. Dunand, and D. N. Seidman, “Coarsening Resistance at 400 ˚C of Precipitation-Strengthened Al-Zr- Sc-Er Alloys,” Acta Materialia, 59, 7029-7042 (2011). C. Booth-Morrison, D. N. Seidman, and D. C. Dunand, “Effect of Er Additions on Ambient and High-Temperature Strength of Precipitation-Strengthened Al-Si-Zr-Sc Alloys,” Acta Materialia 60, 3643-3654 (2012). C. Booth-Morrison, Z. Mao, M. Diaz, C. Wolverton, D. C. Dunand, D. N. Seidman. “On the Role of Si in Accelerating the Nucleation of ’-Precipitates in Al-Zr-Sc Alloys,” Acta Materialia, 60, 4740–4752 (2012). N. Q. Vo, D. C. Dunand, D. N. Seidman, “Atom-Probe Tomographic Study of a Friction-Stir-Welded Al-Mg-Sc alloy,” Acta Materialia,60, 7078-7089 (2012). N. Q. Vo, D. C. Dunand, D. N. Seidman, “Role of Silicon on Precipitation Kinetics of Dilute Al-Zr-Sc-Er alloys,” Materials Science and Engineering A, 677, 485-495 (2016). De Luca; D. N. Seidman; D. C. Dunand, J. Boileau; B. Ghaffari, “A Low-Cost, Coarsening-Resistant, High Temperature Microalloyed Al-Zr-Sc-Er-Mo-Mn. Disclosure Record Number: 83749447, November 1, 2016. J. D. Lin, P. Okle, D. C. Dunand, D. N. Seidman, “Effects of Sb Micro-Alloying on Precipitate Evolution and Mechanical Properties of a Dilute Al-Sc-Zr Alloy,” Materials Science and Engineering A, 680, 64-74 (2017). A. De Luca, D. C. Dunand, D. N. Seidman, “Microstructural and Mechanical Properties of a Dilute Al-Sc-Er-Zr-Si Alloy” to be submitted to Acta Materialia, August (2017). ______________________________________________________________________________ Development of high-strength low-alloy (HSLA) steels that are blast resistant for Naval applications, particularly Naval hulls and decks of aircraft carriers, with an emphasis on understanding on a scientific basis how these alloys develop specific mechanical properties, which are important for blast resistance at temperatures as low as -40 oC. The mechanical properties of these steels are determined by nanometer diameter copper-rich and metal carbide precipitates. It was demonstrated that it is possible to control the number density and mean radii of these copper precipitates in a scientific manner and therefore control the pertinent requisite mechanical properties (yield stress, ultimate tensile stress, total plasticity at failure, and toughness as measured by the Charpy impact values: this research was initially performed in cooperation with the late Prof. Emeritus M. E. Fine, who passed away in 2015 at the age of 97. A deep understanding of the nucleation, growth, and coarsening behavior of concentrated multicomponent alloys of technological value was obtained from these studies. These alloys were characterized using APT, TEM, SEM, optical microscopy, microhardness measurements, tensile and Charpy impact tests. Additionally, the chemistry of the copper-rich precipitates were form were studied using first-principles calculations employing VASP and the results were compared with the experimental observations obtained using atom-probe tomography. Additionally, we studied fusion welding of these iron-copper based alloys, which demonstrated that they are readily welded, which is another metric specified by the Navy. Additionally, a thermally stable Ni-rich austenite formed utilizing a Quench-Lamellarization-Tempering (QLT) treatment for a 10 wt. % Ni martensitic steel contributes to its superior mechanical properties, specifically ballistic resistance. We analyzed the thermodynamic stability of inter-critically formed austenite and the kinetics of its formation during the QLT-treatment. Dilatometry demonstrated that the austenite formed during the L-step at 650 oC begins to transform to martensite during the quenching treatment (following the L-step), with the transformation commencing at 188 oC. Austenite formed after the T-step tempering treatment at 590oC, is, however, thermally stable even at sub-ambient temperatures, as revealed by synchrotron X-ray diffraction. 3-D ultraviolet (wavelength – 355 nm) laser assisted atom-probe tomography (APT) indicated that nanolayers of austenite grow during the T-step with a higher Ni concentration (22 at. %) on the retained austenite from the L-step containing a lower Ni concentration (14.5-17 at. %). DICTRA simulations demonstrated that the austenite growth during the T-step occurs predominantly in the Ni-rich fresh-martensitic regions, which form during quenching following the L-step. These Ni-rich regions enhance the growth kinetics of austenite during the T-step, resulting in an increase in its volume-fraction from 8.1 to 18.5 %, after 1 h of tempering at 590oC. The Ghosh-Olson thermodynamic and kinetic approach was used to predict the sub-ambient martensite-start temperature of the Ni-rich QLT-processed austenite, which cannot be predicted by empirical relationships. D. Isheim, M. S. Gagliano, M. E. Fine, and D. N. Seidman, “Interfacial Segregation at Cu-Rich Precipitates in a Low-Carbon High-Strength Steel Studied on a Sub-Nanometer Scale,” Acta Materialia 54, 841-849 (2006). S. Vaynman, D. Isheim, R. P. Kolli, S. P. Bhat, D. N. Seidman, M. E. Fine, “A High Strength Low-Carbon Ferritic Steel Containing Cu-Ni-Al-Mn Precipitates,” 39A, 363-373 (2008). R. P. Kolli and D. N. Seidman, “The Temporal Evolution of the Decomposition of a Concentrated Multicomponent Fe-Cu Based Steel,” Acta Materialia, 56, 2073-2088 (2008). M. Mulholland and D. N. Seidman, “Multiple Dispersed Phases in a High-Strength Low-Carbon Steel (HSLC): An Atom-Probe Tomographic and Synchrotron X-Ray Diffraction Study,” Scripta Materialia, 60(11), 992-995 (2009). M. D. Mulholland and D. N. Seidman, “Nanoscale Co-Precipitation and Mechanical Properties of a High-Strength Low-Carbon Steel,” Acta Materialia, 59, 1881-1897 (2011). M. D. Mulholland and D. N. Seidman, “Voltage-Pulsed and Laser-Pulsed Atom-Probe-Tomography of a Multiphase High-Strength Low-Carbon Steel,” Microscopy and Microanalysis, 17(6), 950-962 (2011). J. D. Farren, A. H. Hunter, J. N. DuPont, D. N. Seidman, C. V. Robino, E. Kozeschnik, “Microstructural Evolution and Mechanical Properties of Fusion Welds in an Iron-Copper Based Multi-Component Steel,” Metallurgical and Materials Transactions A,43, 4155-4170 (2012). J.-S. Wang, M. D. Mulholland, G. B. Olson, D. N. Seidman, “Prediction of the Yield Strength of a Secondary Hardening Steel,” Acta Materialia, 61, 4939-4952 (2013). R. P. Kolli and D. N. Seidman, “Heat Treatment of Copper Precipitation-Strengthened Steels,” ASM Handbook, Volume 4B: Heat Treatment of Iron and Steels, J. Dossett and G.E. Totten, editors, (ASM International, Materials Park, Ohio, 2014), pp. 188-203. J. T. Bono, J. N. DuPont, D. Jain, S.-I. Baik, and D. N. Seidman, “Investigation of Strength Recovery in Welds of NUCu-140 Steel through Multipass Welding and Isothermal Post-Weld Heat Treatments,” Metallurgical and Materials Transactions A, 46A(11) 5158-5170 (2015). D. Jain, D. Isheim, A. Hunter, D. N. Seidman, "Multicomponent High-Strength Low-Alloy Steel Precipitation-Strengthened by Sub-Nanometric Cu Precipitates and M2C carbides,” Metallurgical and Materials Transaction A, 47A(8), 3860-3872 (2016). D. Jain, D. Isheim, D. N. Seidman, "Carbon Redistribution and Carbide Precipitation in a High-Strength Low-Carbon HSLA-115 Steel Studied on a Nanoscale by Atom-Probe Tomography," Metallurgical and Materials Transactions A, 48(7), 3205-3219 (2017). D. Jain, D. Isheim, X. J. Zhang, G. Ghosh, and D. N. Seidman “Thermally Stable Ni-Rich Austenite Formed Utilizing Multistep Intercritical Heat-Treatments in a Low-Carbon 10 wt. % Ni Martensitic Steel,” Metallurgical and Materials Transactions A, 48A(8), 3642-3654 (2017). ______________________________________________________________________________ The key technology for the linear collider is the high gradient superconducting radio-frequency (SRF) cavity, approximately 20,000 of which will make up the accelerator. The preferred technology was initially to fabricate the cavities from high-purity niobium sheet. From the RF superconductivity point-of-view, the interface between the native niobium oxide on the surface of the cavity and near sub-surface region is the most important one. Superconducting properties of cavities depend on the chemistry and microstructure of the surface oxide and the concentration and location of impurity elements. Little was known, however, about this and the effects of low-temperature baking on the surface region. We employed APT to analyze this near surface region with a particular emphasis on the stoichiometries of the niobium oxides that form and the hydrogen concentration profiles that exist in the niobium oxides and bulk niobium. Specifically, we performed correlative atom-probe tomography and aberration-corrected STEM/EELS to study hydrogen, hydrides and oxides in ‘pure niobium. We are currently studying (started fall 2016) Nb3Sn layers (2 to 4 microns thick) on Nb cavities, with 3 mm thick walls, to understand how they will improve the behavior of the superconducting radio frequency cavities operating at 2.2 K. This research is being performed in cooperation with researchers at the technical division of Fermi National Accelerator Laboratory (FNAL). K. E. Yoon, D. N. Seidman, P. Bauer, C. Boffo, and C. Antoine, “Atomic-Scale Chemical Analyses of Niobium for Superconducting Radio Frequency Cavities,” IEEE Transactions on Applied Superconductivity 17(2), 1314-1317 (2007). K. E. Yoon, D. N. Seidman, C. Antoine, and P. Bauer, “Atomic-Scale Chemical Analyses of Niobium Oxide/Niobium Interfaces via Atom-Probe Tomography,” Applied Physics Letters, 93, 132502 (2008). Y.-J. Kim, D. N. Seidman, R. Tao, and R. F. Klie, “Direct Atomic-Scale Imaging of Nb-Hydrides and Oxides using Atom-Probe Tomography and Aberration-Corrected STEM/EELS,” ACS Nano, 7(1), 732-739 (2013). D. C. Ford, L. D. Cooley, and D. N Seidman, “First-Principles Calculations of Niobium Hydride Formation in Superconducting Radio-Frequency Cavities,” Superconductor Science and Technology, 26, 095002 (2013). D. C. Ford, L. D. Cooley, and D. N Seidman, “Suppression of Hydride Precipitates in Niobium Superconducting Radio-Frequency Cavities,” Superconductor Science and Technology, 26, 105003-105011 (2013). Y.-J. Kim, J. D. Weiss, E. E. Hellstrom, D. C. Larbalestier, D. N. Seidman, “Evidence for Composition Variations and Impurity Segregation at Grain Boundaries in High Current Density Polycrystalline K- and Co-doped BaFe2As2 Superconductors, Applied Physics Letters, 105, 162604-1 to 162604-5 (2014). Y.-J. Kim and D. N. Seidman, “Atom-Probe Tomographic Analyses of Hydrogen Interstitial Atoms in Ultrahigh Purity Niobium,” Microscopy & Microanalysis, 21, 535-543 (2015). ______________________________________________________________________________ Atom-probe tomography (APT) was used to perform 3-D composition profiling of CMOS device structures for extending CMOS technology. The feasibility of APT was demonstrated for uniform planar structures including shallow implant regions, complex metal silicide/silicon layer, and a high-K dielectric stack. This research was performed in cooperation with Prof. Yossi Rosenwaks (Tel Aviv University) who performed Kelvin probe force microscopy to resolve spatial variations in work function values on the nanometer scale and Prof. Lincoln Lauhon (Northwestern University); this research was supported by the Semiconductor Research Corporation (SRC) and IBM Watson Laboratory, Yorktown Heights, New York. The ultimate aim was to analyze chemically and electrically a single transistor on a nanometer to subnanometer scale. We also studied the kinetics of nickel/silicon reactions using synchrotron x-ray diffraction and atom-probe tomography in a correlative manner. Y.-C. Kim, P. Adusumilli, L. J. Lauhon, D. N. Seidman, S.-Y. Jung, H.-D. Lee, R. L. Alvis, R. M. Ulfig, J. D. Olson, “Three-Dimensional Atomic-Scale Mapping of Pd in Ni1-xPdxSi/Si(100) Thin Films,” Applied Physics Letters, 90, 113106-1 to 113106-3 (2007). P. Adusumilli, L. J. Lauhon, D. N. Seidman, C. E. Murray, O. Avayu, and Y. Rosenwaks, “Tomographic Study of Atomic-Scale Redistribution of Platinum During the Silicidation of Ni0.95Pt0.05/Si(100) thin-films," Applied Physics Letters, 94, 103113-1 to 103113-3 (2009). P. Adusumilli, C. E. Murray, L. J. Lauhon, O. Avayu, Y. Rosenwaks, D. N. Seidman, “Three-Dimensional Atom-Probe Tomographic Studies of Nickel Monosilicide/Silicon Interfaces on a Subnanometer Scale,” ECS Transactions, 19(1), 303- 314 (2009). P. Adusumilli, D. N. Seidman, and C. E. Murray, “Silicide-Phase Evolution and Platinum Redistribution During Silicidation of Ni0.95Pt0.05/Si(100),” Journal of Applied Physics, 112(6), 064307-064307-11 (2012). ______________________________________________________________________________ Atom-Probe Tomographic (APT) Studies of Silicon Nanowires, Silicon, Semiconductor Superlattices and Diamond Isotopic Homojunctions. We also applied APT to silicon nanowires, silicon, semiconductor homojunctions with different research groups. Specifically, we collaborated with the research groups of Prof. O. Moutanabbir (Ecole Polytechnique de Montreal), Prof. R. Yerushalmi (the Hebrew University of Jerusalem), Prof. E. Zolotoyabko (Technion) and J.-M. Zuo (University of Illinois at Urbana-Champaign). For the different physical problems addressed utilizing APT we were able to obtain detailed chemical information that could not be acquired employing other characterization techniques. In collaboration with Prof. R. Yerushalmi (Hebrew University of Jerusalem) and Prof. L.J. Lauhon (Northwestern) we studied p-n junctions in silicon nanowires processed using an ex situ processing technique, which involved the correlative use of atom-probe tomography and scanning tunneling microscopy. This permitted us to determine, for the first time, the fraction of dopant atoms that are electrically active. This research was partially supported by the US-Israel Binational Science Foundation and the McCormick School of Engineering and Applied Science of Northwestern University. O. Moutanabbir, D. Isheim, D. N. Seidman, Y. Kawamura, and K. M. Itoh, “Ultraviolet-Laser Atom-Probe Tomographic 3-D Atom-by-Atom Mapping of Isotopically Modulated Si Nanoscopic Layers,” Applied Physics Letters 98, 013111-1 to 013111-3 (2011). Y. Ashuach, Y. Kauffmann, D. Isheim, Y. Amouyal, D. N. Seidman, E. Zolotoyabko, “Atomic Intermixing in Short-Period InAs/GaSb Superlattices,” Applied Physics Letters, 100, 241604 (2012). H.-G. Kim, Y. Meng, J.-L. Rouviére, D. Isheim, D. N. Seidman, and J.-M. Zuo,” Atomic Resolution Mapping of Interfacial Intermixing and Segregation in InAs/GaSb Superlattices,” Journal of Applied Physics, 113, 103511 (2013). O. Moutanabbir, D. Isheim, H. Blumtritt, S. Senz, E. Pippel, and D. N. Seidman, “Colossal Injection of Catalyst Atoms into Epitaxial Silicon Nanowires,” Nature, 496 (April 4th), 78-82 (2013). H. Blumtritt, D Isheim, S. Senz, D. N. Seidman, and O. Moutanabbir, “Preparation of Nanowire Specimens for Laser-Assisted Atom-Probe Tomography,” Nanotechnology 25, 435704 (7 pp) (2014). S. Mukherjee, U. Givan, S. Senz, A. Bergeron, S. Francoeur, M. de la Mata, J. Arbiol, T. Sekiguchi, K. M. Itoh, D. Isheim, D. N. Seidman, and O. Moutanabbir, “Phonon Engineering in Isotopically Disordered Silicon Nanowires,” Nano Letters, 15(6), 3885-3893 (2015). O. Moutanabbir, D. Isheim, Z. Mao, D. N. Seidman, “Evidence of Sub-10 nm Aluminum-Oxygen Precipitates in a Silicon Epitaxial Layer," Nanotechnology, 27(20), 205706-205712 (2016). S. Mukherjee, H. Watanabe, D. Isheim, D. N. Seidman, and O. Moutanabbir, “Laser-Assisted Field Evaporation and Three-Dimensional Atom-by-Atom Mapping of Diamond Isotopic Homojunctions,” Nano Letters 16, 1335-1344 (2016). S. Mukherjee, D. Isheim, D. N. Seidman, O. Moutanabbir, “Mapping Isotopes in Nanoscale and Quantum Materials Using Atom-Probe Tomography,” Microscopy and Microanalysis, 22(Suppl. 3), 652-653 (2016). Z. Sun, O. Hazut, B.-C. Huang, Y.-P. Chiu, C.