1.Jiangxi Key Laboratory of Advanced Copper and Tungsten Materials, Jiangxi Academy of Sciences, Nanchang 330096, China 2.College of New Energy and Materials, China University of Petroleum-Beijing, Changping 102249, China 3.X -ray Science Division, Argonne National Laboratory, Argonne, Illinois 60439, USA
Cite this article:
JIANG Jiang, HAO Shijie, JIANG Daqiang, GUO Fangmin, REN Yang, CUI Lishan. Quasi-Linear Superelasticity Deformation in an In Situ NiTi-Nb Composite. Acta Metall Sin, 2023, 59(11): 1419-1427.
In the past decade, a unique composite system consisting of Nb nanowire and NiTi shape memory alloy matrix has attracted considerable attention. One of the works published in Science proposed that the NiTi-Nb composite has superior properties, including high strength (1.65 GPa), low Young's modulus (25.8 GPa), and quasi-linear superelasticity (6.4%). In particular, given the quasi-linear superelasticity of this composite, (1) continuous stress-induced martensitic transformation occurred even at the beginning of tensile loading, which indicated that the external stress required to start the transformation was reduced to almost zero; (2) the transformation (stress-strain) curve is a “hardening type” rather than a “plateau type,” with apparent Young's modulus of 25.8 GPa, and (3) the amount of quasi-linear superelasticity deformation is 6.4%, which is higher than that of conventional binary NiTi alloy. This work focused on the quasi-linear superelasticity property. Thus, an in situ NiTi-Nb composite was prepared by vacuum induction melting, hot forging, and wire drawing. Microscopic analysis showed that Nb nanowires were distributed in parallel inside the nanocrystalline NiTi matrix along the wire axial direction. Quasi-linear superelasticity was obtained after 9% pre-deformation, with a yield stress of 1.7 GPa, apparent Young's modulus of 34 GPa, and quasi-linear superelasticity deformation of ~5.5%, which is similar to the result proposed in Science. In situ synchrotron XRD measurements were conducted to analyze the effect of pre-deformation on the coupling effect between NiTi and Nb nanowire. The origin and deformation mechanism of the quasi-linear superelasticity were systematically studied.Results revealed that coupling tensile stress in NiTi, which was generated by pre-deformation, increased gradually with the increase of the pre-deformation strain, thereby providing a driving force for stress-induced martensitic transformation. The external stress required to start the transformation could be reduced to almost zero in some local areas as a result of the coupling tensile stress. The initial velocity of transformation increased with the increase of the coupling tensile stress in NiTi. Therefore, a continuous transformation with relatively high velocity was obtained even at the beginning of tensile loading after a proper pre-deformation. Furthermore, the gradient distribution of coupling tensile stress inside B2-NiTi led to the “hardening-type” transformation (stress-strain) curve.
Fund: National Natural Science Foundation of China(51731010);National Natural Science Foundation of China(51861011);National Natural Science Foundation of China(51971243);National Natural Science Foundation of China(51971244);Major Science and Technology Research & Development Projects of Jiangxi Province(20212-AAE01003)
Corresponding Authors:
CUI Lishan, professor, Tel: (010)89731158, E-mail: lscui@cup.edu.cn
Fig.1 Pre-deformation process of the NiTi-Nb sample (a) and multiple-step cyclic stress-strain curves of a binary NiTi alloy (b)
Fig.2 TEM bright field image of the longitudinal section microstructure of the NiTi-Nb composite wire (a) and 2D high-energy XRD pattern of the wire (B2—B2-NiTi, Nb—bcc-Nb) (b)
Fig.3 Quasi-linear superelasticity stress-strain curves of the NiTi-Nb composite (a) typical macroscopic mechanical property of the NiTi-Nb composite after pre-deformation (Ea—apparent Young's modulus) (b) cyclic tensile stress-strain curves of the NiTi-Nb composite after pre-deformation
Fig.4 Multiple-step cyclic stress-strain curves of the NiTi-Nb composite sample, where the max strains of each cycle are 5.5%, 6.5%, 7.5%, 9.0%, 9.8%, and fracture strain in sequence
Fig.5 Evolutions of the diffraction peaks of Nb(220), B2-NiTi(211), and B19'-NiTi(001) planes in NiTi-Nb composite perpendicular to the loading direction during the multiple-step cyclic tensile test
Fig.6 Stress-strain curves of the as-annealed NiTi-Nb composite, and the corresponding B19'-NiTi(001) peak area curves in the 6 loading processes (In each loading process, the “first yield point” on the stress-strain curve just corresponds to the “turning point” on the evolution curve of B19' peak areas, as marked by each dash line)
Fig.7 Slopes of B19'-NiTi(001) peak area curves at the beginning and after the 1st yielding of each loading process, which can be seen as a measurement of the transformation velocity
Fig.8 Evolutions of the lattice strain for Nb(220) plane (a) and B2-NiTi(211) plane (b) perpendicular to the loading direction during the tensile process, which can be regarded as elastic strain vs total strain (elastic + plastic strain) relation of the embedded Nb nanowire and NiTi phase
Fig.9 State evolution diagrams of samples during the tensile loading after a pre-deformation (a) schematic of the pre-deformation process (NW—nanowire) (b) schematic of stress distribution inside the specimen after pre-deformation (σ—stress) (c) full width half maximum (FWHM) values and residual tensile lattice strains of B2-NiTi at the beginning of each loading process, where the increase of FWHM indicates that the stress distribution in B2-NiTi becomes more unequal, and the increase of residual tensile lattice strain indicates the increasing of coupling tensile stress in B2-NiTi (d) schematic of martensitic transformation process which starts near the NiTi/Nb interface and then gradually moves to the core of B2-NiTi when loading a pre-deformed specimen
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