Abstract
Competition between ground states at phase boundaries can lead to significant changes in properties under stimuli, particularly when these ground states have different crystal symmetries. A key challenge is to stabilize and control the coexistence of symmetry-distinct phases. Using BiFeO3 layers confined between layers of dielectric TbScO3 as a model system, we stabilize the mixed-phase coexistence of centrosymmetric and non-centrosymmetric BiFeO3 phases at room temperature with antipolar, insulating and polar semiconducting behaviour, respectively. Application of orthogonal in-plane electric (polar) fields results in reversible non-volatile interconversion between the two phases, hence removing and introducing centrosymmetry. Counterintuitively, we find that an electric field ‘erases’ polarization, resulting from the anisotropy in octahedral tilts introduced by the interweaving TbScO3 layers. Consequently, this interconversion between centrosymmetric and non-centrosymmetric phases generates changes in the non-linear optical response of over three orders of magnitude, resistivity of over five orders of magnitude and control of microscopic polar order. Our work establishes a platform for cross-functional devices that take advantage of changes in optical, electrical and ferroic responses, and demonstrates octahedral tilts as an important order parameter in materials interface design.
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Data availability
Data presented in the main text are open access and can be found on Zenodo65 or as Source data accompanying this manuscript. Owing to the extent of data presented in the Supplementary Information, it is available upon request from the corresponding authors.
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Acknowledgements
R.R., L.W.M., D.A.M., L.-Q.C. and D.G.S. acknowledge support from the Army Research Office under the ETHOS MURI via cooperative agreement W911NF-21-2-0162. The MIM work (J.Y., D.L. and K.L.) was supported by the Office of Science, Office of Basic Energy Sciences, of the US Department of Energy under contract no. DE-SC0019025. Computational resources were provided by ETH Zürich and the Swiss National Supercomputing Center (CSCS), project ID no. s889. Work at ETH was supported by ETH Zürich and the Körber Foundation. M.F. acknowledges support by the Swiss National Science Foundation project 200021_178825. Z.H. and X.G. were supported by the National Natural Science Foundation of China grant no. 92166104. Work at the Molecular Foundry was supported by the Office of Science, Office of Basic Energy Sciences, of the US Department of Energy under contract no. DE-AC02-05CH11231. L.C. acknowledges financial support from the Ford Foundation and the University of California President’s Postdoctoral Fellowship Program. Y.-T.S. and D.A.M. acknowledge financial support from the Department of Defense, Air Force Office of Scientific Research under award FA9550-18-1-0480. The electron microscopy studies were performed at the Cornell Center for Materials Research, a National Science Foundation (NSF) Materials Research Science and Engineering Centers program (DMR-1719875, NSF-MRI-1429155). The microscopy work at Cornell was supported by the NSF PARADIM (DMR-2039380), with additional support from Cornell University, the Weill Institute and the Kavli Institute at Cornell. The authors acknowledge discussions regarding diffraction imaging with J.-M. Zuo as well as M. Thomas, J. G. Grazul, M. Silvestry Ramos and K. Spoth for technical support and careful maintenance of the instruments. We thank X. Huang, A. Fernandez and P. Meisenheimer for fruitful conversations and M. E. Holtz for preliminary electron microscopy studies. We also acknowledge I. Schulze-Jonack and M. S. Stypa for help with substrate crystal growth.
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R.R., D.G.S., L.C. and A.B.M. conceived the project and planned the experiments. Y.-T.S. and H.K.P. performed TEM, TEM sample preparation and atomically resolved polar and structural analysis under supervision of D.A.M. A.B.M. optimized synthesis of the superlattices and performed reciprocal space maps under supervision of D.G.S. L.C. and P.B. performed in-situ SHG measurements with help from A.R. and E.B, and M.F. L.C., P.B. and E.B. prepared the experimental SHG setup. P.B. performed PFM imaging under supervision from L.C. L.C. and P.B. performed electronic transport measurements. J.Y. and D.L. performed MIM and analysis with supervision from K.L. M.M. performed laboratory-based X-ray structural characterization and analysis. L.C. and E.P designed and microfabricated the electric-field devices. L.C. deposited metal layers. First-principles calculations were performed by B.F.G. under the supervision of N.A.S. Phase field calculations were performed by C.D. and F.X. under the supervision of L.-Q.C. and X.G. under the supervision of Z.H. SHG analysis was completed by L.C., P.B. and M.F. Scandate crystal substrates were grown by S.G. L.C., Y.-T.S., R.R., K.L. and L.W.M. wrote the manuscript.
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K.L. holds a patent on the MIM technology, which is licensed to PrimeNano, Inc., for commercial instruments. The terms of this arrangement have been reviewed and approved by the University of Texas at Austin in accordance with its policy on objectivity in research. The remaining authors declare no conflict of interest.
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Supplementary Figs. 1–26, Table 1, Text 1–9 and refs. 1–10.
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Source Data For Fig. 2
Source data for SHG data plotted in Fig. 2c–e.
Source Data For Fig. 4
Source data for DFT data plotted in Fig. 4e, SHG data plotted in Fig. 4i, resistivity data plotted in Fig. 4j and PFM data plotted in Fig. 4k.
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Caretta, L., Shao, YT., Yu, J. et al. Non-volatile electric-field control of inversion symmetry. Nat. Mater. 22, 207–215 (2023). https://doi.org/10.1038/s41563-022-01412-0
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DOI: https://doi.org/10.1038/s41563-022-01412-0
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