-S. Chang, R. Yerushalmi, L. J. Lauhon, D. N. Seidman, “Dopant Diffusion and Activation in Silicon Nanowires Fabricated by ex situ Doping: A Correlative Study via Atom-Probe Tomography and Scanning Tunneling Spectroscopy,” Nano Letters 16, 4490-4500 (2016). S. Mukherjee, N. Kodali, D. Isheim, S. Wirths, J. M. Hartmann, D. Buca, D. N. Seidman, O. Moutanabbir, “Atomic Order in Non-Equilibrium Silicon-Germanium-Tin Semiconductors.” Physical Review B: Rapid Communications, 95, 161402(R) (2017). Z. Sun, D. N. Seidman, L. J. Lauhon, “Nanowire Kinking Modulates Doping Profiles by Reshaping the Liquid-Solid Growth Interface," Nano Letters, 17(7), 4518-4525 (2017). Z. Sun, O. Hazut, R. Yerushalmi, L. J. Lauhon, D. N. Seidman, “Criteria and Considerations for Preparing Atom-Probe Tomography Specimens of Nanomaterials Using an Encapsulation Methodology, submitted to Ultramicroscopy, 3rd July (2017). ______________________________________________________________________________ The fundamental aim of this research was to utilize local-electrode atom-probe (LEAP) tomography to study the three-dimensional atomic-level structure of magnetic multilayers. Previous research indicated that the transport and magnetic properties of magnetic tunnel junction (MTJ) structures, which are used as memory storage devices and magnetic field sensors, depend strongly upon the character of the multilayer’s interfaces. LEAP tomography is ideal for characterizing the morphology and compositional character of the multilayer structure and interfaces at a sub-nanometer scale. Much progress was made on this research topic. Collaborations were established with several groups (Seagate Technology, Canon-ANELVA Corporation and NIST-Maryland) to grow high quality thin-film samples. Procedures were developed for the production of atom probe specimens from thin films grown on silicon wafers using the dual-beam FIB microscope at Argonne National Laboratory, and these specimens have been successfully analyzed in the LEAP tomograph. Interestingly, we find that the tunnel barriers in these first simple MTJs (CoFe/MgO/CoFe) were chemically asymmetric; the lower CoFe layer is found to be slightly oxidized at the CoFe/MgO interface as a result of the growth technique. Additionally, the tunneling I-V character of these structures is asymmetric as a result of this chemical asymmetry. After annealing the structure at 340 °C for 1 h the chemical and I-V asymmetry are both reduced, highlighting the direct connection between very fine scale microstructure and transport behavior. (In cooperation with Dr. Amanda Petford-Long, Argonne National Laboratory.) N. Chiaramonti, D.K. Schreiber, W.F. Egelhoff, D. N. Seidman, and A.K. Petford-Long, “Effect of Annealing on Transport Properties of MgO-based Magnetic Tunnel Junctions,” Applied Physics Letters 93, 103113 (2008). D. K. Schreiber, Y.-S. Choi, Y. Liu, D. N. Seidman, and A. K. Petford-Long, “Three-Dimensional Characterization of Magnetic Tunnel Junctions for Read-Head Applications by Atom-Probe Tomography,” Microscopy and Microanalysis 16(S2), 1912CD (2010). D. K. Schreiber, Y.S. Choi, Y. Liu, A. N. Chiaramonti, D. Djayaprawira, D. N. Seidman, A. K. Petford-Long, “Effects of Elemental Distributions on the Behavior of MgO-Based Magnetic Tunnel Junctions,” Journal of Applied Physics, 109, 103909-1 to 103909-10 (2011). D. K. Schreiber, Y.S. Choi, Y. Liu, A. N. Chiaramonti, D. Djayaprawira, D. N. Seidman, A. K. Petford-Long, “Effects of Elemental Distributions on the Behavior of MgO-Based Magnetic Tunnel Junctions,” Journal of Applied Physics, 109, 103909-1 to 103909-10 (2011). D.K. Schreiber, Y.-S. Choi, Y. Liu, D.D. Djayaprawira, D. N. Seidman, A.K. Petford-Long, “Enhanced Magnetoresistance in Naturally-Oxidized MgO-Based Magnetic Tunnel Junctions with Ferromagnetic CoFe/CoFeB Bilayers,” Applied Physics Letters 98, 232506 (2011). ______________________________________________________________________________ Segregation of impurity (unintentional) or solute (intentional) atoms at either grain boundaries or heterophase interfaces affects the mechanical and electrical properties of materials, which is a ubiquitous phenomenon is in all materials. I have had a strong research program in this area studying grain boundaries in metallic alloys and metal/ceramic heterophase interfaces, with a strong experimental emphasis on studying segregation at the atomic scale (subnanometer) employing atom-probe field-ion microscopy (APFIM), atom-probe tomography and transmission electron microscopy. Additionally, Metropolis algorithm Monte Carlo simulations are performed to study segregation of solute atoms in binary metallic alloys on an atomic scale as a function of a grain boundary’s five macroscopic and three microscopic degrees of freedom. The combination of atomic scale experimental observations and Monte Carlo simulations resulted in a significantly deeper understanding of segregation at grain boundaries than existed prior to when this research program commenced. D. N. Seidman, J. G. Hu, S.-M. Kuo, B. W. Krakauer, Y. Oh and A. Seki, "Atomic Resolution Studies of Solute-Atom Segregation at Grain Boundaries: Experiments and Monte Carlo Simulations," Colloque de Physique Colloque C1, supplément au No. 1, Tome 51, C1-47 - C1-57 (1990). D. Udler and D. N. Seidman, "Solute-Atom Segregation at Symmetrical Twist Boundaries Studied by Monte Carlo Simulation," Physica Status Solidi (b) 172, 267-286 (1992). J. G. Hu and D. N. Seidman, "Relationship of Chemical Composition and Structure on an Atomic Scale for Metal/Metal Interfaces: The W (Re) System," Scripta Metallurgica et Materialia 27 (9) 693-698 (1992). B. W. Krakauer and D. N. Seidman, "Systematic Procedures for Atom-Probe Field-Ion Microscopy Studies of Grain Boundary Segregation," Review of Scientific Instruments 63, 4071-4079 (1992). D. N. Seidman, "Experimental Investigations of Internal Interfaces in Solids," in Materials Interfaces, edited by D. Wolf and S. Yip (Chapman and Hall, London, 1992), Chapt. 2, pp. 58-84. S. M. Foiles and D. N. Seidman, "Atomic Resolution Study of Solute-Atom Segregation at Grain Boundaries: Experiments and Monte Carlo Simulations," in Materials Interfaces, edited by D. Wolf and S. Yip (Chapman and Hall, London, 1992), Chapt. 19, pp. 497-515. B. W. Krakauer and D. N. Seidman, "Absolute Atomic Scale Measurements of the Gibbsian Interfacial Excess of Solute at Internal Interfaces," Physical Review B 48, 6724-6727 (1993). J. D. Rittner, S. M. Foiles and D. N. Seidman, "Simulation of Surface Segregation Free Energies," Physical Review B 50, 12 004-12 014 (1994). D. N. Seidman, B. W. Krakauer and D. Udler, “Atomic Scale Studies of Solute-Atom Segregation at Grain Boundaries: Experiments and Simulations,” Journal of Physics and Chemistry of Solids 55, 1035-1057 (1994). J. D. Rittner, D. Udler, D. N. Seidman and Y. Oh, "Atomic Scale Structural Effects on Solute-Atom Segregation at Grain Boundaries," Physical Review Letters 74, 1115-1118 (1995). J. D. Rittner, D. Udler, D. N. Seidman and Y. Oh, "Atomic Scale Structural Effects on Solute-Atom Segregation at Grain Boundaries," Physical Review Letters 74, 1115-1118 (1995). J. D. Rittner and D. N. Seidman, "<110> Symmetric Tilt Grain Boundary Structures in FCC Metals With Low Stacking-Fault Energies," Physical Review B 54 (10), 6999-7015 (1996). J. D. Rittner and D. N. Seidman, “Solute-Atom Segregation to <110> Symmetric Tilt Grain Boundaries,” Acta Materialia 45, 3191-3202 (1997). B. W. Krakauer and D. N. Seidman, “Subnanometer Scale Study of Segregation at Grain Boundaries in an Fe (Si) Alloy,” Acta Materialia, 46 (17), 6145-6161 (1998). D. N. Seidman, “Subnanometer Scale Studies of Segregation at Grain Boundaries: Simulations and Experiments,” Annual Review of Materials Research, 32, 235-269 (2002). _____________________________________________________________________________ In 2007 an article by Sato et al. at Tohoku University, published in the journal Science, presented results on the ternary alloy Co-Al-W with a gamma(f.c.c.) plus gamma-prime(L12 structure) phase-field and a tiny gamma-prime(L12 structure) phase-field, which exhibited a two-phase microstructure consisting of gamma-prime precipitates (L12 structure) in a gamma (f.c.c.) matrix. Stress-strain diagrams, as a function of temperature, exhibited an anomalous increase in yield stress with increasing stress. Hence, these initial results for Co-Al-W alloys are analogous to what exists in Ni-Al-Cr alloys, which are the best high-temperature superalloys in existence, with many important practical applications for the aviation and electricity generating industries. The Sato et al. article caused many additional research groups around the world to commence working on Co-Al-W alloys: USA, Germany, Japan, China, England, India, General Electric Global Research in Niskayuna, New York, and NIST, Gaithersburg, Maryland. The hope for Co-based superalloys is that they have the potential to supplant Ni-based superalloys for use as turbine blades and disks in jet engines and also in land-based natural gas fired turbine engines employed for generating electricity. The increase of the maximum operating temperature of nickel-based superalloys is approaching a constant. If the maximum operating temperature of cobalt-based superalloys can be made to exceed that of nickel-based superalloys then the energies of many researchers around the world will have paid off. It is too soon to tell if this possibility will become a reality. It was quickly demonstrated experimentally that the Co3-x- y(AlxWy)-precipitate-phase is metastable with increasing temperature and that significant Ni additions are required to increase the dimensions of the gamma(f.c.c.) plus gamma-prime(L12 structure) phase-field. Additionally, other elements had to be added to the Co-Al-W alloy to obtain elevated liquidus, solidus and solvus temperatures. Specifically, Co-Al-W-Ti-Ta-B alloys were demonstrated to be necessary. Boron was added to strengthen the grain boundaries in polycrystalline specimens. Research at Northwestern University was initiated by D. N. Seidman and D. C. Dunand in cooperation with R. D. Noebe and C. K. Sudbrack at NASA Glenn Research, Cleveland, Ohio and later with E. Lass, C. Campbell and U. Kattner at NIST, Gaithersburn, Maryland. And more recently J. Smialek at NASA Glenn Research in the area oxidation studies of cobalt-based alloys. P. J. Bocchini, E. A. Lass, K.-W. Moon, M. E. Williams, C. E. Campbell, U. R. Kattner, D. C. Dunand, and D. N. Seidman, “Atom-Probe Tomographic Study of / Interfaces and Compositions in an Aged Co-Al-W Superalloy,” Scripta Materialia, 68, 563-566 (2013). D. J. Sauza, P. J. Bocchini, D. N. Seidman, D. C. Dunand, “Influence of Ruthenium on Precipitation Evolution in a Model Co-Al-W Superalloy, Acta Materialia, 117, 135-145 (2016). Q. Liu, J. A. Coakley, D. N. Seidman, D. C. Dunand, “Precipitate Evolution and Creep Behavior of a W-Free Co-Based Alloy, Metallurgical and Materials Transactions A, 47(12), 6090-6096 (2016). P. J. Bocchini, C. K. Sudbrack, R. D. Noebe, D. C. Dunand, D. N. Seidman, “Microstructure and Creep Properties of Boron- and Zirconium-Containing Cobalt-based Superalloys, Materials Science and Engineering A, 682, 260-269 (2017). J. A. Coakley, E. A. Lass, D. Ma, M. Frost, H. J. Stone, D. N. Seidman, D. C. Dunand, “Lattice Parameter Misfit Evolution During Creep of a Cobalt-Based Superalloy Single-Crystal with Cuboidal and Gamma-Prime Microstructures,” Acta Materialia, 136, 118-125 (2017). J. A. Coakley, E. A. Lass, D. Ma, M. Frost, D. N. Seidman, D. C. Dunand, H. J. Stone, “Rafting and Elastoplastic Deformation of Superalloys Studied by Neutron Diffraction,” Scripta Materialia, 134, 110-114 (2017). P. J. Bocchini, C. K. Sudbrack, ,R. D. Noebe, D. N. Seidman,, D. C. Dunand, “Effects of Ti Substitutions for Al and W in Co-10Ni-9Al-9W (at. %) Superalloys,” accepted by Acta Materialia, August 8th (2017). E. A. Lass, D. J. Sauza, D. C. Dunand, David N. Seidman, “Multicomponent Strengthened Co-Based Superalloy with an Increased Solvus Temperature and Reduced Mass Density,” to be submitted to Acta Materialia, (2017). D. J. Sauza, D. N. Seidman, D. C. Dunand, “Microstructure Evolution and High-Temperature Strength of a γ/γ’ Co-Al-W-Ti-B Superalloy,” to be submitted to Acta Materialia, (2017). P. J. Bocchini, C. K. Sudbrack, D. J. Sauza, R. D. Noebe, D. N. Seidman, D. C. Dunand, “Effect of W Reduction on Co-10Ni-6Al-6W-6Ti at.% Superalloys,” to be submitted to Acta Materialia, (2017). D. J. Sauza, D. C. Dunand, D. N. Seidman, “γ’-(L12) Precipitate Evolution during Isothermal Aging of a Co-Al-W-Ni Superalloy,” to be submitted to Acta Materialia, (2017). ______________________________________________________________________________ Scientific Accomplishments, 1965 to the present New York University, 1960-1962 For my M.S. thesis research I determined the degree of non-stoichiometry of the semiconductor PbSe, which was thought to be a line compound in the then extant Pb-Se phase diagram. The motivation for these experiments is that PbSe exhibits a reasonable thermoelectric power and hence was thought to be a suitable candidate for small refrigeration systems in remote areas that are not hooked up to an electrical grid system. To determine the degree of nonstoichiometry I grew single crystals of PbxSey with values of x and y that differed from unity, thereby creating p-n junctions in the crystals at different positions. From the locations of the p-n junctions in the single crystals I was able to calculate the range of stability of PbSe over a reasonable temperature range. Additionally, I redetermined a portion of the Pb-Se phase diagram and showed that a then recently postulated monotectic reaction did not exist. Ironically, I returned to the subject of bulk thermoelectric materials as a result of an Energy Frontier Research Center (EFRC) on this subject at Northwestern University many years later. D. N. Seidman, I. B. Cadoff, K. L. Komarek and E. Miller, "Note on the Pb-Se Phase Diagram," Transactions of the American Institute of Metallurgical Engineers 221, 1269-1270 (1961). D. N. Seidman, M.S. thesis, “The Stoichiometry of Lead Selenide and Some Phase Relations in the Lead-Selenium System,” New York University, January 1962. University of Illinois at Urbana-Champaign, 1962-1964 For my Ph.D. thesis research, at the University of Illinois at Urbana-Champaign, I demonstrated that dislocations are the dominant sources of vacancies in a polycrystalline metal, which was accomplished by performing up-quenching experiments on gold and measuring the kinetics of vacancy production in the millisecond range; my Ph.D. thesis supervisor was Robert W. Balluffi, who is alive and well at age 93. These experiments also demonstrated that the efficiency of dislocation climb is a function of the vacancy subsaturation; that is, the chemical potential of a vacancy determines the climb velocity, that is, the kinetics of vacancy producdtion. Additionally, these experiments settled a controversy, precipitated by a theory of the late Prof. Doris Kuhlmann-Wilsdorf (University of Virginia), which asserted that “old” dislocations cannot climb. D. N. Seidman, Ph.D. thesis, “Sources of Thermally Generated Vacancies in Single-Crystal and Polycrystalline Gold,” University of Illinois at Urbana-Champaign,” June 1965. D. N. Seidman and R. W. Balluffi, "Sources of Thermally Generated Vacancies in Single-Crystal and Polycrystalline Gold," Physical Review 139, A1824-A1840 (1965). Cornell University, 1965-1985 As a postdoctoral student, at Cornell University, I set-up a laboratory to study the kinetics of vacancy decay at elevated temperatures by quenching from one elevated temperature to a lower elevated temperature without quenching to room temperature, which constituted a completely new approach to this problem. This was accomplished with fully automated electronic equipment, which circumvented problems associated with quenching to room temperature and provided a deeper understanding into the efficiency of dislocation climb as a function of the vacancy supersaturation in gold; the kinetics of vacancy decay at the lower elevated temperature were followed at temperature using resistivity measurements. Between the up-quenching experiments and these down-quenching experiments it was found that there is fundamental asymmetry in how dislocations climb in the presence of sub- and super-saturations of vacancies, which had not been understood and was clarified. Based on these experimental results a correlation was found between the chemical potential of a vacancy and the efficiency of dislocation climb; that is, the velocity of climb for the experimental conditions compared to diffusion-limited climb, which is the fastest possible climb velocity. D. N. Seidman and R. W. Balluffi, "On the Efficiency of Dislocation Climb in Gold," Physica Status Solidi 17, 531-541 (1966). D. N. Seidman and R. W. Balluffi, "Dislocations as Sources and Sinks for Point Defects in Metals," in Lattice Defects and their Interactions edited by R. R. Hasiguti (Gordon-Breach, New York, 1968), pp. 913-960. C. G. Wang, D. N. Seidman and R. W. Balluffi, "Annealing Kinetics of Vacancy Defects in Quenched Gold at Elevated Temperatures," Physical Review 160, 553-569 (1968). ______________________________________________________________________________ As an assistant professor, at Cornell University (department of materials science and