Polym Int 56:461–466 (2007)
Polymer International
Mini Review
‘Bricks and mortar’ nanoparticle
self-assembly using polymers
Palaniappan Arumugam, Hao Xu, Sudhanshu Srivastava and Vincent M Rotello∗
Department of Chemistry, University of Massachusetts Amherst, 710 North Pleasant Street, Amherst, MA 01003, USA
Abstract: Developments in self-assembly methods allow access to hierarchical materials featuring a wide range
of functionality and applications. Polymer-based self-assembly of nanoparticles opens up new avenues for the
fabrication of highly structured nanocomposites that can serve as bridges between ‘bottom-up’ and ‘top-down’
methods. Of various interactions leading to self-assembly of nanocomposites, hydrogen bonding and electrostatic
interactions are commonly utilized. In this review, we illustrate the design and subsequent property tuning of
various self-assembled nanocomposite materials that were developed based on these interactions.
2007 Society of Chemical Industry
Keywords: nanoparticle assembly; self-assembly; nanocomposites; polymer-based self-assembly
INTRODUCTION
The constant demand for technologically advanced
devices has led to the development of a wide range
of functional materials, including nanoparticle-based
nanocomposite materials.1 – 3 Nanoscale structures are
traditionally achieved using various lithographic techniques (‘top-down’ approach), and are currently
reaching their inherent limitations with respect to their
smallest readily achievable features (<20 nm). Smaller
structures can be easily synthesized, but assembling
them on substrates (for device applications) in an
ordered fashion still remains as a challenge.4,5 The
recent advancements in synthesis and self-assembly
of polymer-based nanocomposite materials provides a
useful approach to this sort of fabrication.6 – 8 In addition, the self-assembly process provides versatile ways
to tailor physical and chemical properties of nanocomposite materials by varying the polymer chain length,
nanoparticle (NP) size, number of assembly layers, and
interparticle spacing between neighboring NPs.9 – 11
The non-covalent interactions that dictate selfassembly are hydrogen bonding, dipole–dipole, electrostatic, van der Waals, and hydrophobic interactions,
between the polymers (supramolecules) and NPs. Selfassembly of NPs and polymers can also be achieved
through covalent bonding but is beyond the scope of
this review.12,13 Of the above non-covalent interactions, electrostatic and hydrogen bonding interactions
play crucial roles in supramolecule–NP self-assembly.
The binary nature of electrostatic interactions provides a straightforward approach to assembly, whereas
the interest in hydrogen bonding-based self-assembly
arose initially from biological system where such
interactions led to the formation of well-ordered
system, e.g. the formation of α-helix and β-sheet
peptide structures. In this article, the use of hydrogen bonding for the self-assembly of nanocomposite
materials is reviewed.
NANOPARTICLE ‘BRICKS’
NPs provide the ‘bricks’ for polymer-mediated bricksand-mortar self-assembly. Synthetic routes are well
established for the preparation of different types of
NPs, including metal, metal oxides, chalcogenides,
pnictides, and semiconductors, with controlled size
and shape.14 – 17 The tunable size-dependent properties exhibited by these materials further enhance their
utility as building blocks for self-assembly.
The first step towards self-assembly is the functionalization of NP surfaces to provide controlled interactions with polymers and/or substrates, and is generally
achieved in a two-stage process. Initially the NPs are
synthesized with a passive organic monolayer which
prevents particle aggregation. The next step involves
complete or partial replacement of the passive organic
layer with appropriate functional group(s) in what
is known as a place-exchange process. This process
has been demonstrated for variety of NPs including
metal, metal oxide, and semiconductors.18 – 22 A typical displacement reaction is represented schematically
in Fig. 1(a).
POLYMER ‘MORTAR’
The next stage of the self-assembly involves introduction of functional/terminal groups in the polymer
moiety (Fig. 1(b)) to provide an affinity towards
∗
Correspondence to: Vincent M Rotello, Department of Chemistry, University of Massachusetts, Amherst, MA 01002, USA
E-mail: rotello@chem.umass.edu
Contract/grant sponsor: NSF; contract/grant number: CHE-0518487
Contract/grant sponsor: University of Massachusetts Center for Hierarchical Manufacturing; contract/grant number: NSEC, DMI-0531171
(Received 4 August 2006; revised version received 6 September 2006; accepted 24 October 2006)
Published online 6 February 2007; DOI: 10.1002/pi.2210
2007 Society of Chemical Industry. Polym Int 0959–8103/2007/$30.00
P Arumugam et al.
