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18
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85038895191
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The strain energy minimization by twin formation is an identical process in both ferroelectric and ferroelastic crystals
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The strain energy minimization by twin formation is an identical process in both ferroelectric and ferroelastic crystals.
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20
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20444369477
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J. D. Eshelby, Solid State Physics: Advances in Research and Applications, edited by F. Seitz and D. Turnbull (Academic, New York, 1956), Vol. 3, p. 79
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J. D. Eshelby, Solid State Physics: Advances in Research and Applications, edited by F. Seitz and D. Turnbull (Academic, New York, 1956), Vol. 3, p. 79.
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21
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85038911067
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See Jona and Shirane (Ref. 16), p. 149
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See Jona and Shirane (Ref. 16), p. 149.
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23
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0030646038
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Materials Research Society P. K. Davies, A. J. Jacobson, C. C. Torardi, and T. A. Vanderah
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D. Balzar, P. W. Stephens, H. Ledbetter, J. Li, and M. L. Dunn, in Solid-State Chemistry of Inorganic Materials, Boston, MA, 1996, edited by P. K. Davies, A. J. Jacobson, C. C. Torardi, and T. A. Vanderah, MRS Symposia Proceedings No. 453 (Materials Research Society, Pittsburgh, PA, 1997), p. 715.
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Li, J.4
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26
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84977244087
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) and comprehensive reviews on dislocation theory and plastic deformation of ionic crystals can be found in monographs by M. T. Sprackling, The Plastic Deformation of Simple Ionic Crystals (Academic, London, 1976)
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Ionic crystals including (Formula presented) are brittle at room temperature and under mechanical deformation the tetragonal phase deforms by twinning easier than by dislocation activation. However, the external electric field will suppress twinning. Dislocations in (Formula presented) were reported already by W. S. Rothwell, J. Am. Ceram. Soc. 47, 409 (1964) and comprehensive reviews on dislocation theory and plastic deformation of ionic crystals can be found in monographs by M. T. Sprackling, The Plastic Deformation of Simple Ionic Crystals (Academic, London, 1976);
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Lothe, J.2
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28
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85038947311
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Oxygen vacancies in (Formula presented) were discussed extensively in the Ref. 4
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Oxygen vacancies in (Formula presented) were discussed extensively in the Ref. 4.
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33
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0003472812
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Addison-Wesley, Reading, MA
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42
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0001617167
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). There are quantitative differences in these models. However, the overall behavior is similar and is not likely to influence the results of this study
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I. Groma, Phys. Rev. B 57, 7535 (1998). There are quantitative differences in these models. However, the overall behavior is similar and is not likely to influence the results of this study.
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Groma, I.1
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43
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85038968824
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Here, we neglect the dislocation-core energy because it is at least a factor of 10 smaller. See, for instance, Sprackling (Ref. 35), p. 48
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Here, we neglect the dislocation-core energy because it is at least a factor of 10 smaller. See, for instance, Sprackling (Ref. 35), p. 48.
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46
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0022733903
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H. Mughrabi, T. Ungar, W. Kienle, and M. Wilkens, Philos. Mag. A 53, 793 (1986).
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48
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85038928326
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This relation assumes that only dislocations with their Burgers vectors coplanar contribute to diffraction-line broadening. Williamson and Smallman (Ref. 36) gave a different relation where all dislocations contribute to the diffraction-line broadening, which is less likely in such a restricted dislocation arrangement
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This relation assumes that only dislocations with their Burgers vectors coplanar contribute to diffraction-line broadening. Williamson and Smallman (Ref. 36) gave a different relation where all dislocations contribute to the diffraction-line broadening, which is less likely in such a restricted dislocation arrangement.
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49
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85038902035
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See Sprackling (Ref. 35), pp. 158, 196
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See Sprackling (Ref. 35), pp. 158, 196.
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50
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33846789188
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See Sprackling (Ref. 35) p. 79. Because in this simple model the dislocation separation within one boundary is equal to the separation between boundaries of the opposite sign, the dislocation strain field is practically constant throughout coherent domains. This implies that the strain-broadened diffraction-line profile is a Gauss function and the size-broadened profile is a Lorentz function, as was obtained for both [001] and [100] of the poled specimen. A more detailed discussion exceeds the scope of this paper. See, for instance, B. E. Warren, in Progress in Metal Physics, edited by B. Chalmers and R. King (Pergamon, New York, 1959), Vol. 8, p. 147 and Ref. 33, and
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See Sprackling (Ref. 35) p. 79. Because in this simple model the dislocation separation within one boundary is equal to the separation between boundaries of the opposite sign, the dislocation strain field is practically constant throughout coherent domains. This implies that the strain-broadened diffraction-line profile is a Gauss function and the size-broadened profile is a Lorentz function, as was obtained for both [001] and [100] of the poled specimen. A more detailed discussion exceeds the scope of this paper. See, for instance, B. E. Warren, in Progress in Metal Physics, edited by B. Chalmers and R. King (Pergamon, New York, 1959), Vol. 8, p. 147 and Ref. 33, and
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51
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