engineering), I established the first laboratory in the world dedicated to study quantitatively the fundamental properties of point defects in quenched or irradiated metals employing an ultrahigh vacuum field-ion microscope (FIM); I became an assistant professor in January 1966. Ultrahigh vacuum (UHV) FIMs were designed and fabricated, as well as liquid-helium cryostats, which permitted FIM specimens to be cooled to temperatures as low as 10 K. Two UHV FIMs were attached to a low-energy (60 kV for singly-charged ions) heavy-metal ion accelerator, with magnetic mass analyses of the ion beam, utilizing three differential stages of pumping, which allowed FIM specimens to be irradiated in situ under UHV conditions at temperatures as low as 10 K. Firstly, using an UHV-FIM, the direct observations of individual mono- and divacancies were made in quenched platinum specimens, thereby yielding the first direct experimental measurement of the ratio of mono- to divacancy concentrations, which yielded an absolute value of the binding free energy of a divacancy that was model independent. This result permitted a detailed explanation of diffusion in platinum to be made in terms of the mono- and divacancy concentrations, without adjustable fitting parameters. The experiments also yielded an absolute value for the specific resistivity of a vacancy in platinum. A. S. Berger, D. N. Seidman and R. W. Balluffi, "A Quantitative Study of Vacancy Defects in Quenched Platinum by Field-Ion Microscopy and Electrical Resistivity Measurements: I. Experimental Results," Acta Metallurgica 21, 123-135 (1973). S. Berger, D. N. Seidman and R. W. Balluffi, "A Quantitative Study of Vacancy Defects in Quenched Platinum by Field-Ion Microscopy and Electrical Resistivity Measurements: II. Analysis," Acta Metallurgica 21, 136-147 (1973). D. N. Seidman, "The Direct Observation of Point Defects in Irradiated or Quenched Metals by Quantitative Field-Ion Microscopy," Journal of Physics F: Metal Physics 3, 393-421 (1973). ______________________________________________________________________________ I developed an extensive program to study experimentally the character of displacement cascades produced by single heavy metal-ions, which were studied in detail using the above described system for irradiating in situ metal FIM specimens. This research yielded the distributions of vacancies within displacement cascades as revealed by radial distribution functions (RDFs) and demonstrated how the RDFs change systematically with the mass of an incident ion at constant incident energy; the studies were performed on both tungsten and platinum specimens. The experimental results also demonstrated that the self-interstitials created within displacement cascades were transported away via focused replacement collision sequences. The result of this program of research was a detailed insight into the primary state of radiation damage in the absence of thermal migration of the point defects created. To accomplish this required the development of what is currently called three-dimensional (3-D) field-ion microscopy, which involved dissecting a field-ion microscope specimen in a highly controlled manner on an atom-by-atom basis and an atomic-plane by atomic-plane basis. In between each field-evaporation pulse an FIM image was recorded on 35 mm cine film, which had a 1000-foot cartridge. Each 1000 feet of 35 mm cine film was analyzed using a two-dimensional analysis instrument that permitted us to record the positions of every atom in a given {hkl} plane and then using software to reconstruct a 3-D map of atoms, vacancies and self-interstitial atoms. All of the above was reported in an unpublished Cornell University Materials Science Report #1159 by R. M. Scanlan et al., 1969. Recently a modern version of what we had performed in 1969 has been accomplished using a charge coupled device (CCD) camera by researchers at the University of Rouen and the University of Oxford, F. Vurpillot et al., (2017). R. M. Scanlan, D. L. Styris, D. N. Seidman and D. G. Ast, "An Image Intensification and Data Recording Analysis System for a Field-Ion Microscope," Cornell University Materials Science Center Report #1159, April 24th (1969). (27 pages and 14 figures) L. A. Beavan, R. M. Scanlan and D. N. Seidman, "The Defect Structure of Depleted Zones in Irradiated Tungsten," Acta Metallurgica 19, 1339-1350 (1971). K. L. Wilson and D. N. Seidman, "A Field-Ion Microscope Study of the Point Defect Structure of a Depleted Zone in Ion (W+) Irradiated Tungsten," in Defects and Defect Clusters in B.C.C Metals and their Alloys Nuclear Metallurgy, edited by R. J. Arsenault (University of Maryland, 1973), Vol. 28, pp. 216-239. D. N. Seidman, "The Study of Radiation Damage in Metals with the Field-Ion and Atom-Probe Microscopes," Surface Science 70, 532-565 (1978). C.-Y. Wei and D. N. Seidman, "Direct Observation of the Vacancy Structure of Depleted Zones in Tungsten Irradiated with 30 keV W+, Mo+ or Cr+ Ions at 10 K," Applied Physics Letters 34, 622-624 (1979). M. I. Current and D. N. Seidman, "Sputtering of Tungsten: A Direct View of a Near Surface Depleted Zone Created by a Single 30 keV 63Cu+ Projectile," Nuclear Instruments and Methods 170, 377-381 (1980). D. N. Seidman, M. I. Current, D. Pramanik and C. -Y. Wei, "Direct Observation of the Primary State of Radiation Damage of Ion-Irradiated Tungsten and Platinum," Nuclear Instruments and Methods 182/183, 477-481 (1981). C-.Y. Wei and D. N. Seidman, "The Spatial Distribution of Self-Interstitial Atoms Around Depleted Zones in Tungsten Ion-Irradiated at 10 K," Philosophical Magazine A 43, 1419-1439 (1981). M. I. Current, C. -Y. Wei and D. N. Seidman, "Single Atom Sputtering Events: Direct Observation of Near Surface Depleted Zones," Philosophical Magazine A 43, 103-138 (1981). C.-Y. Wei, M. I. Current and D. N. Seidman, "Direct Observation of the Primary State of Damage of Ion-Irradiated Tungsten: I. Three-Dimensional Spatial Distributions of Vacancies," Philosophical Magazine A 44, 459-491 (1981). D. N. Seidman, M. I. Current, D. Praminik, C.-Y. Wei, “Direct Observations of the Primary State of Ion-Irradiated Tungsten and Platinum,” Nuclear Instruments and Methods, 182, 477-481 (1981). D. N. Seidman, M. I. Current, D. Praminik and C. Y. Wei, "Atomic Resolution Observations of the Point Defect Structure of Depleted Zones in Ion-Irradiated Metals," Journal of Nuclear Materials 108 & 109, 67-68 (1982). M. I. Current, C. -Y. Wei and D. N. Seidman, "Direct Observation of the Primary State of Damage of Ion-Irradiated Tungsten: II. Definitions, Analyses and Results," Philosophical Magazine A, 47, 407-434 (1983). D. Pramanik and D. N. Seidman, "The Irradiation of Tungsten with Metallic Diatomic Molecular Ions: Atomic Resolution Observations of Depleted Zones," Nuclear Instruments and Methods 209/210, 453-459 (1983). D. Pramanik and D. N. Seidman, "Atomic Resolution Observations of Nonlinear Depleted Zones in Tungsten Irradiated with Metallic Diatomic Molecular Ions," Journal of Applied Physics 54, 6352-6367 (1983). D. Pramanik and D. N. Seidman, "Atomic Resolution Study of Displacement Cascades in Ion-Irradiated Platinum," Journal of Applied Physics 60, 137-150 (1986). R. S. Averback and D. N. Seidman, "Energetic Displacement Cascades and Their Roles in Radiation Effects," Materials Science Forum 15-18, 963-984 (1987). D. N. Seidman, R. S. Averback, and R. Benedek, "Displacement Cascades: Dynamics and Atomic Structure," Physica Status Solidi (b) 144, 85-104 (1987). F. Vurpillot, F. Danoix, M. Gilbert, S. Koelling, M. Dagan, D. N. Seidman, “True Atomic-Scale Imaging in Three Dimensions: A Review of the Rebirth of Field-Ion Microscopy,” Microscopy and Microanalysis, published online March 24th, 2017, https://www.cambridge.org/core/journals/microscopy-and-microanalysis/article/true-atomicscale-imaging-in-three-dimensions-a-review-of-the-rebirth-of-fieldion-microscopy/653239ACADA33D508D6812467208837F ______________________________________________________________________________ Additionally, the elastically deposited energy, from a large number of implanted ions, was determined as a function of depth by measuring the profile of the vacancy damage created in platinum specimens. This was the first direct experimental determination of the elastically deposited energy and perhaps the only one to date. Physically the elastically deposited energy is the energy expended in creating point defects and by definition requires detection of all the vacancies and self-interstitial atoms (SIAs). This is a unique approach to determine this basic physical quantity, associated with radiation damage, because it has atomic scale resolution. D. Pramanik and D. N. Seidman, "Direct Determination of a Radiation Damage Profile with Atomic Resolution in Ion-Irradiated Platinum," Applied Physics Letters 43, 639-641 (1983). _____________________________________________________________________________ The diffusivities of self-interstitial atoms in W, Pt, Pt-Au, Mo, Mo-Re, ordered Ni4Mo, and ordered Pt3Co were directly determined from in situ irradiation experiments using the apparatus described above. For these experiments specimens were irradiated at 10 K, which is below the temperature where self-interstitial atoms (SIAs) migrate in these metals. The FIM specimens were then warmed continuously from 10 K, with the surface of the specimens serving as a strong sink for SIAs; this experiment is essentially an isochronal warming experiment. The SIAs were detected by the contrast effects they produced when they arrived at the free surface, and the temperature at which they migrated freely was detected by a peak in the flux of SIAs arriving at the free surface. A mathematical diffusion model was developed to extract the diffusivities and migration energies of the migrating SIAs. Additionally, the experiments yielded the volume change of migration of a SIA, since an FIM specimen is subjected, to first order, to a negative hydrostatic pressure. Similar experiments performed on specimens of the alloys Pt-Au and Mo-Re provided direct evidence for the trapping of SIAs at solute atoms. Additionally, experiments on the ordered alloys Ni4Mo and Pt3Co yielded direct evidence for two different geometric forms of the SIAs in these ordered compounds. R. M. Scanlan, D. L. Styris and D. N. Seidman, "An In Situ Field-Ion Microscope Study of Irradiated Tungsten: I. Experimental Results," Philosophical Magazine 23, 1439-1457 (1971). R. M. Scanlan, D. L. Styris and D. N. Seidman, "An In Situ Field-Ion Microscope Study of Irradiated Tungsten: II. Analysis and Interpretation," Philosophical Magazine 23, 1459-1478 (1971). P. Petroff and D. N. Seidman, "Direct Observation of Long-Range Migration of Self-Interstitial Atoms in Stage I of Irradiated Platinum," Applied Physics Letters 18, 518-520 (1971). D. N. Seidman, K. L. Wilson and C. H. Nielsen, Comment on "Free Migration of Interstitials in Tungsten," Physical Review Letters 35, 1041-1042 (1975). D. N. Seidman, K. L. Wilson and C. H. Nielsen, "The Study of Stages I to IV of Irradiated or Quenched Tungsten and Tungsten Alloys by Field-Ion Microscopy," in The Proceedings of the International Conference on Fundamental Aspects of Radiation Damage in Metals, edited by M. T. Robinson and F. W. Young Jr. (National Technical Information Service, U. S. Department of Commerce, Springfield, Virginia, 1975), pp. 373-396. C.-Y. Wei and D. N. Seidman, "The Stage II Recovery Behavior of a Series of Ion-Irradiated Platinum (Gold) Alloys as Studied by Field-Ion Microscopy," Radiation Effects 32, 229-249 (1977). K. L. Wilson and D. N. Seidman, "The Point-Defect Structure in Stage I of Ion or Electron-Irradiated Tungsten as Studied by Field-Ion Microscopy," Radiation Effects 33, 149-160 (1977). K. L. Wilson, M. I. Baskes and D. N. Seidman, "An In Situ Field-Ion Microscope Study of the Recovery Behavior of Ion-Irradiated Tungsten and Tungsten Alloys," Acta Metallurgica 28, 89-102 (1980). ______________________________________________________________________________ The ordered alloys Ni4Mo and Pt3Co were used to study directly and quantitatively elastically deposited energy profiles. This was accomplished by measuring the change in the Bragg-Williams long-range order (LRO) parameter as a function of depth from the irradiated surface of a FIM nanotip. The classical definition of the LRO could be used directly because of changes in the contrast of the FIM patterns on an atomic scale. Additionally, the elastically deposited energy profiles were determined as a function of both ion energy and crystallographic <hkl> direction. These results yielded one of the only experimental checks of ion-solid scattering theories at low energies, and also provided direct evidence for channeling of the implanted ions at low energies; that is, less than 1500 Vdc. J. Aidelberg and D. N. Seidman, "Direct Determination of Radiation Damage Profiles in the Order-Disorder Alloy Pt3Co Irradiated with Low-Energy (500-2500 eV) Ne Ions," Nuclear Instruments and Methods 170, 413-417 (1980). J. Aidelberg and D. N. Seidman, "Atomic Resolution Observations of Radiation-Damage Profiles in Ordered Alloys," Materials Science Forum 15-18, 1047-1052 (1987). J. Aidelberg and D. N. Seidman, "Direct Observation of Uncorrelated Long-Range Migration of Self-Interstitial Atoms in Ordered Alloys," Materials Science Forum 15-18, 273-278 (1987). ______________________________________________________________________________ To understand the basic physics of field-ion microscopy I initiated a series of experiments on the process of field-ionization, which involves the quantum mechanical tunneling of an imaging gas atom’s outermost electron into an FIM specimen. This involved fabricating a miniature Faraday cup, compatible with UHV, to detect the helium ion-current from individual {hkl} atomic planes as a function of the applied electric field; Wei and Seidman, 1977. This experiment demonstrated that the probability of ionization of an atom residing in a given {hkl} plane was a strong function of both its {hkl} crystallography and local electric field. Thereby, providing a physical explanation for the so-called current-voltage characteristic curves of an entire nanotip. Additionally, the temperature dependence of the resolution of a field-ion microscope was determined by measuring the image diameter of an atom as function of a nanotip’s temperature at constant electric field. The results of this experiment showed unequivocally that the field-ionized helium atoms have a quadratic dependence on the temperature of a nanotip, which is a direct reflection of the fact that they are thermally accommodated to a certain degree. The experiments demonstrated, however, that helium atoms are not fully accommodated to the temperature of the nanotip at the moment they are field-ionized. Y. C. Chen and D. N. Seidman, "On the Atomic Resolution of a Field-Ion Microscope," Surface Science 26, 61-84 (1971). Y. C. Chen and D. N. Seidman, "The Field Ionization Characteristics of Individual Atomic Planes," Surface Science 27, 231-255 (1971). C.-Y. Wei and D. N. Seidman, "A Novel Faraday Cup for the Simultaneous Observation and Measurement of Ion-Beam Currents," Review of Scientific Instruments 48, 1617-1620 (1977). ______________________________________________________________________________ After the invention of the atom-probe field-ion microscope (APFIM) by Mueller, Panitz and McLane, in 1968, I commenced building an ultrahigh vacuum APFIM, which was controlled completely by a computer; that is, the process of initiating field-evaporation pulses and the detection of the field-evaporated ions employing a micro-channel plate occurred without human intervention. The detection process yields the time-of-flight and therefore the mass-to-charge state ratio of an ion, that is, its chemical identity. This was accomplished using a Data General Nova 6 computer, which was one of the early commercial computers for controlling scientific equipment in a laboratory. This APFIM also had a specimen exchange device, a double-tilt goniometer stage, and a low-energy ion gun attached to it, with magnetic mass filtering of the ion-beam: Amano and Seidman, 1979. The appearance of an article, 1977, on this APFIM at Cornell University set the platinum standard for all future APFIMs fabricated around the world. I emphasize strongly that when this UHV APFIM was fabricated it was not possible to purchase a UHV compatible double-tilt goniometer stage, a specimen exchange device, a low-energy ion gun with magnetic mass filtering, and hence they were all fabricated in the Instrument Shop of the Laboratory of Atomic and Solid State Physics (LASSP) at Cornell University. Additionally, a commercial time-to-digital converter with a resolution of better than 10 nsec was not commercially available and one had to be fabricated, which was made possible with advice from the Newman Laboratory’s electronics shop; the latter served the experimental particle physicists at Cornell. In my first archival article describing the UHV APFIM in detail, results were also presented for tungsten, molybdenum, a molybdenum-titanium alloy, a molybdenum-titanium-zirconium (TZM) alloy, a low swelling stainless steel (L1A), and an iron-based metallic glass (Metglass 2826). The results obtained demonstrated the power of an APFIM for extracting chemical information on an atomic scale and indicated that a wide range of materials could be readily studied. T. M. Hall, A. Wagner, A. S. Berger and D. N. Seidman, "A Time-of-Flight Atom-Probe Field-Ion Microscope for the Study Defects in Metals," Cornell Materials Science Center Report No. 2357 (1975). 