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Solovyova, M. I.; Shtern, D. M.; Kozlov, E. V.

doi:10.1023/a:1020579007493

Russian Physics Journal

2002

DOI: 10.1023/a:1020579007493

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M. I. Solovyova

D. M. Shtern

E. V. Kozlov

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2013

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“…Of these, the C11 b ordered Ti 2 Ni structure and the ordered Ti 5 Ni 3 structure, as plotted in Figure 6, are suggested to be related to the occurrence of the extra diffuse scattering streaks. From Figure 6, a fully ordered C11 b Ti 2 Ni structure can induce diffraction spots at the 0.33 q 001 and 0.67 q 001 positions and a fully ordered Ti 5 Ni 3 structure can induce those at the 0.5 q 001 and 0.75 q 001 positions [12]. These extra diffraction spots induced by the fully ordered C11 b Ti 2 Ni and Ti 5 Ni 3 structures are all located near the edges of the peak intensities of the diffuse scattering streaks shown in Figures 3(b) and 4(c).…”

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“…modified version of the statistical concentration wave method [12,13], previous studies have shown that for a non-stoichiometric composition, many predicted order phases based on a basic B2 structure are possible. Of these, the C11 b ordered Ti 2 Ni structure and the ordered Ti 5 Ni 3 structure, as plotted in Figure 6, are suggested to be related to the occurrence of the extra diffuse scattering streaks.…”

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A study of the structure of G-P zones in Ti-rich TiNi shape memory melt-spun ribbons

Cheng

Chen

2013

Philosophical Magazine

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A hybrid structure composed of ordered C11 b Ti 2 Ni and Ti 5 Ni 3 substructures for the G-P zones precipitated in Ti-rich Ti-Ni shape memory ribbons is proposed to explain the appearance of extra diffuse scattering streaks in transmission electron microscopy observations. The point defects of Ni vacancies and Ti antisites, resulting in the lattice fluctuant displacement, also cause the incommensurate extra diffuse scattering streaks. IntroductionThin films/ribbons of Ti-rich TiNi-based shape memory alloys (SMAs) fabricated by sputtering or melt-spinning have been the subject of much recent research, since their intrinsic large recovery strain and force can be used as powerful microactuators in microelectromechanical systems. TiNi-based SMAs are known to undergo B2→B19′ martenstitic transformation upon cooling. However, an intermediate R-phase (rhombohedral) transformation can be induced easily by the stress field around precipitates, which will depress the B19′ transformation temperature simultaneously. When the R-phase transformation is induced, TiNi SMA undergoes a two-stage B2→R→B19′ transformation. As a result, an intermediate R-phase transformation may occur prior to B19′ martensitic transformation when the stress field is established around the precipitates [1]. Thin coherent plate-like Ti-rich Guinier-Preston (G-P) zones and the nano-scale disc-like Ti 2 Ni precipitates are found in either sputtered Ti-rich TiNi films heated at various temperatures [1][2][3] or in melt-spun ribbons with or without annealing [4]. Studies using high-resolution transmission electron microscopy (HRTEM) have shown that the plate-like G-P zones contain few epitaxial layers and have perfect coherent interfaces with the B2 matrix [5,6]. The existence of Ti-rich G-P zones in Ti-rich TiNi films/ ribbons is quite interesting since they increase the yield stress for slip deformation, because the coherent strain fields around them resist the dislocation movements, resulting in good shape memory properties [6,7]. The structure of G-P zones is presumed to be a body-centred tetragonal (BCT) lattice, equivalent to the C11 b ordered structure for

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confidence: 97%

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confidence: 99%

A study of the structure of G-P zones in Ti-rich TiNi shape memory melt-spun ribbons

Cheng

Chen

2013

Philosophical Magazine

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Cited by 1 publication

References 3 publications

A study of the structure of G-P zones in Ti-rich TiNi shape memory melt-spun ribbons

A study of the structure of G-P zones in Ti-rich TiNi shape memory melt-spun ribbons

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