Figure 1. General schematic of NP self-assembly. (a) Place exchange of NP surface with appropriate functional groups. (b) Addition of the
complementary functional groups to polymers. (c) Electrostatic and/or hydrogen bonding interaction between NP surface and functional polymers
leads to self-assembly of NPs.
surface-functionalized NPs and to direct self-assembly
(Fig. 1(c)). As with NPs, there are numerous strategies for polymer synthesis, including living radical
polymerization (LRP) and ring-opening metathesis
polymerization (ROMP).23 – 25 The ‘living’ nature of
both of these processes allows the ready synthesis of
block copolymers26,27 that can be further functionalized either before or after the polymerization process.
The introduction of functional monomers during
the polymerization process allows growth of polymers with versatile functionality. Nonetheless, there
are challenges in terms of processability as the polymerization conditions and rates may differ for different
functional monomers. As an alternative, functionality
in polymers can be introduced after the polymerization process. Thus, using one polymer scaffold, a series
of polymers with similar structures and varying functionality can be synthesized.28 – 30 In addition to linear
polymers, highly branched macromolecules (such as
dendrimers) can also be used as nanometric building blocks, as these molecules can offer wide range
of functionality and structures.31,32 The chemistry in
this area is well developed for accurate placement of
functionality along the branching chains.33,34
DENDRIMER-MEDIATED SELF-ASSEMBLY OF
NANOPARTICLES
Precise control of the optical and magnetic properties of the NPs is essential for further progress
in fields such as optical storage, optical computing, magnetic storage, magnetic refrigeration,
and biosensors.35 – 37 Traditionally, these properties
of NPs are affected by the particle size and/or
shape. Through dendrimer-mediated self-assembly,
Frankamp et al. demonstrated a novel way to regulate the interparticle spacing of gold38 and magnetic properties of iron oxide (γ -Fe2 O3 ) NPs.39
They fabricated thin films of gold nanocomposites
using carboxylic acid-functionalized gold NPs (‘brick’)
and amine-terminated polyamidoamine (PAMAM)
462
dendrimers (‘mortar’). The precise control of spacing between NPs by different dendrimer generations,
generation G0 to G4, enabled them to blue-shift
the surface plasmon resonance (SPR) of as-formed
thin films. Thus, the modulation of dipolar coupling
between NPs provides a new approach to tune the optical properties of nanocomposite materials.40 The same
group has influenced the spacing between magnetic
NPs (e.g. γ -Fe2 O3 ) again by the use of a PAMAM
dendrimer39 and observed sequential changes in the
blocking temperature (the temperature below which
a superparamagnetic material shows ferromagnetic
behavior) with an increase in dendrimer generations.
The general sense of increase in interparticle spacing (d) between NPs upon dendrimer assembly is
represented in Fig. 2.
In another approach, Boal et al. developed a complementary technique, using a triazine-functionalized
linear polymer (mortar) and γ -Fe2 O3 NPs (brick),
to control the spacing between magnetic NPs in
a polymer–NP assembly.41 First, γ -Fe2 O3 NPs of
∼6.5 nm diameter were synthesized by a literature
method42 followed by a place-exchange reaction with
thymine-functionalized diol ligand. The ligand favors
hydrogen bonding interactions with triazine polymer
and leads to self-assembly of γ -Fe2 O3 nanocomposites. Upon assembly, a decrease in blocking temperature was observed, compared to blocking temperature
from nanoparticle precipitate, and attributed to the
increased spacing between the particles. Thus, the
controlled manipulation of interparticle spacing provides new dimensionality to influence the optical
and magnetic properties (other than shape and size)
of NPs.
MULTIPOINT INTERACTION-INDUCED
SELF-ASSEMBLY
The reversibility, controlled affinity, and high specificity of hydrogen bonding-based self-assembly allow
one to design ordered arrays of NPs. By using
Polym Int 56:461–466 (2007)
DOI: 10.1002/pi
‘Bricks and mortar’ nanoparticle self-assembly
Figure 2. Schematic representation of sequential increase in interparticle spacing d upon assembly with different generations of PAMAM
dendrimer.