62 pages of text plus 27 figures. T. M. Hall, A. Wagner, A. S. Berger and D. N. Seidman, "An Atom-Probe Field-Ion Microscope for the Study of Defects in Metals," Scripta Metallurgica 10, 485-488 (1976). This is a four page summary article of the longer report cited immediately above. T. M. Hall, A. Wagner and D. N. Seidman, "A Computer Controlled Time-of-Flight Atom-Probe Field-Ion Microscope for the Study of Defects in Metals," Journal of Physics E: Scientific Instruments 10, 884-893 (1977). J. Amano and D. N. Seidman, "A Differentially-Pumped Low-Energy Ion-Beam System for an Ultrahigh Vacuum (UHV) Atom-Probe Field-Ion Microscope," Review of Scientific Instruments 50, 1125-1129 (1979). ______________________________________________________________________________ The UHV APFIM was employed to study the fundamental properties of 4He and 3He in tungsten, where the 4He or 3He atoms were implanted using an attached low-energy ion gun with magnetic mas- filtering; the latter was separated from the APFIM by a single stage of differential pumping, which was important for maintaining UHV conditions in the APFIM during the helium implantation process. The motivation for this experiment was the fact that helium is a by-product of so-called no- reactions in neutron (no) irradiated materials; when -particles come to rest in a lattice they are helium atoms. At the time of our experiments simulations of the diffusion of helium in f.c.c. and b.c.c. metals indicated an activation energy for diffusion of ~0.25±0.25 eV, whereas thermal desorption experiments indicated that the same activation energy is several electron volts. Since helium is insoluble in all metals it precipitates out and resides in bubbles, which are deleterious to nuclear reactor materials. To model the behavior of reactor materials in the presence of helium bubbles it is essential to know the diffusivity of helium atoms and this experiment was specificanlly designed to measure this quantity. The experiments were performed by implanting 4He or 3He into perfect tungsten specimens, at a cryogenic temperature, 10 K, using an implantation energy of 300 eV, which transferred energy to a primary knock-on atom of tungsten, which was well below the threshhold energy for producing stable Frenkel pairs; therefore at 300 eV the production of Frenkel pairs was completely suppressed. Then the immobile implantation profile was determined by APFIM in situ at the implantation temperature, which served as a reference state. The implanted specimen was then aged isothermally at a series of elevated temperatures for fixed periods of time, and the implantation profiles were re-measured after each aging treatment. The temperature and time dependence of the recovery of the implanted 4He or 3He profile yielded the diffusivity and migration energy of interstitial helium for 4He or 3He and the activation energy for migration, which was determined to be 0.24±0.10 eV for both isotopes, with no measurable classical isotope effect in the pre-exponential factor of the diffusivity. The reason for the discrepancy between the model calculations and the thermal desorption experiments is that the experiments utilized an implantation energy that created stable Frenkel pairs, and the implanted helium atoms wound up being trapped at vacancies with a large binding energy. Hence, the desorption experiments measured the sum of the binding and migration energies of helium and not simply a migration energy, whereas the APFIM experiments utilized an implantation energy that did not produce deep point defect traps for helium. Our studies constitute the only experimental studies of implanted helium atoms in the complete absence of radiation damage. We also utilized the APFIM to study hydrogen implanted in tungsten at 29 K. Wagner and D. N. Seidman, "The Range Profiles of 300 and 475 eV 4He+ Ions and Diffusivity of 4He in Tungsten," Physical Review Letters 42, 515-518 (1979). J. Amano, A. Wagner and D. N. Seidman, "Range Profiles of Low-Energy (100 to 1500 eV) Implanted 3He and 4He Atoms in Tungsten: I. Experimental Results," Philosophical Magazine A 44, 177-198 (1981). J. Amano, A. Wagner and D. N. Seidman, "Range Profiles of Low-Energy (100 to 1500 eV) Implanted 3He and 4He Atoms in Tungsten: II. Analysis and Interpretation," Philosophical Magazine A 44, 199-222 (1981). D. N. Seidman, J. Amano and A. Wagner, "The Study of Defects, Radiation Damage and Implanted Gases in Solids by Field-Ion and Atom-Probe Microscopies," in Advanced Techniques for Characterizing Microstructures, edited by F. W. Wiffen and J. Spitznagel (Metallurgical Society of AIME, Warrendale, PA, 1982), pp. 125-144. J. Amano and D. N. Seidman, "The Diffusivity of 3He Atoms in Perfect Tungsten Crystals," Journal of Applied Physics 56, 983-992 (1984). T. Macrander and D. N. Seidman, "An Atom-Probe Field-Ion Microscope Study of 200 eV Ions Implanted in Tungsten at 29 K," Journal of Applied Physics 56, 1623-1629 (1984). Y.-J. Kim and D. N. Seidman, “Atom-Probe Tomographic Analyses of Hydrogen Interstitial Atoms in Ultrahigh Purity Niobium,” Microscopy & Microanalysis, 21, 535-543 (2015). ______________________________________________________________________________ An alloy subjected to fast neutron irradiation has a dynamic phase diagram with the flux of neutrons, number of neutrons per unit area per unit time, being the control variable. Irradiation of a specimen is an example of a driven system as it is an open thermodynamic system and one does not know a priori what the final state of the system will look like This dynamic phase diagram is determined by the kinetic properties of the point defects produced, vacancies and self-interstitial atoms (SIAs) and their interactions with the solvent and solute atoms constituting the alloy. It is theoretically possible to obtain either homogeneous radiation-induced precipitation (RIP) or heterogeneous RIP at pre-existing lattice defects in a specimen (G. Martin and P. Bellon). To study these ideas experimentally on an atomic scale W-10 at.% Re and W-25% Re specimens were fast-neutron irradiated in EBR-II and subsequently studied by APFIM; both Re concentrations were such that at the irradiation temperature the alloys were in the primary single-phase field of the W-Re phase diagram. After irradiation both alloys contained precipitates and by measuring their compositions it was demonstrated that the precipitates were homogeneously nucleated, thereby validating the idea that homogeneous RIP is possible. Possible kinetic pathways were for the precipitation processes were suggested. R. Herschitz and D. N. Seidman, "An Atomic Resolution Study of Homogenous Radiation-Induced Precipitation in a Neutron-Irradiated W-10 at. % Re Alloy," Acta Metallurgica 32, 1141-1154 (1984). (Overview No. 39). R. Herschitz and D. N. Seidman, "An Atomic Resolution Study of Radiation-Induced Precipitation and Solute Segregation Effects in a Neutron-Irradiated W-25 at. % Re Alloy," Acta Metallurgica 32, 1155-1171 (1984). (Overview No. 39). ______________________________________________________________________________ Next my interests turned toward interfacial segregation phenomena and the system chosen for the initial studies were Co-Nb and Co-Fe alloys, because the free energy difference between the f.c.c. and h.c.p. phases of these cobalt-base alloys is very small and therefore the alloys contain a high number density of intrinsic stacking faults. The stacking faults served as simple and well-defined two dimensional planar interfaces for segregants. The temperature dependence of segregation at stacking faults in Co-Nb and Co-Fe alloys was studied by APFIM and the enthalpy of segregation of Nb or Fe to stacking faults was measured in Co-Nb and Co-Fe alloys. A classical thermodynamic model was developed for interfacial segregation at stacking faults was developed, which took into account solute-solute interactions within the plane of the stacking fault. These experiments and analyses developed constituted the first quantitative study of segregation at stacking faults by APFIM, and they served as a basis for the segregation studies I performed at Northwestern University. R. Herschitz and D. N. Seidman, "Atomic Resolution Observations of Solute-Atom Segregation Effects and Phase Transitions in Stacking Faults in Dilute Cobalt Alloys: I. Experimental Results," Acta Metallurgica 33, 1547-1563 (1985). R. Herschitz and D. N. Seidman, "Atomic Resolution Observations of Solute-Atom Segregation Effects and Phase Transitions in Stacking Faults in Dilute Cobalt Alloys: II. Analysis and Discussion," Acta Metallurgica 33, 1565-1576 (1985). ______________________________________________________________________________ Additionally, studies were made of the APFIM’s ability, as an instrument, for studying order-disorder phenomena in Ni4Mo and Pt3Co, and as a result analysis techniques were developed for performing quantitative experiments with this technique. For example, the proper experimental conditions were found for determining the chemistry of superlattice planes in these ordered alloys, which turned out to have general applicability to all ordered alloys. M. Yamamoto and D. N. Seidman, "Quantitative Compositional Analyses of Ordered Pt3Co by Atom-Probe Field-Ion Microscopy," Surface Science 118, 535-554 (1982). M. Yamamoto and D. N. Seidman, "The Quantitative Compositional Analyses and Field-Evaporation Behavior of Ordered Ni4Mo on an Atomic Plane-by-Plane Basis: An Atom Probe Field-Ion Microscope Study," Surface Science 129, 281-300 (1983). ______________________________________________________________________________ The APFIM was also used to perform one of the first studies, 1982, of a compound semiconductor, GaP, where the stoichiometry of the {111} superlattice planes were studied in detail. The results presented in this 1982 in this article were useful for experiments performed on nanowires of InAs using our LEAP3000 tomograph, 2006, which only had the ability to use voltage pulsing . M. Yamamoto, D. N. Seidman and S. Nakamura, "A Study of the Composition of the {111} Planes of GaP on an Atomic Scale," Surface Science 118, 555-571 (1982). D. E. Perea, J. E. Allen, S. J. May, B. W. Wessels, D. N. Seidman, L. J. Lauhon, “Three-Dimensional Nanoscale Composition Mapping of Semiconductor Nanowires,” Nano Letters 6 (2), 181-185 (2006). ______________________________________________________________________________ Northwestern University, September 1st, 1985 to the present At Northwestern University I continued initially an effort in the area of radiation damage, which involved a search for the amorphization of silicon using high-energy electrons (1 MeV) in the Argonne National Laboratory high-energy electron microscope. The first result was negative as no matter how low the temperature of the silicon specimen, 6 K, it could not be amorphized using electrons. A byproduct of this research was, however, the discovery that simultaneous irradiation with 1 MeV electrons and heavy ions could result in either amorphization or the suppression of amorphization, which was both a novel and surprising result that was explainable in terms of the production of Frenkel pairs by electron irradiation and displacement cascades by heavy ions. D. N. Seidman, R. S. Averback, P. R. Okamoto and A. C. Baily, "The Crystalline-to-Amorphous Phase Transition in Irradiated Silicon," in Beam-Solid Interactions and Phase Transformations, edited by H. Kurz, G. L. Olson and J. M. Poate (Materials Research Society, Pittsburgh, PA 1986), Vol. 51, pp. 349-355. D. N. Seidman, R. S. Averback, P. R. Okamoto and A. C. Baily, "Amorphization Processes in Electron-and/or Ion-Irradiated Silicon," Physical Review Letters 58, 900-903 (1987). X. W. Lin, J. Koike, D. N. Seidman, and P. R. Okamoto, "Amorphization of Ge/Al or Si/Al Bilayer Specimens Induced by 1 MeV Electron Irradiation at 10 K," Philosophical Magazine Letters 60, 233-240 (1989). ______________________________________________________________________________ After arriving at Northwestern, September 1st, 1985, I decided to focus on the problem of interfacial segregation because of its importance in so many phenomena in materials science and engineering. Initially, I concentrated on grain-boundary segregation in binary metallic alloys because dealing with single-phase materials reduces the level of complexity somewhat, although in hindsight not radically. A grain boundary is characterized by five macroscopic degrees of freedom (DOF) and three microscopic DOF. The experimental approach involved measuring the five macroscopic DOF by transmission electron microscopy and the Gibbsian interfacial excess of solute using atom-probe field-ion microscopy (APFIM), which necessitated modifying a double-tilt holder for a transmission electron microscope to hold APFIM specimens. A procedure was developed that permitted us to find a grain boundary in an APFIM specimen, determine its five DOF, then back polish the specimen using a specially fabricated millisecond electropolishing unit to bring the grain boundary close to a nanotip’s surface in an APFIM specimen. Then the specimen was transferred to the APFIM to analyze chemically the grain boundary. This experimental procedure was a tour de force, which enabled us to obtain information that had heretofore not been obtained by any other technique. B. W. Krakauer, J. G. Hu, S. -M. Kuo, R. L. Mallick, A. Seki, D. N. Seidman, J. P. Baker and R. Lolyd" A System for Systematically Preparing Atom-Probe Field-Ion Microscope Specimens for the Study of Internal Interfaces," Review of Scientific Instruments 61, 3390-3398 (1990). B. W. Krakauer and D. N. Seidman, "Systematic Procedures for Atom-Probe Field-Ion Microscopy Studies of Grain Boundary Segregation," Review of Scientific Instruments 63, 4071-4079 (1992). D. N. Seidman, "Experimental Investigations of Internal Interfaces in Solids," in Materials Interfaces, edited by D. Wolf and S. Yip (Chapman and Hall, London, 1992), Chapt. 2, pp. 58-84. S. M. Foiles and D. N. Seidman, "Atomic Resolution Study of Solute-Atom Segregation at Grain Boundaries: Experiments and Monte Carlo Simulations," in Materials Interfaces, edited by D. Wolf and S. Yip (Chapman and Hall, London, 1992), Chapt. 19, pp. 497-515. ______________________________________________________________________________ The physical quantity measured by the atom-probe FIM for a grain-boundary (GB) is the Gibbsian interfacial excess of solute, which is the correct thermodynamic quantity to determine the level of segregation without any assumptions as to how the excess solute atoms are arranged at a GB. I was the first one to realize that it is possible to extract the Gibbsian interfacial excess utilizing an APFIM. This approach was applied to grain boundaries in Mo-Re, Pt-Ni, and Fe-Si alloys. In the case of the Fe-Si alloy sufficient data was collected to sample a significant portion of grain-boundary space for segregation. Specifically, the Gibbsian interfacial excess of solute was plotted as a function of the sin(), where is the rotation angle about the disorientation vector, c, and the dot product of the c and n vectors; the n vector is the unit normal to the grain boundary plane; when this dot product is zero c is parallel to n and the grain boundaries are symmetric twist boundaries, when this dot product is unity the grain boundaries are symmetric tilt boundaries. For values of this dot product other than zero and unity the grain boundaries are nonsymmetrical and are neither pure tilt of pure twist in character. For the experimental data obtained this plot yields a surface of the Gibbsian interfacial excess of solute as a function of the five macroscopic DOF, where the five macroscopic DOF have been folded into two axes. Plotting the experimental data in this manner yields physical insight into the absorptive capacity of different types of grain boundaries for solute atoms, which is not, once again, obtainable by any other technique. J. G. Hu, S. -M. Kuo, A. Seki, B. W. Krakauer and D. N. Seidman, "The Structure and Composition of a = 9/≈ Interface in a Mo (Re) Alloy via Transmission Electron and Atom-Probe Field-Ion Microscopies," Scripta Metallurgica et Materialia 23, 2033-2038 (1989). D. N. Seidman, J. G. Hu, S.