Novel B19\ensuremath{'} strain glass with large recoverable strain

Novel B19′ strain glass with large recoverable strain

Qianglong Liang, Dong Wang, Jian Zhang, Yuanchao Ji, Xiangdong Ding, Yu Wang, Xiaobing Ren, and Yunzhi Wang

Phys. Rev. Materials 1, 033608 – Published 22 August 2017

Abstract

We report a strain glass state (B19′ strain glass) in a Ni-rich TiNi shape memory alloy produced by cold rolling. As compared to previously reported strain glasses, this strain glass state has outstanding properties including quasilinear superelasticity with a large recoverable strain (∼4%), and slim hysteresis and high strength (∼1.0 GPa) over a wide temperature range (∼200 K). The existence of the B19′ strain glass state is confirmed by (i) frequency dispersion of storage modulus, (ii) continuous decrease of electrical resistivity, and (iii) continuous growth of B19′ nanodomains upon cooling. This study proves that the effect of defect strength on the creation of a strain glass state is in parallel to the effect of cooling rate on the creation of a structural glass, e.g., any strain crystal (i.e., martensite) can be turned into a strain glass if strong enough defects could be engineered.

Received 30 December 2016
Revised 3 May 2017

DOI:https://doi.org/10.1103/PhysRevMaterials.1.033608

Physics Subject Headings (PhySH)

Ferroelasticity Glass transition Martensitic phase transition Phase transitions

Glasses Relaxor ferroelectrics Shape-memory materials Spin glasses

Differential scanning calorimetry Rheology techniques Transmission electron microscopy

Condensed Matter, Materials & Applied Physics

Authors & Affiliations

Qianglong Liang¹, Dong Wang^1,*, Jian Zhang^1,†, Yuanchao Ji¹, Xiangdong Ding¹, Yu Wang¹, Xiaobing Ren^1,2, and Yunzhi Wang^1,3,‡

¹Center of microstructure science, Frontier Institute of Science and Technology, State Key Laboratory for Mechanical Behavior of Materials, Xi'an Jiaotong University, Xi'an 710049, China
²Ferroic Physics Group, National Institute for Materials Science, Tsukuba, 305-0047, Ibaraki, Japan
³Department of Materials Science and Engineering, The Ohio State University, 2041 College Road, Columbus, Ohio 43210, USA

^*Corresponding author: Wang_dong1223@xjtu.edu.cn
^†Corresponding author: Jian.zhang@xjtu.edu.cn
^‡Corresponding author: Wang.363@osu.edu

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Vol. 1, Iss. 3 — August 2017

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Figure 1
(a) The change in entropy of transition for samples having different amounts of cold work $ɛ_{p}$ , inset describes the DSC results with $ɛ_{p}$ from 0% to 70% upon cooling. (b) DSC results with $ɛ_{p} = 27 %$ show no obvious endothermic and exothermic peak, the inset shows in situ XRD results indicating that the sample maintains a B2 structure upon cooling.
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Figure 2
DMA measurements of frequency dependence of storage modulus (left axis) upon cooling for $T i_{49.2} N i_{50.8}$ with $ɛ_{p} = 27 %$ (a), $ɛ_{p} = 40 %$ (b), and $ɛ_{p} = 70 %$ (c). The inset shows the Vogel-Fulcher fitting results of $T_{g}$ (storage modulus dip temperature) and $T_{0}$ is the ideal glass frozen temperature. The normalized (at 298 K) electrical resistivity curves (for cooling) of $T i_{49.2} N i_{50.8}$ with $ɛ_{p} = 27 %$ are also shown in (a) (right axis). The arrows indicate temperatures at which the electrical resistivity reaches the extremum points, i.e., local minimum $(T_{ρ \min})$ and local maximum $(T_{ρ \max})$ , respectively.
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Figure 3
TEM dark-field images and the corresponding diffraction patterns of $T i_{49.2} N i_{50.8}$ cold rolled down to a thickness reduction of 27%: (a), $(a^{'})$ , and $(a^{''})$ at $T = 298 K > T_{g}$ ; (b), $(b^{'})$ , and $(b^{''})$ at $T = 243 K \sim T_{g}$ ; (c), $(c^{'})$ , and $(c^{''})$ at $T = 193 K < T_{g}$ ; (d), $(d^{'})$ , and $(d^{''})$ at $T = 96 K$ . The zone axis is ${[111]}_{B 2}$ .
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Figure 4
(a) Stress-strain curves at different temperatures, which were performed under tensile test with strain control. The curves of different temperature are shown horizontally for a better exhibition. (b) Temperature dependence of stress hysteresis. (c) Temperature dependence of elastic modulus obtained at different temperatures for $T i_{49.2} N i_{50.8}$ with $ɛ_{p} = 27 %$ . (d) 30 times tensile cycling test isothermally at room temperature for $T i_{49.2} N i_{50.8}$ with $ɛ_{p} = 27 %$ ; and (e) the evolution of maximum strain and residual strain under cycling test.
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Figure 5
Schematic drawings of microstructure evolution and the associated free energy curves at $ɛ_{p} = 0$ (a1)–(a3′) and at $ɛ_{p} = 27 %$ (b1)–(b3′) upon cooling and loading. (a1) and (a1′) Microstructure and free energy curve at high temperature (HT) where the austenite is stable. (a2) and (a2′) Microstructure and free energy curve at low temperature (LT) where the martensite (both variants M1 and M2) is stable. (a3) and (a3′) Microstructure and free energy curve under loading where a single martensitic variant (M2) is stable. (b1) and (b1′) Microstructure and free energy curve at high temperature (HT) with randomly distributed martensitic nanodomains (small volume fraction). (b2) and (b2′) Microstructure and free energy curve at low temperature (LT) with randomly distributed martensitic nanodomains (large volume fraction). (b3) and (b3′) Microstructure and free energy curve under loading with the external load favoring one of the martensitic variants. Free energy curves with different colors describe different local regions experiencing different stresses. The green and red arrows in (b1′) through (b3′) indicate an increase in the local stress.
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Physical Review Materials

Novel B19′ strain glass with large recoverable strain

Qianglong Liang, Dong Wang, Jian Zhang, Yuanchao Ji, Xiangdong Ding, Yu Wang, Xiaobing Ren, and Yunzhi Wang

Phys. Rev. Materials 1, 033608 – Published 22 August 2017

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