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Tuning structural, transport, and magnetic properties of epitaxial SrRuO3 through Ba substitution

Zeeshan Ali, Zhen Wang, Alessandro R. Mazza, Mohammad Saghayezhian, Roshan Nepal, Thomas Z. Ward, Yimei Zhu, and Jiandi Zhang
Phys. Rev. B 107, 144405 – Published 5 April 2023
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Abstract

The perovskite ruthenates (ARuO3, A=Ca, Ba, or Sr) exhibit unique properties owing to a subtle interplay of crystal structure and electronic-spin degrees of freedom. Here, we demonstrate an intriguing continuous tuning of crystal symmetry from orthorhombic to tetragonal (no octahedral rotations) phases in epitaxial SrRuO3 achieved via Ba substitution (Sr1xBaxRuO3 with 0x0.7). An initial Ba substitution to SrRuO3 not only changes the ferromagnetic properties, but also tunes the perpendicular magnetic anisotropy via flattening the Ru–O–Ru bond angle (to 180), resulting in the maximum Curie temperature and an extinction of RuO6 rotational distortions at x0.20. For x0.2, the reduction of RuO6 octahedral rotational distortion dominantly enhances the ferromagnetism in the system, though competing with the effect of the RuO6 tetragonal distortion. Further increasing Ba substitution (x>0.2) gradually enhances the tetragonal-type distortion, resulting in the tuning of Ru4d orbital occupancy and suppression of ferromagnetism. Our results demonstrate that isovalent substitution of the Asite cations significantly and controllably impacts both electronic and magnetic properties of perovskite oxides.

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  • Received 28 November 2022
  • Revised 29 January 2023
  • Accepted 17 March 2023

DOI:https://doi.org/10.1103/PhysRevB.107.144405

©2023 American Physical Society

Physics Subject Headings (PhySH)

Condensed Matter, Materials & Applied Physics

Authors & Affiliations

Zeeshan Ali1,*, Zhen Wang1,2,3, Alessandro R. Mazza4,5, Mohammad Saghayezhian1, Roshan Nepal1, Thomas Z. Ward4, Yimei Zhu3,†, and Jiandi Zhang1,6,‡

  • 1Department of Physics & Astronomy, Louisiana State University, Baton Rouge, Louisiana 70803, USA
  • 2University of Science and Technology of China, Hefei, Anhui 230026, People's Republic of China
  • 3Condensed Matter Physics & Materials Science, Department, Brookhaven National Laboratory, Upton, New York 11973, USA
  • 4Materials Science and Technology Division, Oak Ridge National Laboratory, Oak Ridge, Tennessee 37831, USA
  • 5Center for Integrated Nanotechnologies, Los Alamos National Laboratory, Los Alamos, New Mexico 87545, USA
  • 6Beijing National Laboratory for Condensed Matter Physics, Institute of Physics, Chinese Academy of Sciences, Beijing 100190, People's Republic of China

  • *zee89ali@gmail.com
  • zhu@bnl.gov
  • jiandiz@iphy.ac.cn

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Issue

Vol. 107, Iss. 14 — 1 April 2023

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Images

  • Figure 1
    Figure 1

    XRD characterization of Sr1xBaxRuO3 (0x0.7) thin films at room temperature: (a) Long-range coupled (θ-2θ) scan, (b) θ-2θ scan around (002) spot, and (c) obtained out-of-plane pseudocubic (cpc) lattice constant vs Ba-concentration (x). SrTiO3 (002)pc Bragg's reflection and film peaks are marked with * and arrows, respectively.

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  • Figure 2
    Figure 2

    XRD reciprocal space mapping about the (103)pc reflections from (a) x=0, (b) x=0.08, and (c) x=0.2 of Sr1xBaxRuO3 thin films.

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  • Figure 3
    Figure 3

    (a) Large-area HAADF-STEM, and (b) highly magnified HAADF images taken along the [100]-STO direction for Sr0.92Ba0.08RuO3 film. The yellow line marks the substrate-film interface. (c) Dopant-concentration (Sr/Ba) profile of Sr (pink) and Ba (green) extracted from Sr-L and Ba-L edges for Sr0.92Ba0.08RuO3. (d) Large-area, (e) high-magnification HAADF-STEM images taken along the [100]-STO direction, and (f) dopant-concentration (Sr/Ba) profile of Sr (pink) and Ba (green) for Sr0.8Ba0.2RuO3 film.