-M. Kuo, B. W. Krakauer, Y. Oh and A. Seki, "Atomic Resolution Studies of Solute-Atom Segregation at Grain Boundaries: Experiments and Monte Carlo Simulations," Colloque de Physique Colloque C1, supplément au No. 1, Tome 51, C1-47 - C1-57 (1990). S. M. Foiles and D. N. Seidman, "Solute-Atom Segregation at Internal Interfaces," MRS Bulletin 15 (9), 51-57 (1990). S. -M. Kuo, A. Seki, Y. Oh and D. N. Seidman, "Solute-Atom Segregation: An Oscillatory Ni Profile at an Internal Interface in Pt (Ni)," Physical Review Letters 65, 199-202 (1990). J. G. Hu and D. N. Seidman, "Atomic Scale Observations of Two-Dimensional Re Segregation at an Internal Interface in W (Re)," Physical Review Letters 65, 1615-1618 (1990). D. N. Seidman, "Solute-Atom Segregation at Internal Interfaces on an Atomic Scale: Atom Probe Experiments and Computer Simulations," Materials Science and Engineering A, 137, 57-67 (1991). J. G. Hu and D. N. Seidman, "Relationship of Chemical Composition and Structure on an Atomic Scale for Metal/Metal Interfaces: The W (Re) System," Scripta Metallurgica et Materialia 27 (9) 693-698 (1992). B. W. Krakauer and D. N. Seidman, "Systematic Procedures for Atom-Probe Field-Ion Microscopy Studies of Grain Boundary Segregation," Review of Scientific Instruments 63, 4071-4079 (1992). W. Krakauer and D. N. Seidman, "Absolute Atomic Scale Measurements of the Gibbsian Interfacial Excess of Solute at Internal Interfaces," Physical Review B: Rapid Communications, 48, 6724-6727 (1993). D. N. Seidman, B. W. Krakauer and D. Udler, “Atomic Scale Studies of Solute-Atom Segregation at Grain Boundaries: Experiments and Simulations,” Journal of Physics and Chemistry of Solids 55, 1035-1057 (1994). B. W. Krakauer and D. N. Seidman, “Subnanometer Scale Study of Segregation at Grain Boundaries in an Fe (Si) Alloy,” Acta Materialia, 46 (17), 6145-6161 (1998). B. W. Krakauer and D. N. Seidman, “Distributions of Grain Boundaries in an Fe-3 at. % Si Alloy,” Interface Science 8, 27-40 (2000). _____________________________________________________________________________ In parallel with the experimental program on grain boundary segregation I started an effort at modeling GB segregation using initially linear isotropic elasticity theory to look at the interaction of a solitary solute atom with a tilt boundary or a twist boundary. The elastic interactions were the classical first and second-order interactions (pV and elastic moduli effects), which yielded some insights, all within a continuum framework, which I found to be less than satisfying. Hence, I switched to performing Monte Carlo simulations using embedded atom method (EAM) potentials, which had been developed by M. I. Baskes, M. Daw and S. Foiles (Sandia Laboratories, Livermore, CA) and are continuous long-range potentials. The well-known Metropolis algorithm was employed and in addition to switching the chemical identities of atoms we also included random relaxations of atoms in the unit cell, which is important because solute atoms can be either oversize or undersize with respect to the matrix atoms. The Monte Carlo simulations were performed for both symmetric twist and tilt boundaries, which were studied both without and with solute atoms to make certain that the anticipated grain boundary structures we obtained agreed with those of well- known boundaries, which had been studied experimentally employing high resolution electron microscopy. The systems studied were Au-Pt, Ni-Pt, and Ni-Pd. The first Monte Carlo simulations were performed for symmetric [001] twist boundaries in Pt-Au, which showed that the Au solute atoms are segregated at grain boundaries with unique patterns, which were not predicted using linear isotropic elasticity theory and therefore showed clearly the limitations of this classical continuum approach. These detailed Monte Carlo simulations were also used to determine the temperature dependence of segregation, which yielded both the enthalpy and entropy of segregation for symmetric [001] twist boundaries in a Pt-Au alloy. The results demonstrated that the value of the Gibbsian interfacial excess of Au increased with increasing twist angle and then reached a level plateau in the high-angle regime. It was discovered utilizing Monte Carlo simulations that the microscopic DOF can affect strongly the value of the Gibbsian interfacial excess of solute. That is, a grain boundary with a specified set of macroscopic DOF but with different sets of microscopic DOF can have significantly different values of the Gibbsian interfacial excess of solute. This result is important because it explains why Auger spectroscopy often yields very different levels of segregation for the same grain boundaries. Monte Carlo simulations were then used to study in great depth Gibbsian segregation at a series of [110] symmetric tilt boundaries in a Ni-Pd alloy; this alloy was chosen because it exhibits a continuous series of solid-solutions at the temperature chosen for the segregation studies. A first step in this research involved studying grain boundaries in pristine nickel to determine the lowest energy structure(s) for each tilt angle. This involved first using molecular statics simulation at 0 K to find the lowest energy structure(s), which lead to the surprising result that for a given tilt angle there are often geometrically different structures that have identical energies. Hence, the bicrystals were annealed at the segregation temperature using a Monte Carlo (Metropolis algorithm) code, which resulted in a smaller number of stable of grain boundary structures for each tilt angle. After analyzing the structural units in the stable grain boundary structures it was concluded that the popular structural unit model (SUM) for describing grain boundaries has no predictive power whatsoever, much to the chagrin of its proponent. The next step in this research program was to study segregation of Pd at the grain boundary structures found to be stable at the segregation temperature. The overlapping distributions Monte Carlo technique was employed to calculate segregation free energy distributions of the solute, Pd, at all the tilt boundaries. Firstly, it was found that tilt boundaries contain both attractive and repulsive sites for Pd. Secondly, the segregation free energy distributions were classified into three general types of distributions: (a) segregation occurs mainly at sites associated within the cores of the grain boundary dislocations; (b) segregation occurs at a combination of core and elastically strained sites; and (c) segregation occurs primarily at elastically strained sites. This detailed physical picture of segregation at grain boundaries is significantly different from one found in text books and review articles on this subject. A major result of all the research on grain boundaries is the proof that the five macroscopic degrees of freedom are thermodynamic state variables, as postulated by the late John W. Cahn. That is, the Gibbsian interfacial excess of solute at a grain boundary is a function of the five macroscopic degrees of freedom and therefore a five-dimensional space for grain-boundary segregation exists, implying that the local phase rule for interfaces postulated by J. W. Cahn is correct; that is, the Gibbs phase rule for bulk phases needs to modified to take into account the five DOFs when applied to grain-boundaries, such that it becomes  + f = C + 7, where  is the number of phases at a grain boundary, fis the number of degrees of freedom, C is the number of components in the system, and 7 stands for pressure, temperature, and the five macroscopic DOF. By using the displacement shift complete (DSC) lattice we demonstrated the effects of the three microscopic degrees of freedom (DOF) on Gibbsian segregation at a series of [110] symmetric tilt grain-boundaries (STGBs). Specifically, for a given STGB with fixed macroscopic DOF but different microscopic DOF the values of the Gibbsian excess of solute were shown to depend on the microscopic DOF. This result was unanticipated and met with some skepticism at the time, which has since disappeared. D. Udler and D. N. Seidman "Solute-Atom Interactions with Low-Angle Twist Boundaries," Scripta Metallurgica et Materialia 26, 449-454 (1992). D. Udler and D. N. Seidman "Solute-Atom Interactions with Low-Angle Tilt Boundaries," Scripta Metallurgica et Materialia 26, 803-808 (1992). A. Seki, D. N. Seidman, Y. Oh, and S. M. Foiles, "Monte Carlo Simulations of Segregation at [001] Twist Boundaries in a Pt (Au) Alloy -I. Results," Acta Metallurgica et Materialia 39, 3167-3177 (1991). Seki, D. N. Seidman, Y. Oh, and S. M. Foiles, "Monte Carlo Simulations of Segregation at [001] Twist Boundaries in a Pt (Au) Alloy -II. Discussion," Acta Metallurgica et Materialia 39, 3179-3185 (1991). D. Udler and D. N. Seidman, "Solute-Atom Segregation at Symmetrical Twist Boundaries Studied by Monte Carlo Simulation," Physica Status Solidi (b) 172, 267-286 (1992). J. G. Hu and D. N. Seidman, "Relationship of Chemical Composition and Structure on an Atomic Scale for Metal/Metal Interfaces: The W (Re) System," Scripta Metallurgica et Materialia 27 (9) 693-698 (1992). D. Udler and D. N. Seidman, "Atomic Scale Simulations of Solute-Atom Segregation at Grain Boundaries in Binary FCC Alloys," Materials Science Forum 155-156, 189-204 (1994). D. N. Seidman, B. W. Krakauer and D. Udler, “Atomic Scale Studies of Solute-Atom Segregation at Grain Boundaries: Experiments and Simulations,” Journal of Physics and Chemistry of Solids 55, 1035-1057 (1994). J. D. Rittner, S. M. Foiles and D. N. Seidman, "Simulation of Surface Segregation Free Energies," Physical Review B 50, 12 004-12 014 (1994). J. D. Rittner, D. Udler, D. N. Seidman and Y. Oh, "Atomic Scale Structural Effects on Solute-Atom Segregation at Grain Boundaries," Physical Review Letters 74, 1115-1118 (1995). Udler and D. N. Seidman, "Solute-Atom Segregation/Structure Relations at High-Angle (002) Twist Boundaries in Dilute Ni-Pt Alloys," Interface Science 3, 41-73 (1995). Udler and D. N. Seidman, "Solute-Atom Segregation at High-Angle (002) Twist Boundaries in Dilute Au-Pt Alloys," Journal of Materials Research 10 (8), 1933-1941 (1995). J. D. Rittner and D. N. Seidman, "Limitations of the Structural Unit Model," Materials Science Forum 207-209 333-336 (1996). Udler and D. N. Seidman, "Solute-Segregation Induced Structural Phase Transition at a Twist Boundary," Materials Science Forum 207-209 449-452 (1996). J. D. Rittner and D. N. Seidman, "<110> Symmetric Tilt Grain Boundary Structures in FCC Metals With Low Stacking-Fault Energies," Physical Review B 54 (10), 6999-7015 (1996). D. Udler and D. N. Seidman, “A Congruent Phase Transition at a Twist Boundary Induced by Solute Segregation,” Physical Review Letters 77, 3379-3382 (1996). J. D. Rittner, D. Udler, and D. N. Seidman, “Solute Atom Segregation at Symmetric Twist and Tilt Boundaries in Binary Metallic Alloys on an Atomic Scale” Interface Science 4, 65-80 (1996). D. Udler and D. N. Seidman, “Grain Boundary and Surface Energies of FCC Metals,” Physical Review B 54, 11133-11136 (1996). J. D. Rittner and D. N. Seidman, “Solute-Atom Segregation to <110> Symmetric Tilt Grain Boundaries,” Acta Materialia 45, 3191-3202 (1997). D. Udler and D. N. Seidman, “Solute Segregation at [001] Tilt Boundaries in Dilute FCC Alloys,” Acta Materialia 46, 1221-1233 (1998). B. W. Krakauer and D. N. Seidman, “Subnanometer Scale Study of Segregation at Grain Boundaries in an Fe (Si) Alloy,” Acta Materialia, 46 (17), 6145-6161 (1998). Udler and D. N. Seidman, “Monte Carlo Simulation of the Concentration Dependence of Solute-Atom Segregation at Vicinal Grain Boundaries,” Interface Science, 6 (4), 259-265 (1998). Low-density TiAl alloys are of potential value for use at high temperatures in both jet engines and land-based gas turbine engines, as a possible replacement for the more dense nickel-based alloys, in the cooler portions of an engine. We studied with conventional atom-probe tomography a series of TiAl alloys, with -2/ heterophase interfaces, that contained carbide precipitates, which are intentionally present to increase the high-temperature creep resistance of these alloys. This research found that the oxygen that is present in TiAl alloys partitions to the carbide precipitates and hence the latter is an excellent getter for excess of oxygen, which embrittles TiAl alloys, thereby discovering a potential technique for reducing the brittle character of these alloys at lower temperatures. More recently I recommenced performing research on titanium alloys with Dr. James A. Coakley, a European Union Marie Curie Research Fellow, on precipitation in titanium alloys using both a LEAP4000X Si and a LEAP5000XS tomographs, with emphases place on the earliest stages of precipitation of the omega phase. The latter instrument, with a detection efficiency of 80% demonstrated that it is possible to detect the very earliest stages of precipitation of the omega-phase, which was not possible with the LEAP4000X Si. S. S. A. Gerstl, Young-Won Kim, and D. N. Seidman, “Atomic-Scale Chemistry of 2/ Interfaces in a Multicomponent TiAl Alloy,” Interface Science 12 303-310 (2004). J. Coakley, D. N. Seidman, D. Isheim, V. A. Vorontsov, D. Dye, M. Ohnuma, “Precipitation Processes in Beta-Titanium Alloys,” Current Advances in Materials and Processes, Report of the 171st ISIJ Meeting (CAMP-ISIJ), 29, 72 (2016). J. A. Coakley, D. Isheim, A. Radecka, D. Dye, H. J. Stone, D. N. Seidman, “Microstructural Evolution in a Superelastic Beta-Ti Alloy,” Scripta Materialia, 128, 87-90 (2017). J. A. Coakley, A. Radecka, D. Dye, P. A. J. Bagot, T. L. Martin, T. J. Prosa, Y. Chen, H. J. Stone, D. N. Seidman, D. Isheim, “Atom-Probe Tomography of Titanium Alloys and the Omega Phase,” submitted to Materials Science and Engineering A, July 11th (2017). ______________________________________________________________________________ In series with the research program on segregation at grain boundaries and heterophase interfaces in metallic system I initiated a program on segregation at heterophase interfaces for ceramic/metal systems. This program had both experimental and simulational components; the latter involved first-principles calculations using density functional theory. The initial research was based on producing heterophase interfaces by internal oxidation of Cu-Mg and Ag-Cd alloys. For both systems this results in the formation of a high number density of nanometer scale octahedral-shaped MgO or CdO precipitates, which are faceted on {222} planes, which is a polar plane. The polar planes are either 100% cations or 100% anions: MgO is an excellent insulator with a large band gap energy, whereas CdO is almost a semiconductor with a small band gap. Using atom-probe field-ion microscopy it was demonstrated that the terminating plane for the {222}MgO/Cu interface is the anion, oxygen, while for the {222}CdO/Ag heterophase interface it was found that the terminating plane may be either the cation, Ag, or the anion, O, with equal probabilities. Hence, the termination depends on the band gap of the metal oxide, which suggested that our results could be explained using first-principles calculations, which was indeed the case. The first-principles calculations demonstrated that for the {222}MgO/Cu heterophase interface that both cation (Mg-) and anion (O+) terminations are stable but an anion termination is more stable than a cation termination, which is in agreement with our experimental observations. For the {222}CdO/Ag heterophase interface both cation (Cd-) and anion (O+) terminations have the identical stability, from first principles calculations, to within many decimal places, which is also consistent with our atom-probe field-ion microscope experimental results. When the research on the {222}MgO/Cu heterophase interface commenced it was generally accepted, based on high-resolution electron-microscopy (HREM) observations, that this interface is incoherent because of the large misfit, ca. 15 %, between the Cu matrix and the MgO precipitates. Utilizing, however, a dedicated scanning transmission electron microscope (STEM) at Oak Ridge National Laboratory, with a point-to-point resolution of less than 0.2 nm, misfit dislocations were found with the correct inter-dislocation spacing, thereby proving that it is a semi-coherent interface. More generally it was demonstrated that answering the question as to the degree of coherency of an interface depends on the instrument used to detect the misfit dislocations. The electronic structure of the {222}MgO/Cu heterophase interface was studied utilizing parallel electron energy-loss spectroscopy (EELS) measurements at Cornell University in a dedicated STEM; the EELS technique samples the unfilled electron energy levels; this work was performed in collaboration with D. A. Muller and J. Silcox. John Bardeen had postulated in the late 1940s the existence of metal-induced gap states (MIGS) for metal/semiconductor heterophase interfaces, which had not been observed at the time of our experiments for reasons that became transparent after we performed EELS experiments, which demonstrated that MIGS exists for the {222}MgO/Cu heterophase interface because MgO has a large band gap, 7.8 eV, implying that the interface states are highly localized and therefore detectable. Whereas for metal/silicon interfaces this is not the case (the band gap for silicon is only 1.11 eV) and hence they are not detectable using EELS. The experimental result for the {222}MgO/Cu heterophase interface is consistent with first-principles calculations we performed in parallel. Segregation of Ag at the {222}MgO/Cu heterophase interface was studied using atom-probe field-ion microscopy and the Gibbsian interfacial excess of Ag at this interface was determined, thereby determining this quantity for the first time in an unambiguous manner for a heterophase interface without extensive deconvolution. The reason for this is that internal oxidation produces heterophase interfaces that are free of impurity atoms and hence segregation can be studied of a specific solute atom without impurity atoms affecting its absorptive properties. Atom-probe field-ion microscopy was also used to study the segregation of Au at {222}CdO/Ag heterophase interfaces, thereby demonstrating the general applicability of this approach to another metal/metal-oxide internal interface. A similar experimental approach was used to study segregation of Sb at -Fe/molybdenum nitride interfaces, which were produced by internal nitridation of an -Fe(Mo, Sb or Sn) alloy. The initial molybdenum nitride precipitates were platelets that were one or two atomic layers thick and had no misfit dislocations in spite of the large lattice parameter misfit, in excess of 20 %, between -Fe and molybdenum nitride. In the absence of misfit dislocations the Gibbsian interfacial excess is very small, whereas as the molybdenum nitride platelets thicken the Gibbsian excess increases because of the appearance of misfit dislocations. Thereby, demonstrating that in this system the level of segregation is coupled with the presence of misfit dislocations and that the driving force may be the release of elastic strain energy associated with oversized Sb or Sn atoms, although one cannot rule out the role played by electronic effects without performing first-principles calculations. The presence of misfit dislocations was detected using HREM and it was shown that as the platelets thickened the number density of interfacial misfit dislocations increased but did not reach the requisite value to accommodate all of the elastic misfit strain energy, indicating that there was a problem nucleating dislocations. Our conventional atom-probe field-ion microscope was used to study interfacial segregation in a series of metal oxide/metal heterophase interfaces with the goal of finding rules for predicting which elements would segregate at a heterophase interface. The systems studied were MgO/Cu(Ag), MgO/Cu(Sb), CdO/Ag(Au) and MnO/Ag(Sb) and the Gibbsian interfacial excesses were measured for the different solute atoms, Ag, Sb, and Au. The so-called Wynblatt-Ku model, which is commonly used to predict whether or not an element segregates at an interface, was employed to see if it is in agreement with the observed experimental results and it was found that its “predictability” rating is ca. 50%, implying that is of limited value for metal oxide/metal systems. The reason for the failure of the Wynblatt-Ku model is that it neglects electronic effects and assumes that the main driving force for interfacial segregation is elastic; that is, the reduction in the misfit elastic strain energy associated with an oversize or undersize atom. In parallel with the experimental program on metal oxide/metal interfaces a first-principles and simulational effort was executed. For example, the chemistry and bonding at {222} MgO/Cu heterophase interfaces was studied using first-principles calculations. Also, first principles simulations of a {222} MgO/Cu interface with misfit were performed thereby incorporating the dislocation structure of the interface for the first time for any ceramic/metal system. A classical interatomic potential for Nb-alumina interfaces was developed for studying structure-property relationships of oxide surfaces and interfaces. The effect of misfit on heterophase interface energies was studied in detail. Interface structure and energy calculations were performed for carbide precipitates in -TiAl. And the partitioning of impurities in multi-phase TiAl alloys was theoretically studied. D. A. Shashkov and D. N. Seidman, "Atomic Scale Studies of Segregation at Ceramic/Metal Heterophase Interfaces" Physical Review Letters 75, 268-271 (1995). D. A. Shashkov and D. N. Seidman, “Atomic-Scale Studies of Silver Segregation at MgO/Cu Heterophase Interfaces,” Applied Surface Science 94/95, 416-421 (1996). D. A. Shashkov, D. K. Chan, R. Benedek and D. N. Seidman, “Atomistic Characterization of Ceramic /Metal Heterophase Interfaces: Experiments and Simulation,” Interface Science and Materials Interconnection, Proceedings of JIMIS-8 (1996), edited by Y. Ishida, M. Morita, T. Suga, H. Ichinose, O. Ohashi, J. Echigoya, The Japan Institute of Metals, pp. 85-92 (1996). D. A. Shashkov, R. Benedek, and D. N. Seidman, “Subnanoscale Characterization of MgO/Cu Heterophase Interfaces: Experiments and Atomistic Simulations” Journal of Surface Analysis (Japan) 3, 377-382 (1997). D. A. Muller, D. A. Shashkov, R. Benedek, L. H. Yang, J. Silcox and D. N. Seidman, “Atomic Scale Observations of Metal-Induced Gap States at {222} MgO/Cu Interfaces,” Physical Review Letters, 80, 4721-4744 (1998). D. A. Shashkov, M. F. Chisholm, and D. N. Seidman, “Atomic-Scale Structure and Chemistry of Ceramic/Metal Interfaces - I. Atomic Structure of {222} MgO/Cu (Ag) Interfaces,” Acta Materialia 47, 3939-3951 (1999). D. A. Shashkov, D. A. Muller, and D. N. Seidman, “Atomic-Scale Structure and Chemistry of Ceramic/Metal Interfaces - II. Solute Segregation at MgO/Cu (Ag) and CdO/Ag (Au) Interfaces,” Acta Materialia 47, 3953-3963 (1999). D. K. Chan, D. N. Seidman, and K. L. Merkle, "The Chemistry and Structure of CdO/Ag {222} Heterophase Interfaces," Physical Review Letters 75, 1118-1121 (1995). D. K. Chan, D. N. Seidman, and K. L. Merkle, "The Chemistry and Structure of {222} CdO/Ag Heterophase Interfaces on an Atomic Scale," Applied Surface Science 94/95, 409-415 (1996). D. A. Shashkov, D. K. Chan, R. Benedek and D. N. Seidman, “Atomistic Characterization of Ceramic /Metal Heterophase Interfaces: Experiments and Simulation,” Interface Science and Materials Interconnection, Proceedings of JIMIS-8 (1996), edited by Y. Ishida, M. Morita, T. Suga, H. Ichinose, O. Ohashi, J. Echigoya, The Japan Institute of Metals, pp. 85-92 (1996). D. A. Shashkov, D. K. Chan, R. Benedek and D. N. Seidman, “Atomistic Characterization of Ceramic /Metal Heterophase Interfaces: Experiments and Simulation,” Interface Science and Materials Interconnection, Proceedings of JIMIS-8 (1996), edited by Y. Ishida, M. Morita, T. Suga, H. Ichinose, O. Ohashi, J. Echigoya, The Japan Institute of Metals, pp. 85-92 (1996). R. Benedek, D. N. Seidman, and L. H. Yang, “Atomistic Simulation of Ceramic/Metal Interfaces: {222} MgO/Cu” Microscopy and Microanalysis 3, 333-338 (1997). R. Benedek, D. N. Seidman, M. Minkoff, L. H. Yang and A. Alavi, “Atomic and Electronic Structure, and Interatomic Potentials at a Polar Ceramic/Metal Interface: {222} MgO/Cu,” Physical Review B, 60, 16094-16102 (1999). R. Benedek, A. Alavi, D. N. Seidman, L. H. Yang, D. A. Muller, and C. Woodward, “First Principles Simulation of a Ceramic/Metal Interfaces with Misfit,” Physical Review Letters 84, 3362-3365 (2000). O. C. Hellman, J. A. Vandenbroucke, J. Rüsing, D. Isheim, and D. N. Seidman, “Analysis of Three-Dimensional Atom-Probe Data by the Proximity Histogram,” Microscopy and Microanalysis 6, 437-444 (2000). Named Best Materials Paper published in Microscopy and Microanalysis in the year 2000. J. Rüsing, J. T. Sebastian, O. C. Hellman, and D. N. Seidman, “Three-Dimensional Investigations of Ceramic/Metal Heterophase Interfaces by Atom-Probe Microscopy,” Microscopy and Microanalysis 6, 445-451 (2000). Named Best Materials Paper published in Microscopy and Microanalysis in the year 2000. K. Albe, R. Benedek, D. N. Seidman and R. S. Averback, “Classical Interatomic Potential for Nb-Alumina Interfaces,” Materials Research Society Symposium Proceedings of “Structure-Property Relationships of Oxide Surfaces and Interfaces,” edited by C. Barry Carter, Xiaoqing Pan, Kurt E. Sickafus, Harry L. Tuller, and Tom Wood, Materials Research Society Symposium, 654, AA4.3.1-AA4.3.6 (2001). R. Benedek, D. N. Seidman, and C. Woodward, “Effect of Misfit on Heterophase Interface Energies,” Journal of Physics: Condensed Matter, 24, 1-24 (2002). O. C. Hellman and D. N. Seidman, “Measurement of the Gibbsian Interfacial Excess of Solute at an Interface of Arbitrary Geometry using Three-Dimensional Atom-Probe Microscopy,” Materials Science & Engineering A, 327(1), 24-28 (2002). R. Benedek, D. N. Seidman and C. Woodward, “Theory of Interface Properties for Carbide Precipitates in TiAl” Metallurgical and Materials Transactions A, 34A (10), 2097-211 (2003). R. Benedek, D. N. Seidman, and C. Woodward, “Interface Energies for Carbide Precipitates in TiAl,” Interface Science, 12, 57-71 (2004). R. Benedek, A. van de Walle, S. S. A. Gerstl, M. Asta, D. N. Seidman, and C. Woodward, “Partitioning of Impurities in Multi-Phase TiAl Alloys,” Physical Review B 71, 094201 (2005). Isheim, E. J. Siem, and D. N. Seidman, “Nanometer Scale Solute Segregation at Heterophase Interfaces and Microstructural Evolution of Molybdenum Nitride Precipitates,” Ultramicroscopy, 89 (1-3), 195-202 (2001). D. Isheim and D. N. Seidman, "Subnanometer-Scale Chemistry and Structure of -Iron/Molybdenum Nitride Heterophase Interfaces," Materials and Metallurgical Transactions A 33A, 2317-2326, (2002). ______________________________________________________________________________ A major research effort, which is still ongoing, was undertaken to understand the detailed roles played by the major alloying elements in nickel-based superalloys used in both jet engines for military and commercial aircraft and land-based gas-turbine engines for generating electricity. This involved the preparation of a series of Ni-Al-Cr alloys, which are the basis of all commercial nickel-base alloys, and adding quaternary, quinary, and sexanary elements one at a time; the additional refractory alloying elements added are tungsten, rhenium, tantalum, ruthenium, and niobium. Commercial nickel-base superalloys may contain upwards of eight to ten elements and each element has been added for a specific purpose. These excellent high-temperature structural alloys have been developed over a long period of time and have made possible two-phase single-crystal turbine blades that operate at elevated temperatures. The detailed physical reasons why, however, the additional alloying elements improve nickel-base superalloys has not yet been elucidated in detail. To commence this research program we studied the temporal evolution of the nanostructure of Ni-Al-Cr, Ni-Al-Cr-Re, and Ni-Al-Cr-W alloys using conventional atom-probe tomography. In this research we also employ transmission electron microscopy to determine precipitate size distributions (PSDs), number denisyt of precipitates, supersaturations of each element, and mean precipitate radii (<R(t)>. Specifically, the temporal evolution at 873 K of a Ni-Al-Cr alloy with moderate supersaturations of Al and Cr was studied in excruciating quantitative detail. Basically we studied the kinetics of a first-order phase transformation, where the temporal evolution of the chemistry of the alloy as well as the nanostructure is quantitatively measured to obtain a detailed physical picture. This is accomplished by aging specimens in the two phase region,  (f.c.c.) matrix plus ’(L12) precipitates, for different times and measuring the chemistry of both phases, the mean radius, <R>, the number density, Nv, and the morphology of the ’(L12) precipitates. For the alloy compositions studied the lattice parameter misfit is close to zero and hence the ’(L12) precipitates remain spheroidal for times as long as 1024 hours. By measuring all of these parameters from the earliest possible aging times we obtained a complete physical picture of the temporal evolution and found experimentally the kinetic pathways. Additionally, we were able to compare our experimental data with the temporal predictions of the Kuehmann-Voorhees model of quasi-state coarsening of a ternary alloy for <R>, Nv, and the supersaturation of the solute elements (Al and Cr) in the matrix. Furthermore, we were able to show that the composition trajectory of the ’(L12)-precipitate phase is not along the tie line connecting the ’(L12) and  (f.c.c.) phases, while the composition trajectory of the  (f.c.c.) phase is along the tie line. An analysis of the compositions of the ’(L12) phases demonstrated a capillary effect for small precipitate radii; the smallest radius measured was 0.45 nm, which corresponds to a precipitate containing 20 atoms. Also the chemical widths of the ’(L12)/(f.c.c.) interfaces were measured and shown to be broader than anticipated, which is an important unanticipated effect. Finally, using the classical definitions of radial distribution functions (RDFs) in direct lattice space, we were able to demonstrate that in the as-quenched state there is short-range ordering of Ni and Al atoms, which is the precursor to the ’(L12) precipitates that we detect at 600 seconds in the atom-probe tomographic reconstructions. This information permitted an upper bound to be placed on the critical nucleus radius of 0.45 nm, which does not depend on a knowledge of the interfacial free energy or the supersaturation and is independent of a model. Finally, an analysis of the experimental data permitted a value of the ’(L12)/(f.c.c.) interfacial free energy to be calculated. The many results obtained from this study are the most complete ones obtained for a binary or ternary decomposing alloy. In parallel with the experimental studies on the decomposition of the ternary Ni-Al-Cr alloy discussed above a vacancy-medaited lattice kinetic Monte Carlo (LKMC) simulation study was performed, which permitted a greater understanding of the experimental results as there is a symbiotic relationship between the two approaches to this problem. The LKMC studies involve the use of one monovacancy in a lattice of atoms bound together by pair-wise potentials out to fourth nearest-neighbor atoms and monovacancy-atom interactions to first nearest-neighbor atoms. LKMC simulations have the important virtue that a physical time is determined as opposed to the use of the Metropolis algorithm MC simulation, where the time is nonphysical and depends on the speed of the computer used. Thus, LKMC results are directly comparable to experimental results after being normalized to the vacancy concentration in pure nickel at the aging temperature. The LKMC results have demonstrated, among other things, that the occurrence of necks between gamma prime precipitates is controlled by the vacancy-solute binding free energy; that is, when the vacancy-solute binding energy is set equal to zero at second, third and fourth nearest-neighbor.positions the necks disappear. The vacancy-solute binding energy also controls the width of the ’(L12)/(f.c.c.) heterophase interface. With the vacancy-solute binding free energy present to fourth nearest-neighbor positions the width determined by the LKMC simulation is close to the experimental width, whereas in the absence of the vacancy-solute binding energy at at