Quantitative reorientation behaviors of macro-twin interfaces in shape-memory alloy under compression stimulus in situ TEM

doi:10.1016/j.jmst.2021.08.036

Abstract

Abstract:

Twinning stress is known to be a critical factor for the actuating performance of magnetic shape memory alloys because of the harmful deterioration of their magnetic field-induced strain effect. However, the intrinsic origin of the high twinning stress is still in debate. In this work, we firstly fill this gap by precisely probing the reorientation behaviors of A-C and A-B two common macro-twin interfaces under the stimulus of uniaxial compression in-situ transmission electron microscope. The grain boundary is proved to be the main reason for large twinning stress. The twinning stress of the A-C and A-B type interfaces quantitatively are -0.69 and 1.27 MPa within the plate respectively. The A-C type interface evidently has smaller twinning stress and larger deformation variable than the A-B interface. Under the action of compression, not only the orientations of the crystals have changed, but also the roles of the major and minor lamellae have changed for both interfaces due to the movements of twinning dislocations. Combining in-situ and quasi in-situ electron diffraction data, the reorientation process is clearly and intuitively shown by the stereographic projection. Atomic models and the theory of dislocation motion are proposed to phenomenologically clarify the intrinsic mechanism. This work is believed to not only provide a deeper understanding of the deformation mechanism of magnetic shape memory alloys under uniaxial compression testing, but also discover that compression training is not the mechanical training way to decrease the twinning stress of non-modulated martensite in single crystal shape memory alloys.

Key words: Magnetic shape memory alloys, Non-modulated martensite, Reorientation behavior, Twinning stress, In-situ TEM

Seungchan Cho, Junghwan Kim, Ilguk Jo, Jae Hyun Park, Jaekwang Lee, Hyun-Uk Hong, Bong Ho Lee, Wook Ryol Hwang, Dong-Woo Suh, Sang-Kwan Lee, Sang-Bok Lee. Quantitative reorientation behaviors of macro-twin interfaces in shape-memory alloy under compression stimulus in situ TEM[J]. J. Mater. Sci. Technol., 2022, 107: 243-251.

Figures/Tables 10

Fig. 1. Schematic illustrations of A-C and A-B type interfaces in NM martensite of Ni2MnGa alloy and the direction of in-situ TEM compression experiment applied stress. (a) A-C and (b) A-B type macro-twin interfaces.

Table 1 Lattice correspondence between martensitic variants and parent phase [45].

Variant	[110]_M	[$\bar{1}$10 ]_M	[001]_M
A₁	[$\bar{1}$10 ]_P	[110]_P	[001]_P
B₃	[101]_P	[$\bar{1}$01 ]_P	[010]_P
C₃	[$\bar{1}$01 ]_P	[101]_P	[010]_P
A₂, B₄, C₄	[01$\bar{1}$ ]_P	[011]_P	[100]_P

Fig. 2. The structural characterization of the A-C and A-B type interfaces before compression. (a) The BF image of the A-C type interface, in which top-right and bottom-right inserts are the detected SAED patterns of variants A and C taken from the blue and yellow circles in (a), respectively. (b) The SAED pattern of the twin interface taken from the red circle in (a). (c) The atomic HAADF image of the A-C type interface. (d) The BF image of the A-B type interface, in which top-right and bottom-right inserts are the SAED patterns of variants A and B taken from the blue and green circles in (d), respectively. (e) The SAED pattern taken from the red circle in (d). (f) The atomic HAADF image of the A-B type interface.

Table 2 Twinning elements between the martensitic variants.

Variant pairs	K₁	K₂	η₁	η₂
A₁-B₃ and A₁ C₃	(0$\bar{1}$ 1)	(0$\bar{1}$$\bar{1}$ )	[0$\bar{1}$$\bar{1}$ ]	[0$\bar{1}$ 1]
A₁-A₂, C₃ C₄ and B₃-B₄	($\bar{1}$ 01)	($\bar{1}$ 0$\bar{1}$ )	[$\bar{1}$ 0$\bar{1}$ ]	[$\bar{1}$ 01]

Fig. 3. Mechanical characterization in situ TEM. (a) The recorded stress-depth curves of the A-C type (blue) and A-B type (red) macro-twin interfaces. (b-e) The SEM images before and after compression of the A-C type (b, c) and A-B type (d, e) interface cut into square pillars. Blue and red arrows point out their interface positions, respectively.

Table 3 Schmid factors of two twin systems under compressive loading.

Schmid factor	Intra-plate	Inter-plate
Type A-C	0.3837	0
Type A-B	0.3837	0

Fig. 4. Structural characterization of the two interfaces after compression. (a) The BF image of the A-C type interface, in which top-right and bottom-right insets are the SAED patterns taken from the blue and yellow circles in (a), respectively. (b) The SAED pattern taken from the red circle in (a). (c) The BF image of the A-B type interface, in which top-right and bottom-right insets are the SAED patterns taken from the blue and green circles in (c), respectively. (d) The SAED pattern taken from the red circle in (c).

Fig. 5. The stereographic projections. (a, b) The A-C type interface before and after compression, in which variants A1, A2, C3 and C4 are marked by red, blue, green and purple solid points, respectively. The black points mark the projection of evolved single variant combined by variants A2 and C4. (c, d) The A-B type interface before and after compression, in which variants A1, A2, B3 and B4 are marked by red, blue, green and purple solid points, respectively. The black points mark the projection of evolved single variant combined by variants A2 and B4.

Fig. 6. The atomic models of reorientation behaviors of Ni2MnGa martensitic variants under the uniaxial compression. (a, b) The atomic structure of the A-C type interface before and after compression, respectively. (c, d) The atomic structure of the A-B type interface before and after compression, respectively.

Fig. 7. The geometric models of reorientation behaviors of martensitic variants under compressive loading. (a, c) The generation and movement of the twinning dislocations of the A-C and A-B type interfaces under the compression, respectively, in which arrows show the motion direction of the generated dislocations. (b, d) The outcomes of the A-C and A-B type interfaces after the action of compression, respectively.

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