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  • Figure 4
    Figure 4

    (a) Crystal structure of bulk SrRuO3 (SRO). Orthorhombic (O) and pseudocubic (pc) unit cells are indicated by green and orange color, respectively. (b) Pseudocubic unit cell of SRO. Octahedral rotation is in phase along the [100]pc ([001]O), out of phase about the [010]pc([110]O), and [001]pc([110]O) axes, respectively. (c) Schematic illustrations of orthorhombic SRO unit-cell orientation on a cubic SrTiO3 substrate with two possible orientations (domains A and B). In-phase rotation (+) axis [100]pc of the film lies within the film plane, which aligns along the [100]S of the substrate in domain A, and along [010]S in domain B. (d) Half-integer x-ray reflections for SRO. (e) Representation of octahedral rotation pattern in SRO film. Here, the coordinates are defined with respect to pseudocubic lattice.

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  • Figure 5
    Figure 5

    Domain structure in Sr0.92Ba0.08RuO3 film. (a), (b) Projected crystal structures representing domains A and B along with simulated electron diffraction patterns in the [100]pc (domain A) and [010]pc (domain B) directions. (c), (d) High-resolution STEM images with electron beam incident along the [100]S direction, and corresponding FFT patterns with characteristic fractional spots marked in red (domain B) and green (domain A), respectively. Forbidden spots marked by the arrows, absent in the simulated electron diffractions, were observed due to multiple scattering of the electron and sample. (e) HAADF image of Sr0.92Ba0.08RuO3 film. Dotted yellow line marks the film-substrate interface. (f), (g) Zoom-in images of the regions marked in panel (e) superimposed by the corresponding Asite cation displacement forming zigzag pattern in the Sr/Ba-O plane. (h) Asite cation displacement as a function of distance from substrate.

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  • Figure 6
    Figure 6

    Crystal structure of Sr0.8Ba0.2RuO3 film determined via S/TEM. (a) HRTEM image taken along the [100] direction, and (b) the corresponding FFT pattern. (c) HRTEM image with (d) FFT pattern taken along the [210] direction. FFT patterns are indexed using the notation of the pseudocubic structure. (e) Highly magnified annular bright-field (ABF) STEM image taken along the [100] direction with projected structural model. Yellow line marks the TiO2(Sr/Ba)O interface. In panel (e) an octahedra without tilt could be observed. (f) Half-integer x-ray reflections for Sr0.8Ba0.2RuO3 film.

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  • Figure 7
    Figure 7

    Magnetization as a function of temperature [M(T)], and magnetic field [M(H)] for the family of Sr1xBaxRuO3 (0x0.2) thin films. (a), (b) SrRuO3, (c), (d) Sr0.92Ba0.08RuO3, and (e), (f) Sr0.8Ba0.2RuO3.

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  • Figure 8
    Figure 8

    (a) Sr1xBaxRuO3 (0x0.2) thin films, temperature-dependent resistivity. Inset in panel (a) is temperature-dependent resistivity derivative (dρ/dT) plotted against temperature (T). Magnetoresistance (MR) of (b) SrRuO3, (c) Sr0.92Ba0.08RuO3, and (d) Sr0.8Ba0.2RuO3 thin films measured at different temperatures with magnetic field applied along out-of-plane direction. MR curves are offset to avoid overlap.

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  • Figure 9
    Figure 9

    Anomalous Hall resistivity (ρAHE) of (a) SrRuO3, (b) Sr0.92Ba0.08RuO3, and (c) Sr0.8Ba0.2RuO3. (d) Temperature dependence of anomalous Hall resistivity (ρAHE) measured at the magnetic-field value of 5 T for series of Sr1xBaxRuO3 (0x0.5) thin films.

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  • Figure 10
    Figure 10

    (a) Phase diagram of TC in series of Sr1xBaxRuO3 thin films as function of Ba concentration (x), and ratio of out-of-plane (cpc) and in-plane (apc) pseudocubic lattice constants. (b) Schematic illustration of Ru4d orbitals. RuO6 octahedron undergoes tetragonal crystal-field splitting (ΔT) due to cpc/apc>1.

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