second, third and fourth nearest-neighbor positions the width is narrower. The necks play an important role in the coarsening mechanism of gamma-prime precipitates, which is different from the classical evaporation-condensation model that is implicit in the Lifschitz-Slyozov-Wagner (LSW) model of coarsening, where large precipitates grow at the expense of small precipitates. The coagulation-coalescence model discovered via experiments and the LKMC simulations operates even when the gamma-prime precipitates have similar radii. The KLMC simulations demonstrate that the existence of the off-diagonal terms in the diffusion matrix, which involve significant amounts of diffusive fluxes are important. The presence of these diffusive fluxes was discovered by including a non-zero value for the chemical potential of the vacancy, which is physically reasonable since the inter-precipitate distance is small compared with the distance between the predominant sources and sinks of vacancies, dislocations. A key question for any first order phase transformation is: How does a uniform solid-solution decompose into two phases? This question has been answered experimentally, employing atom-probe tomography, for a Ni-Al-Cr alloy that decomposes at 873 K. The kinetics of clustering are detected employing radial distribution function (RDF) analyses of the solute atoms in direct lattice space. The APT results show the existence of a precipitate at an aging time of 600 seconds using isoconcentration surfaces to delineate the gamma-prime precipitates. For times shorter than 600 seconds RDF analyses centered on the solute atoms, Al and Cr, demonstrated that in the as-quenched state there is already Ni-Al ordering present, the precursor to ordered Ni3(Al1-xCrx) precipitates, which becomes stronger with increasing time with Al substituting for Cr in the domains. As the aging time progresses the domains evolve into visible precipitates of Ni3(Al1-xCrx) (L12), detected via isoconcentration surfaces. Thus the genesis of a new phase has been followed, in direct lattice space, from the quenched-in state to the direct observation of precipitates. The uniqueness and strength of this approach is that it does not depend on deconvolution of data recorded in Fourier space. K. E. Yoon, D. Isheim, R. D. Noebe and D. N. Seidman, “Nanoscale Studies of the Chemistry of a René N6 Superalloy,” Interface Science, 9, 249-255 (2002). C. K. Sudbrack, K. E. Yoon, Z. Mao, R. D. Noebe, D. Isheim, and D. N. Seidman, “Temporal Evolution of Nanostructures in a Model Nickel-Base Superalloy: Experiments and Simulations,” in Electron Microscopy: Its Role in Materials Research – The Mike Meshii Symposium, Edited by J.R. Weertman, M. E. Fine, K. T. Faber, W. King and P. Liaw (TMS (The Minerals, Metals & Materials Society), Warrendale, PA, 2003), pp. 43-50. C. K. Sudbrack, D. Isheim, R. D. Noebe, N. S. Jacobson, and D. N. Seidman, “The Influence of Tungsten on the Chemical Composition of a Temporally Evolving Nanostructure of a Model Ni-Al-Cr Superalloy,” Microscopy and Microanalysis 10, 355-365 (2004). C. K. Sudbrack, K. E. Yoon, R. D. Noebe and D. N. Seidman, “Temporal Evolution of the Nanostructure and Phase Compositions in a Model Ni-Al-Cr Superalloy,” Acta Materialia 54, 3199-3210 (2006). C. K. Sudbrack, R. D. Noebe, and D. N. Seidman, “Compositional Pathways and Capillary Effects of Isothermal Precipitation in a Nondilute Ni-Al-Cr Superalloy,” Acta Materialia 55, 119-130 (2007). Z. Mao, C. K. Sudbrack, K. E. Yoon, G. Martin, and D. N. Seidman, “The Mechanism of Morphogenesis in a Phase Separating Concentrated Multi-Component Alloy.” Nature Materials 6, 210-216 (2007). C. Booth-Morrison, J. Weninger, C. K. Sudbrack, Z. Mao, R. D. Noebe, and D. N. Seidman, “Effects of Solute Concentrations on Kinetic Pathways in Ni-Al-Cr Alloys,” Acta Materialia, 56 3422-3438 (2008). C. Booth-Morrison, Z. Mao, and D. N. Seidman, “Tantalum and Chromium Site Substitution Patterns in the Ni3Al (L12) ’-Precipitate Phase of a Model Ni-Al-Cr-Ta Superalloy,” Applied Physics Letters, 93, 033103-1 to 033103-3 (2008). C. Booth-Morrison, R. D. Noebe, and D. N. Seidman, “Effects of a Tantalum Addition on the Temporal Evolution of a Model Ni-Al-Cr Superalloy During Phase Decomposition,” Acta Materialia, 57, 908-919 (2009). C. Booth-Morrison, Y. Zhou, R. D. Noebe, and D. N. Seidman, “On the Nanoscale Phase Decomposition of a Low-Supersaturation Ni-Al-Cr Alloy,” Philosophical Magazine, 90(1), 219-235 (2010). Z. Mao, C. Booth-Morrison, C. K. Sudbrack, G. Martin, and D. N. Seidman, “Kinetic Pathways for Phase Separation: An Atomic-Scale Study in Ni-Al-Cr Alloys,” Acta Materialia, 60(4), 1871–1888 (2012). Z. Mao, C. Booth-Morrison, E. Plotnikov, D. N. Seidman, “The Effects of Temperature and Ferromagnetism on the-Ni/’-Ni3Al Interfacial Free-Energy Calculated from First-Principles,” Journal of Materials Science, 47, 7653-7659 (2012). E. Y. Plotnikov, Z. Mao, R. D. Noebe, D. N. Seidman, “Temporal Evolution of the γ(fcc)/γ’(L12) Interfacial Width in Binary Ni-Al Alloys,” Scripta Materialia, 70, 51–54 (2014). Y. Huang, Z. Mao, R. D. Noebe, D. N. Seidman, “The Effects of Refractory Elements (Re, Ru, W and Ta) on Ni Excesses and Depletions at γ'/γ Interfaces in Ni-based Superalloys: Atom-Probe Tomographic Experiments and First-Principles Calculations,” Acta Materialia, 121, 288-298 (2016). _____________________________________________________________________________ In collaboration with my colleague Prof. D. C. Dunand (Northwestern University), which commenced in 1998, I started a program on the study of the Al-Sc-X system, where X is a ternary alloying element. This research involves a combined study of the high-temperature creep properties between 0.6 and 0.7 of the absolute melting point of pure aluminum, with the characterization of the microstructure utilizing atom-probe tomography, transmission electron and scanning electron microscopies. Scandium has the highest strengthening effect, on a per atom basis, of all the elements in the period table that dissolve in Al. The reason for this is that the phase that precipitates out of single-phase Al-Sc solid-solutions is Al3Sc (L12) and this phase has a melting point greater than 1300 oC. Al3Sc precipitates coarsen at elevated temperatures but they do not dissolve like precipitates in the common age-hardening aluminum alloys, for example, the widely utilized Al-Cu alloys that are used for engine blocks in motor vehicles. We proceeded to study Al-Sc-Mg and Al-Sc-Zr alloys and discovered that the latter alloy forms Al3(Sc1-xZrx) precipitates with an Al3Sc core surrounded by a Zr shell. This shell acts as a diffusion barrier and decreases the coarsening kinetics significantly with respect to the coarsening behavior of Al3Sc precipitates in Al-Sc and Al-Sc-Mg alloys. The high temperature creep properties are determined by climb over the Al3(Sc1-xZrx) precipitates and this results in excellent threshold stresses for creep. The next major step in this research involved decreasing the Sc concentrations in the Al-Sc-Zr alloys by substituting rare earth (RE) elements for Sc because they are considerably cheaper and more plentiful in the earth’s crust than Sc. Additionally, we added silicon as it accelerates the precipitation kinetics and is not deleterious to the stability of the alloy if added in small concentrations. We also found that small concentrations of Sb additions serve as a nucleant for precipitates, thereby increasing their number density and concomitantly the alloy’s strength. We have also demonstrated that by a judicious choice of the concentrations of the different alloying elements that the Sc concentration can be significantly reduced without a deterioration in the coarsening kinetics and mechanical properties. We are also able to increase the maximum operating temperature of our Al-Sc-Zr-Er alloys by the addition of Mn and/or Mo. Furthermore, at NanoAl LLC, Skokie, Illinois, we have developed high-temperature aluminum alloys without Sc -- http://nanoal.com/ . I am a co-founder and co-chief scientific officer of NanoAl LLC, which was incorporated in 2013. NanoAl LLC is located in Skokie, IL 60077. B. Fuller, D. N. Seidman, and D. C. Dunand, “Creep Properties of Coarse-Grained Al (Sc) Alloys at 300˚C,” Scripta Materialia 40, 691-696 (1999). E. A. Marquis and D. N. Seidman, “Nanoscale Morphological Evolution of Al3Sc Precipitates in Al(Sc) Alloys,” Acta Materialia 49, 1909-1919 (2001). D. N. Seidman, E. A. Marquis, and D. C. Dunand, “Precipitation Strengthening at Ambient and Elevated Temperatures of Heat-Treatable Al(Sc) Alloys,” Acta Materialia 50, 4021-4035 (2002). E. A. Marquis and D. N. Seidman, “A Subnanoscale Study of Segregation at Al/Al3Sc Interfaces,”, Proceedings Microscopy and Microanalysis, Volume 8, Supplement 2, 2002, pp. 1100CD-1101CD. C. B. Fuller, D. N. Seidman, and D. C. Dunand, “Mechanical Properties of Al(Sc,Zr) Alloys at Ambient and Elevated Temperatures,” Acta Materialia 51(16) 4803-4814 (2003). E. A. Marquis, D. N. Seidman, M. Asta, C. M. Woodward, and V. Ozoliņš, “Segregation at Al/Al3Sc Heterophase Interfaces on an Atomic Scale: Experiments and Computations,” Physical Review Letters 91, 036101-1 to 036101-4 (2003). C. B. Fuller, J. L. Murray, and D. N. Seidman, “Temporal Evolution of the Nanostructure of Al(Sc,Zr) Alloys: Part I-Chemical Compositions of Al3(Sc1-XZrX) Precipitates,” Acta Materialia 53, 5401-5413 (2005). C. B. Fuller and D. N. Seidman, “Temporal Evolution of the Nanostructure of Al(Sc,Zr) Alloys: Part II-Coarsening of Al3(Sc1-XZrX) Precipitates,” Acta Materialia 53, 5415-5428 (2005). E. A. Marquis and D. N. Seidman, “Nanostructural Evolution of Al3Sc Precipitates in an Al-Sc-Mg Alloy by Three-Dimensional Atom-Probe Microscopy,” Surface and Interface Analysis 36, 559-563 (2004). E. A. Marquis and D. N. Seidman, “Coarsening Kinetics of nanoscale Al3Sc Precipitates in an Al-Mg-Sc Alloy,” Acta Materialia 53, 4259-4268 (2005). M. van Dalen, D. C. Dunand, and D. N. Seidman, “Effects of Ti Additions on the Microstructure and Creep Properties of Precipitation-Strengthened Al-Sc Alloys, Acta Materialia 53, 4225-4235 (2005). E. A. Marquis, D. N. Seidman, M. Asta, and C. Woodward, “Effects of Mg on the Nanostructural Temporal Evolution of Al3Sc Precipitates: Experiments and Simulation,” Acta Materialia 54, 119-130 (2006). E. A. Marquis, J. L. Riesterer, D. N. Seidman, and D. J. Larson, “Analysis of Mg Segregation at Al/Al3Sc Interfaces by Atom-Probe Tomography,” Microscopy & Microanalysis 2006, Navy Pier, Chicago, IL, Microscopy & Microanalysis 12 (Supp 2) 914 CD (2006). R. A. Karnesky, M. E. van Dalen, D. C. Dunand, and D. N. Seidman, “Effects of Substituting Rare-Earth Elements for Scandium in a Precipitation-Strengthened Al-0.08 at.% Sc Alloy,” Scripta Materialia 55, 437-440 (2006). R. Karnesky, D. N. Seidman, and D. C. Dunand, “Creep of Al-Sc Microalloys with Rare-Earth Element Additions,” International Aluminum Alloy Congress, Vancouver, British Columbia. Canada, Materials Science Forum 519-521, 1035-104 (2006). R. A. Karnesky, D. C. Dunand, and D. N. Seidman, “Evolution of Nanoscale Precipitates in Aluminum Microalloyed with Scandium and Erbium,” Acta Materialia, 57, 4022-4031 (2009). M. E. van Dalen, R. A. Karnesky, J. R. Cabotaje, D. C. Dunand, D. N. Seidman, “Erbium and Ytterbium Solubilities in Aluminum as Determined by Nanoscale Characterization of Precipitates,” Acta Materialia, 57, 4081-4089 (2009). K. E. Knipling, R. A. Karnesky, C. P. Lee, D. C. Dunand, and D. N. Seidman, “Precipitation Evolution in Al-0.1 Sc, Al-0.1 Zr, and Al-0.1 Sc-0.1 Zr (at.%) Alloys During Isochronal Aging,” Acta Materialia, 58, 5184-5195 (2010). C. Monachon, D. C. Dunand, and D. N. Seidman, “Atomic-Scale Characterization of Aluminum-Based Multi-Shell Nanoparticles Created by Solid-State Synthesis,” Small, 6 (16), 1728-1731 (2010). O. Beeri, D. C. Dunand, and D. N. Seidman, “Role of Impurities on Precipitation Kinetics of Dilute Al-Sc Alloys,” Materials Science and Engineering A, 527, 3501-3509 (2010). M. E. Van Dalen, D. C. Dunand, and D. N. Seidman “Microstructural Evolution and Creep Properties of Precipitation-Strengthened Al-0.06Sc-0.02Gd and Al-0.06Sc-0.02Yb (at.%) Alloys,” Acta Materialia, 59, 5224-5237 (2011). M. E. van Dalen, T. Gyger, D. C. Dunand, D. N. Seidman “Effects of Yb and Zr Micro-Alloying Additions on the Microstructures and Mechanical Properties of Dilute Al-Sc Alloys” Acta Materialia, 59, 7615-7626 (2011). C. Booth-Morrison, D. C. Dunand, and D. N. Seidman, “Coarsening Resistance at 400 ˚C of Precipitation-Strengthened Al-Zr- Sc-Er Alloys,” Acta Materialia, 59, 7029-7042 (2011). C. Booth-Morrison, D. N. Seidman, and D. C. Dunand, “Effect of Er Additions on Ambient and High-Temperature Strength of Precipitation-Strengthened Al-Si-Zr-Sc Alloys,” Acta Materialia 60, 3643-3654 (2012). C. Booth-Morrison, Z. Mao, M. Diaz, C. Wolverton, D. C. Dunand, D. N. Seidman. “On the Role of Si in Accelerating the Nucleation of ’-Precipitates in Al-Zr-Sc Alloys,” Acta Materialia, 60, 4740–4752 (2012). N. Q. Vo, D. C. Dunand, and D. N. Seidman, “Improving Aging and Creep Resistance in a Dilute Al-Sc-Si Alloy by Microalloying with Zr and Er," Acta Materialia, 63, 73-85 (2014). A. De Luca, D. C. Dunand, D. N. Seidman, “Mechanical Properties and Optimization of the Aging of a Dilute Al-Sc-Er-Zr-Si Alloy with a High Zr/Sc Ratio,” Acta Materialia, 119, 35-42 (2016). N. Q. Vo, D. C. Dunand, D. N. Seidman, “Role of Silicon on Precipitation Kinetics of Dilute Al-Zr-Sc-Er alloys,” Materials Science and Engineering A, 677, 485-495 (2016). J. D. Lin, P. Okle, D. C. Dunand, D. N. Seidman, “Effects of Sb Micro-Alloying on Precipitate Evolution and Mechanical Properties of a Dilute Al-Sc-Zr Alloy,” Materials Science and Engineering A, 680, 64-74 (2017). A. De Luca, D. C. Dunand, D. N. Seidman, “Microstructural and Mechanical Properties of a Dilute Al-Sc-Er-Zr-Si Alloy,” to be submitted to Acta Materialia, August (2017). ___________________________________________________________________________ We have studied the silicidation of silicon with thin films of nickel and in particular the effects of Pd or Pt additions on the crystal structures of the nickel silicides utilizing synchrotron radiation at the Advanced Photon Source, Argonne National Laboratory. This research is being performed in cooperation with Prof. Lincoln Lauhon, Northwestern University, and Prof. Yossi Rosenwaks, Tel Aviv University. The aim being to correlate the local chemical compositions of the nickel silicide films, as measured by atom-probe tomography at Northwestern University, with the local work function as measured by Kelvin Probe Force Microscopy at Tel Aviv University. This research was sponsored by the Semiconductor Research Corporation, the US-Israel Binational Science Foundation and IBM Thomas J. Waston Research Center, Yorktown Heights, New York. P. Adusumilli, L. J. Lauhon, D. N. Seidman, C. E. Murray, O. Avayu, and Y. Rosenwaks, “Tomographic Study of Atomic-Scale Redistribution of Platinum During the Silicidation of Ni0.95Pt0.05/Si(100) thin-films" Applied Physics Letters, 94, 103113-1 to 103113-3 (2009). P. Adusumilli, C. E. Murray, L. J. Lauhon, O. Avayu, Y. Rosenwaks, D. N. Seidman, “Three-Dimensional Atom-Probe Tomographic Studies of Nickel Monosilicide/Silicon Interfaces on a Subnanometer Scale,” ECS Transactions, 19(1), 303- 314 (2009)”. P. Adusumilli, D. N. Seidman, C. E. Murray, C. Lavoie, and B. Yang, “Redistribution of Arsenic Dopant Atoms During Silicidation of Ni0.95Pt0.05 Thin-Films,” to be submitted to Journal of Applied Physics, 2017. P. Adusumilli, D. N. Seidman, C. E. Murray, C. Lavoie, and B. Yang, “Effects of a TiN Cap Layer on the Silicidation Kinetics of Ni0.95Pt0.05 Thin-Films,” to be submitted to Microelectronics Engineering, 2017. ______________________________________________________________________________ In June 2001 the three-dimensional atom-probe (3DAP) microscope or conventional atom-probe tomograph commenced working reasonably well; the ultrahigh vacuum system for this instrument was designed and fabricated at Northwestern University and made to work with components purchased from the then Kindbrisk Company, later called Oxford Nanoscience Ltd., which was part of the Polaron plc Company. In 2008 Oxford Nanoscience Ltd. was purchased by Imago Scientific Instruments, Madison, Wisconsin, which reduced the number of manufacturers of atom-probe tomographs in the world to two, Imago Scientific Instruments and Cameca. The latter sold an instrument that was designed and fabricated at the University of Rouen. On April 1, 2010 Ametek, which owns Cameca, purchased Imago Scientific Instruments and