Figure 3. Multipoint hydrogen bonding-based self-assembly. (a) Six-point hydrogen bond formation between barbituric acid-functionalized gold
NPs and Hamilton receptor-functionalized block copolymer (BCP). (b) Self-assembly of NPs on a thin film of microphase separated BCP.
multipoint hydrogen interactions, two- and threedimensional self-assembled nanocomposites are generated and the NPs of such assembly are found
to exhibit different physical properties compared to
the isolated particles.43 Based on six-point hydrogen bonding interactions, Binder et al. controlled the
binding of barbituric acid-functionalized gold NPs
onto specific sites of microphase-separated block
copolymers (BCPs)44 (Fig. 3). One block of the
poly(oxynorbornenes) BCP was functionalized with
a receptor to favor six-point hydrogen bonding with
the NPs, while the other block was functionalized
with a fluorinated side chain to favor microphase separation. The immobilization of NPs by the use of
supramolecular interactions leads to generation of a
new class of hybrid nanoscale materials with potential
applications in multifunctional biosensors and novel
electronic, mechanical, and photonic devices.30
As in the case with block copolymers, different functionality can be introduced onto predefined regions
of surfaces to make the surface a suitable substrate
Polym Int 56:461–466 (2007)
DOI: 10.1002/pi
for orthogonal self-assembly. Xu et al. demonstrated
the formation of orthogonal self-assembly by taking
advantage of electrostatic, hydrogen bonding, and
hydrophobic interactions.45 First, they made a silicon
wafer surface positive by spin casting poly(4-vinyl-Nmethylpyridinium iodide) (PVMP) on the wafer. Then
spin-casting of a thymine-functionalized polystyrene
(Thy-PS) overlayer was performed followed by exposing the surface to UV light under a photoresist mask.
The overall process resulted in the generation of
Thy-PS squares and positively charged PVMP lines
(Fig. 4(a)).45
The generation of orthogonal patterns was then
demonstrated by the use of diaminopyridinefunctionalized polystyrene (DAP-PS) and carboxylatederivatized CdSe@ZnS core–shell NPs (COONP). The three-point hydrogen bonding between
diamidopyridine-thymine and electrostatic interactions between pyridinium-carboxylate led to the
fabrication of self-assembled orthogonal patterns
(Fig. 4(b). The selective depositions of NPs on specific
463
P Arumugam et al.
Figure 4. Schematic representation of an orthogonal self-assembly process. (a) Functionalization of silicon wafer surface with PVMP and Thy-PS
polymer. (b) Orthogonal pattern generation through PS-Thy:PS-DAP recognition and PVMP:COO-NP electrostatic interactions.
sites of the polymer templated surfaces gives the possibility of generating complex self-assembled patterns
and also provides new horizons for the hierarchical
organization of nanostructure materials on surfaces.
THREE-DIMENSIONAL SELF-ASSEMBLY:
CONSTRUCTION AND INCLUSION OF
TAILORED PROPERTIES
The reversible nature of hydrogen bonding and electrostatic interactions allows one to tailor the morphology and functional properties of supramolecular
nanostructures at the same time. Using diblock copolymers [P4VP(MSA)1 (PDP)1 and PS] composed of
a coil-like block and a polymer–amphiphile complex block, Ruokolainen et al. controlled a polymeric
microstructure at two length scales.46 They took
advantage of the effects of hydrogen bonding at different temperatures to transform the microstructure
morphology. As shown in Fig. 5(a), below 100 ◦ C, the
P4VP(MSA)1 (PDP)1 and PS blocks form a lamellar structure (alternating layers) with a long period
Lb ≈ 35 nm and further microphase separates into
another lamellar structure with a period Lc ≈ 4.8 nm.
In the 100–150 ◦ C temperature region, the second
lamellar structure disappears along long period Lc ,
while retaining the first lamellar structure along long
period Lb (Fig. 5(b)). This leads to the formation of an
order–disorder assembly which can be further manipulated at higher temperatures (>150 ◦ C) to form an
order–order assembly. The second lamellar structure
converts into a cylindrical shape above 150 ◦ C. The
system shows tunability of the protonic conductivity
upon change in morphology.
Shenhar et al. regulated the spatial distribution of
guest molecules within block copolymer films using
molecular recognition methods.47 Block copolymers,
made of polystyrene in one block (apolar domain)
464
and polystyrene bearing 2,6-diamidopyridine (DAP)
in another block (polar domain) (represented by
PS-b-PS/DAP), were used as a polymer scaffold.
Thymine (Thy), and N(3)methyl-thymine (MeThy)
both bearing polyether dendron backbones were used
as guests. Three-point hydrogen bonding between
Thy and DAP regulated the distribution of the
guest while the increase in dendrimer generation
regulated the morphology of the block copolymer to
lamellar, cylindrical, and spherical shapes (Fig. 6).
Thus, hierarchical materials showing a wide range of
applications were accessed by the integration of block
copolymer self-assembly with molecular recognition
processes.