discontinued the atom-probe tomograph designed at the University of Rouen and there is now only one source of instruments, Cameca, unfortunately. At Northwestern University we purchased from Cameca (December 2004) a local-electrode atom-probe tomograph (LEAP) 4000X Si, which currently utilizes a picosecond ultraviolet laser (wavelength = 355 nm) to dissect specimens essentially one atom at a time. I received recently an ONR DURIP grant, for $1,210,000, to upgrade the LEAP4000X Si to a LEAP5000XS to increase the detection efficiency to 80% from 50%, which is a 60% increase in detection efficiency and to increase the field-of-view. The upgrade will take place in the last quarter of 2017. Educational Mission M.S. Students 1. Lewis A. Beavan Research Engineer, Atomics M.S. degree, 1971 International, California 2. James W. Bohlen Career Naval Officer, U. S. Navy M.S. degree, 1971 3. John J. Burke Staff Engineer, TRW Corporation M.S. degree, 1974 Cleveland, OH 4. Ching-Yu Wei Staff Scientist, General Electric M.S. degree, 1975 Corporate Research & Development Laboratory, Schenectady, NY 5.. Charles H. Nielsen Manager, Electron Microscopy M.S. degree, 1977 Laboratory, JEOL Corporation Boston, MA 6.. Mr. Roi Gat Scientist in an Israeli high-tech M.S. degree, 1985 startup company Hebrew University 7. Mark R. Holzer Staff Engineer, 3M Corp. M. S. degree, 1989 Minneapolis, MN 8. Daniel J. Deputy Staff Engineer, Intel Corp. M.S. degree, 1990 Phoenix, AZ 9. Tracey L. Wolfsdorf WOLFSDORF BRENNER, INC M.S., 1994 Negotiation & Conflict Manag. For Technology People Boston, Massachusetts 10. Karthik Hariharan Consultant, Boston Consulting M.S. degree, 1994 Chicago, IL 11. Mr. Daniel Cecchetti Software Company M.S. degree, 2011 Madison, WI 12. Mr. Xin Yin Northwestern University M.S. degree, 2013 13. Tianyu (Judy) Zhu Co-supervised with Prof. David C. Dunand, Northwestern University Northwestern University M.S. Degree, 2015 14. Phillip Okle Ph.D. student M.S. degree, 2015 ETH, Zurich, Switzerland 15. James McKinney Northwestern University M.S. degree, 2015 16. I-Wen Hsieh Northwestern University M.S. degree, 2015 17. Jeffrey D. Lin Northwestern University M.S. degree, 2015 Fan-Ping Cui Ph.D. Student M.S. degree, 2017 University of Illinois, Urbana-Champaign, IL 19. Ms. Francesca Long Co-supervised with Prof. David C. Dunand, Northwestern University Northwestern University 20. Mr. Chunan (Kevin) Li Northwestern University M.S. degree, 2017 now at Trondheim, Norway Ph.D. students 1. Ronald M. Scanlan Group leader, Superconducting Ph.D. degree, 1971 Magnetic Materials, Lawrence Livermore National Laboratory, Livermore, CA 2. Yung-Chang Chen Private Businessman Ph.D. degree, 1971 C. G. Wang Co-supervised with Prof. R. W. Balluffi, Cornell University IBM Watson Laboratory Ph.D. degree, 1971 Yorktown Heights, New York Arnold S. Berger Co-supervised with Prof. R. W. Balluffi, Cornell University Director of Research Ph.D. degree, 1971 Applied Microsystems Corporation 5020 148th Ave. NE PO Box 97002 Richmond, Washington 98073-9702 5. Dieter G. Ast Prof. Emeritus, Materials Science & Ph.D. degree, 1972 Engineering, Cornell University Ithaca, New York 6. Kenneth L. Wilson Group leader, Fusion Materials Ph.D. degree, 1975 Sandia Livermore National Lab. Sandia, CA—retired. 7. Ching-Yu Wei Staff Scientist, General Electric Ph.D. degree, 1975 Corporate Research & Development Laboratory, Schenectady, NY 8. Alfred Wagner Research Scientist, Liquid Metal Ion Ph.D. degree, 1978 Source Technology, IBM Watson Research Center, Yorktown Heights, NY 9. Jacob Aidelberg Group Leader, Silicon Technology Ph.D. degree, 1980 Intel Corporation, Santa Clara, CA Retired, Israel 10. Dipinkar Pramanik Manager of Reliability Ph.D. degree, 1980 VLSI Technology, San Jose, CA 11. Roman Herschitz Staff Scientist R.C.A. Research Ph.D. degree, 1983 Laboratory, Princeton, NJ Cornell University 12. Bradley M., Davis Process Engineer, AMD Corp. Ph.D. degree, 1990 Austin, Texas 13. Jieguang (Jay) Hu Argonne National Ph.D. degree, 1991 Laboratory, Argonne, Illinois 14. Bruce W. Krakauer Engineering Fellow, Materials Ph.D. degree, 1993 AO Smith Corporate Technology Center, Milwaukee, WI 15. Akira Seki Dr. Akira Seki spent two years working with me as a visiting scientist from Sumitomo Metals and he co-published a number of articles with me as you can see from searching for his name in my list of publications, which he submitted to the University of Tokyo and for which he was awarded a Ph.D. degree. Sumitomo Metals Ph.D. degree, 1993 Japan 16. David K. Chan Quintech Electronics Ph.D. degree, 1994 Indiana, Pennsylvania Vice-President for Sales 17. John D. Rittner Interim Technologies Inc. Ph.D. degree, 1996 Oak Brook, IL 18. Yeongcheol Kim Professor Ph.D. degree, 1996 Korea University of Technology and Education Chungcheongnam-do, South Korea 19. Dmitriy A. Shashkov H. C. Starck Inc. Ph.D. degree, 1997 CEO and President Boston, MA 20. Jung-Il Hong Daegu Gyeongbuk Institute Science, Ph.D. degree, 1999 Associate Prof., Chair, Physics Dept., Daegu Metropolitan City, S. Korea 21. Dmitriy Gorelikov Soluris Inc. Ph.D. degree 2001 Senior Scientist 45 Winthrop St. Concord, MA 01742 22. Christian Fuller Co-supervised with Prof. D. C. Dunand, Northwestern University GE Healthcare Life Sciences, Ph.D. degree, 2002 Amersham, 23. Jason Sebastian Questek LLC Ph.D. degree, 2002 Evanston, IL Director of Technology Group 24. Emmanuelle Marquis Co-supervised with Prof. D. C. Dunand , Northwestern University University of Michigan at Ann Arbor Ph.D. degree, 2002 Department of Materials Science Associate Professor of MS&E 25. Kevin E. Yoon US Trade Mark and Patent Office Ph.D. degree, 2004 Patent Examiner 26. Chantal K. Sudbrack QuestTek LLC Ph.D. degree, 2004 Senior Materials Research Engineer Evantson, IL 27. Dr. Stephan Gerstl Atom-Probe Tomography Manager Ph.D., 2005 ETH Zurich, Zurich, Switzerland 28. Keith E. Knipling Co-supervised with Prof. D. C. Dunand, Northwestern University Naval Research Laboratory Ph.D. degree 2006 Research Scientist Washington, D.C. 29. Marsha van Dalen Co-supervised with Prof. D. C. Dunand, Northwestern University Director of Research & Development Ph.D. degree, 2007 at Eye Care & Cure, Tuscon, AZ 30. Richard Karnesky Sandia National Laboratories Ph.D. degree, 2007 Research Staff Scientist Livermore, California 31. R. Prakash Kolli University of Maryland Ph.D. degree, 2007 Dept. Materials Science & Eng. Research professor 32. Christopher Booth-Morrison Rolls Royce Inc. Ph.D. degree, 2009 Materials and Process Engineer Montreal, Canada 33. Daniel Schreiber Co-Supervised with Dr. A. Petford-Long, Argonne National Laboratory Pacific Northwest National Lab. Ph.D. degree, 2011 Research Scientist Richland, Washington 34. Yang Zhou Micron Technology Ph.D. degree, 2010 Process Engineer, Boise, ID 35. Matthew Krug Co-Supervised with Prof. D. C. Dunand, Northwestern University General Electric Ph.D. degree, 2011 Physical Metallurgist Alcoa Center, Pennsylvania 36. Praneet Adusumilli Co-Supervised with Prof. L. J. Lauhon, , Northwestern University IBM Research Laboratory Ph.D. degree, 2011 Staff Scientist Albany, New York 37. Michael D. Mulholland ArcelorMittal Steel Company Ph.D. degree, 2012 Physical Metallurgist South Chicago, Indiana 38. Allan Hunter University of Michigan-Ann Arbor Ph.D. degree, 2012 Manager of Atom-Probe Laboratory 39. Denise Ford Co-Supervised with Dr. L. Cooley, Fermi National Accelerator Laboratory Argonne National Laboratory Ph.D. degree, 2013 Post-doctoral student 40. Peter Bocchini Co-Supervised with Prof. D. C. Dunand, Northwestern University Carpenter Technology Ph.D. degree, 2015 Alabama 41. Elizaveta (Liza) Plotnikov 3M Company Ph.D. degree candidate, ABD Minneapolis, Minnesota 42. Daniel Sauza Co-Supervised with Prof. D. C. Dunand, Northwestern University Alcoa Technical Center Ph.D. degree, 2016 Physical Metallurgist Alcoa Center, Pennsylvania 43. Dr. Divya Jain Intel Corporation Ph.D. degree, 2017 Materials Engineer Chandler, Arizona 44. Yanyan (Ashley) Huang Ms. Y. Huang did her Ph.D. thesis research with me at Northwestern University and was awarded her Ph.D. degree by Chongqing University, P.R.C. Chongqing University, Chongqing Ph.D. degree, to be determined P. R. China 45. Sumit Bhattacharya Co-Supervised with Dr. Michael Pellin, Argonne National Laboratory Research Associate Ph.D. degree, 2017 Argonne National Laboratory Research associate 46. Mr. Zhiyuan (Julian) Sun Co-Supervised with Prof. Lincoln J. Lauhon, Northwestern University Apple Park Ph.D. degree, 2019 Researcher, Flexible electronics Cupertino, California 47. Mr. Ding Wen (Tony) Chung Co-supervised with Prof. David C. Dunand, Northwestern University Northwestern University Ph.D. degree, 2020 Blue Origin, LLC 48. Mr. Richard Mishi Co-supervised with Prof. David C. Dunand, Northwestern University Oak Ridge National Laboratory Ph.D. degree, 2020 Oak Ridge, TN 49. Mr. Qingqiang Ren Co-supervised with Prof. David C. Dunand, Northwestern University Oak Ridge National Laboratory Ph.D. degree, 2020 Oak Ridge, TN 50. Mr. Chia-Pao (Brian) Lee Northwestern University Ph.D. candidate 51. Mr. Daniel F. Rosenthal Co-Supervised with Prof. D. C. Dunand, Northwestern University Northwestern University Ph.D. candidate 52. Ms. Whitney Tso Northwestern University Ph.D. candidate 53. Mr. Eric Viklund Northwestern University Ph.D. candidate Postdoctoral Students 1. Dr. David L. Styris Senior Research Scientist, Battelle Northwest Laboratory 2. Dr. K. H. Lie location unknown 3. Prof. Pierre M. Petroff Professor emeritus, University of California, Santa Barbara, CA 4. Dr. John T. Robinson Private businessman, USA 5. Dr. Brian Dury Private businessman. U. K. 6. Prof. Robert S. Averback Prof. of Materials Science and Engineering, University of Illinois at Urbana, Urbana, IL 7. Dr. Guy Ayrault Private businessman, USA 8. Dr. Thomas M. Hall President, Maxwell Electron Inc. Corporation, Raleigh, NC 9. Dr. Jun Amano Project Manager, Hewlett Packard Corp. Solid State Materials Dept. Palo Alto, CA 10. Dr. Michael I. Current Dean, Engineering Education, Ion Beam Technologies, Applied Materials Inc., Austin, TX 11. Dr. Masahiko Yamamoto Professor Emeritus, Materials Science, Osaka Univ., Japan 12. Dr. Albert T. Macrander Physicist, Group Leader, Advanced Photon Source, Argonne National Editor-in-Chief, Review of Scientific Instruments 13. Prof. Avner Brokman Associate Professor of Materials Science, Hebrew University of Jerusalem, Jerusalem, Israel 14. Dr. X. W. Lin Staff Scientist VLSI Technology, San Jose, CA 15. Dr. Akira Seki Staff Scientist Sumitomo Metals Research Laboratory, Amagasaki, Japan 16. Dr. S.-M. Kuo Staff Engineer, Motorola Corp. Phoenix, AZ 17. Dr. Yoonsik Oh unknown location 18. Dr. Ho Jang Professor of Materials Science Korea University Seoul, South Korea 19. Dr. Gerjan Van Bakel Senior Research Scientist Department of Applied Physics Delft University of Technology Delft, The Netherlands 20. Dr. Dmitry Udler Deutsche Bank Manhattan, New York 21. Dr. Roy Benedek Argonne National Laboratory Materials Science Division 22. Dr. Marilyn Nowakowski Senior Engineer, Intel Hillsboro, Oregon 23. Dr. Xu Zhang Northwestern University 1997-1998 Start-up company in California 24. Dr. Olof Hellman Northwestern University 1997-2000 Microsoft Corporation Redmond, WA 25. Dr. Joerg Ruesing Northwestern University 1998-1999 Deutsche Bank, Frankfort am Main, Germany 26. Dr. Albert Assaban Northwestern University 1999-2000 Marseille, France 27. Dr. Zugang Mao Northwestern University Senior research Associate 2001 to present 28. Dr. Chantal K. Sudbrack Materials Engineer NASA Glenn Research Cleveland, OH for 8.5 years QuesTek, Evanston, IL, 2018-19 29. Dr. Jason Sebastian Chief Executive Officer Questek LLC Evanston, IL 30. Dr. Kevin E. Yoon US Patent and Trade Mark Office 31. Dr. Ofer Beeri Northwestern University, 2005-2006, Negev Nuclear Research Center Dimona, Israel 32. Dr. Yulin (Mark) Lu Northwestern Univ., 01/06 to 01/07 University of Kentucky 33. Dr. Aniruddha Biswas Senior Materials Engineer Baba Nuclear Research Center Mubai, India 34. Dr. Chris Booth-Morrison Co-supervised with Prof. David C. Dunand, Northwestern University, for Booth-Morrision’s postdoctoral stint Materials and Process Engineer Rolls-Royce Ltd. Montreal, Canada 35. Prof. Yeong-Cheol KIM Professor, Korea University of Technology and Education 36. Prof. Yaron Amouyal Associate Prof., Technion-Israel Institute of Technology, Haifa Dept. of Materials Science & Engineering 37. Dr. Ivan D. Blum Materials Engineer CNRS Laboratory at the University of Rouen, France 38. Prof. Yoon-Jun Kim Assistant Professor Inha University South Korea 39. Dr. Nhon Q. Vo NanoAl LLC, Co-Founder Chief Technological Officer CEO Skokie, Illinois 40. Dr. Haiming Wen Visiting post-doctoral student. Co-supervised with Profs. Enrique Lavernia and Julie M. Schoenung of the University of California, Davis and currently at University of California, Irvine. Assistant Professor Missouri University of Science & Technology Rolla, Missouri 41. Dr. Anthony De Luca Co-supervised with Prof. David C. Dunand, Northwestern University, for De Luca’s postdoctoral stint for research on a Ford Research grant on aluminum alloys, May 6th, 2014 through May 18, 2018.   Swiss Federal Laboratories for Materials Science &Technology Empa Zurich, Switzerland 42. Dr. James A. Coakley University of Miami Presently, assistant professor European Union Marie Curie Fellow 43. Mr. Yukihiro Shingaki Northwestern University Visiting Fellow from JFE Steel for two years 44. Dr. Amy Marquardt Northwestern University Post-doctoral research associate 45. Dr. Jacques Perrin Toi nin Northwestern University Post-doctoral research associate 46. Dr. Sung-Il Baik Northwestern University Post-doctoral student August 2, 2010 to 47. Dr. Jae-Yel Lee Northwestern University Post-doctoral research associate Now at FNAl 48. Dr. Amir Farkoosh Northwestern University Post-doctoral research associate 49. Dr. Shipeng Shu Northwestern University Post-doctoral research associate Now at Argonne National Lab. 50. Dr. Fei Zhu Northwestern University Post-doctoral associate Now at UM Ann Arbor 51. Dr. Rafael Casas Northwestern University Post-doctoral associate 52. Dr. Jae-Gil Jung Visitor from Korea Institute of Materials Science (KIMS) 53. Dr. Myung-Yeon Kim Visitor from Research associate professor, visiting scientists, professors, pre-doctoral students and undergraduate students 53. Prof. Dieter Isheim Northwestern University Research Associate Professor 54. Dr. Georges Martin Centre des Etudes Nucleaire Saclay 55. Mr. Michael Benbarhoum British Airways, Manhattan, NY 56. Prof. Noam Eliaz Tel Aviv University, Israel Chair, Department of Materials Science and Engineering 57. Prof. Yi-You TU Southeast University, Nanjing, China 58. Dr. Jiang-Tang JIANG Harbin Institute of Technology, 59. Dr. Yanyan (Ashley) HUANG Chongqing University, Chongqing, 60. Prof. Mehet YILDIRIM Middle East Technical Univ., Ankara 61. Dr. Bernard Aufray CRMC2-CNRS, Campus de Luminy, 62. Dr. Helene Giordano Univ. Aix-Marseille III, France 63. Prof. Yong-Sheng LI Nanjing University of Science & Technology 64. Mr. Leonardo Coelho Universidade Federal de Santa Catarina, Brazil, undergraduate 65. Mr. Luca Mazzaferro Universidade Federal de Santa Catarina, Brazil, undergraduate 66. Prof. Feng SUN Shanghai Jiao Tong University  67. Dr. Weiguo YANG Jisangsu Univ. of Science & Technology, Jiangsu, China 68. Mr. Dong An Predoctoral visiting scholar 2015-2016 plus summer 2016 69. Mr. Fabian Andrioli Brazilian University Undergraduate student 70. Mr. Timothy Murat University of Wisconsin, Madison REU Undergraduate student, summer 2016 71. Ms. Ruiyang Xue Shanghai Jiao Tong University Undergraduate student, summer 2016 Ph.D. student, UI Urbana-Champaign, IL 72. Mr. Fan-ping Cui Shanghai Jiao Tong University Undergraduate student, academic year, 2016-2017, plus summer 2017 73. Ms. Jennie Wang Yale University REU student 75. Mr. Jackson Finamore Colorado School of Mines Summer student, 2017 76. Mr. Rafael Casas Ferreras University of Madrid Visiting pre-doctoral student 77. Ms. Jin-Yeon Kim Seoul National University Visiting pre-doctoral student, 2017 78. Mr. Quentin P. Mineur Visiting student from 79. Mr. Michael Wright Northwestern University Undergraduate student, summer 2018, in cooperation with Dr. Tao SUN, Advanced Photon Source, Argonne National Laboratory April 9, 2023 David N. Seidman Current Positions, Education, Professional Societies, Honors and Awards, Editorial Services, Professional Experiences and Services, Conferences Organized, Listings, Educational Mission, Research Areas and Interests (Past and Present), 6