The possibility of using self-assembled nanocomposites for potential drug delivery systems was demonstrated by Thibault et al.48 where they utilized the
complementary interaction between the DAP- and
Thy-functionalized polymers to form recognitioninduced polymersome (RIP) vesicles. By making use of
competition between monovalent (flavin) and multivalent guest molecules (Thy-Au) to bind to RIP, they
controlled the stability of RIP. Tailored stability of
RIP provided a platform for controlled release of guest
molecules attached to it.
CONCLUSIONS AND FUTURE DIRECTIONS
Self-assembly of nanocomposites based on recognition
between polymers and NPs provides new dimensionality in nanofabrication processes where the generation of high-performance and low-cost devices is of
paramount importance. The ability to direct reversible
hydrogen bonding and/or electrostatic interactions in
one, two, and three dimensions, at predefined positions, provides immense flexibility to self-assembly
processes. The tunable properties exhibited by these
nanocomposite materials can be exploited in fields
ranging from electronics to molecular biology.
Polym Int 56:461–466 (2007)
DOI: 10.1002/pi
‘Bricks and mortar’ nanoparticle self-assembly
Figure 5. Graphical representation of the self-organized structures of PS-block-P4VP(MSA)1 (PDP)1 . (a) Alternating two-dimensional PS layers and
one-dimensional P4VP(MSA)1 and PDP layers at temperature below 100 ◦ C. (b) Alternating PS and disordered P4VP(MSA)1 (PDP)1 lamellae in the
temperature region 100–150 ◦ C. (c) One-dimensional disordered P4VP(MSA)1 (PDP)x (with x ≪ 1) cylinders within the three-dimensional PS-PDP
above 150 ◦ C. (Reprinted with permission from Ruokolainen J, Makinen R, Torkkeli M, Makela T, Serimaa R, Brinke Gt et al., Science 280:557–560
(1998)).
Figure 6. Strategy for molecular recognition-based self-assembly. (a) Three-point hydrogen bonding between 2,6-diaminopyridine
(DAP)-functionalized block copolymers (BCPs) and thymine-functionalized dendron macromolecules. (b) Transmission electron micrographs show
change in morphology of BCPs with change in dendron generations.
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P Arumugam et al.
While researchers have made considerable progress
in understanding and harnessing self-assembly, the
extent of complex structures that can be obtained
through the self-assembly is limited. Simple entropy
gain, cooperative non-covalent interactions, and nonspecific packing would be insufficient to obtain multicomponent complex structures. As such, enhanced
understanding of the fundamental nature of selfassembly, coupled with new developments in polymer
and particle synthesis should open up new avenues for
the creation of functional materials.
ACKNOWLEDGEMENTS
The support of the NSF (CHE-0518487) and the
University of Massachusetts Center for Hierarchical
Manufacturing (NSEC, DMI-0531171) is gratefully
acknowledged.
REFERENCES
1 Bakueva L, Musikhin S, Sargent EH, Ruda HE and Shik A,
in Handbook of Organic–Inorganic Hybrid Materials and
Nanocomposites, vol. 2. American Scientific Publishers,
Stevenson Ranch, California, pp. 181–215 (2003).
2 Shenhar R, Norsten TB and Rotello VM, Adv Mater 17:657
(2005).
3 Sanchez C, Soler-Illia G, Ribot F, Lalot T, Mayer CR and
Cabuil V, Chem Mater 13:3061 (2001).
4 Cui Y and Lieber CM, Science 291:851 (2001).
5 Arumugam P, Shinozaki SS, Wang R, Mao G and Brock SL,
Chem Commun 1121 (2006).
6 Leunissen ME, Christova CG, Hynninen AP, Royall CP,
Campbell AI, Imhof A, et al, Nature 437:235 (2005).
7 Zeng H, Li J, Liu JP, Wang ZL and Sun S, Nature 420:395
(2002).
8 Boal AK, Ilhan F, DeRouchey JE, Thurn-Albrecht T, Russell TP and Rotello VM, Nature 404:746 (2000).
9 Gittins DI, Bethell D, Schiffrin DJ and Nichols RJ, Nature
408:67 (2000).
10 Taton TA, Mirkin CA and Letsinger RL, Science 289:1757
(2000).
11 Sandrock ML and Foss CA, J Phys Chem B 103:11398
(1999).
12 Peng H, Tang J, Pang J, Chen D, Yang L, Ashbaugh HS, et al,
J Am Chem Soc 127:12782 (2005).
13 Zin MT, Yip H-L, Wong N-Y, Ma H and Jen AKY, Langmuir
22:6346 (2006).
14 El-Sayed MA, Acc Chem Res 34:257 (2001).
15 Masala O and Seshadri R, Annu Rev Mater Res 34:41 (2004).
16 Murray CB, Kagan CR and Bawendi MG, Annu Rev Mater Sci
30:545 (2000).
17 Brock SL, Perera SC and Stamm KL, Chem Eur J 10:3364
(2004).
18 Templeton AC, Wuelfing WP and Murray RW, Acc Chem Res
33:27 (2000).
466
19 Templeton AC, Hostetler MJ, Warmoth EK, Chen S, Hartshorn
CM, Krishnamurthy VM, et al, J Am Chem Soc 120:4845
(1998).
20 Boal AK, Das K, Gray M and Rotello VM, Chem Mater 14:2628
(2002).
21 Hong R, Fischer NO, Emrick T and Rotello VM, Chem Mater
17:4617 (2005).
22 Peng XG, Wilson TE, Alivisatos AP and Schultz PG, Angew
Chem Int Ed 36:145 (1997).
23 Chiefari J, Chong YK, Ercole F, Krstina J, Jeffery J, Le TPT,
et al, Macromolecules 31:5559 (1998).
24 Hawker CJ and Wooley KL, Science 309:1200 (2005).
25 Bielawski CW and Grubbs RH, Angew Chem Int Ed 39:2903
(2000).
26 Hawker CJ, Bosman AW and Harth E, Chem Rev 101:3661
(2001).
27 Coessens V, Pintauer T and Matyjaszewski K, Prog Polym Sci
26:337 (2001).
28 Shenhar R, Sanyal A, Uzun O, Nakade H and Rotello VM,
Macromolecules 37:4931 (2004).
29 Carroll JB, Jordan BJ, Xu H, Erdogan B, Lee L, Cheng L, et al,
Org Lett 7:2551 (2005).
30 Malkoch M, Thibault RJ, Drockenmuller E, Messerschmidt M,
Voit B, Russell TP, et al, J Am Chem Soc 127:14942 (2005).
31 Jikei M and Kakimoto M, Prog Polym Sci 26:1233 (2001).
32 Zimmerman SC, Zeng FW, Reichert DEC and Kolotuchin SV,
Science 271:1095 (1996).
33 KukowskaLatallo JF, Bielinska AU, Johnson J, Spindler R,
Tomalia DA and Baker JR, Proc Natl Acad Sci USA 93:4897
(1996).
34 Vogtle F, Gestermann S, Hesse R, Schwierz H and Windisch B,
Prog Polym Sci 25:987 (2000).
35 Murray CB, Kagan CR and Bawendi MG, Annu Rev Mater Sci
30:545 (2000).
36 Spaldin N, Magnetic Materials: Fundamentals and Device Applications. Cambridge University Press, Cambridge, UK, p. 250
(2003).
37 Zhu M-Q, Zhu L, Han JJ, Wu W, Hurst JK and Li ADQ, J Am
Chem Soc 128:4303 (2006).
38 Frankamp BL, Boal AK and Rotello VM, J Am Chem Soc
124:15146 (2002).
39 Frankamp BL, Boal AK, Tuominen MT and Rotello VM, J Am
Chem Soc 127:9731 (2005).
40 Srivastava S, Frankamp BL and Rotello VM, Chem Mater
17:487 (2005).
41 Boal AK, Frankamp BL, Uzun O, Tuominen MT and Rotello
VM, Chem Mater 16:3252 (2004).
42 Rockenberger J, Scher EC and Alivisatos AP, J Am Chem Soc
121:11595 (1999).
43 Huang C-H, McClenaghan ND, Kuhn A, Bravic G and Bassani DM, Tetrahedron 62:2050 (2006).
44 Binder WH, Kluger C, Straif CJ and Friedbacher G, Macromolecules 38:9405 (2005).
45 Xu H, Hong R, Lu T, Uzun O and Rotello VM, J Am Chem Soc
128:3162 (2006).
46 Ruokolainen J, Makinen R, Torkkeli M, Makela T, Serimaa R,
Brinke Gt, et al, Science 280:557 (1998).
47 Shenhar R, Xu H, Frankamp BL, Mates TE, Sanyal A, Uzun O,
et al, J Am Chem Soc 127:16318 (2005).
48 Thibault RJ, Galow TH, Turnberg EJ, Gray M, Hotchkiss PJ
and Rotello VM, J Am Chem Soc 124:15249 (2002).
Polym Int 56:461–466 (2007)
DOI: 10.1002/pi