Supplementary Information
A biopolymer-like metal enabled hybridmaterial with exceptionalmechanical prowess
Junsong Zhang1, Lishan Cui1*, Daqiang Jiang1, Yinong Liu2*, Shijie Hao1, Yang Ren3, Xiaodong Han4, Zhenyang Liu1, Yunzhi Wang5,6, Cun Yu1, Yong Huan7, Xinqing Zhao8, Yanjun Zheng1, Huibin Xu8, Xiaobing Ren5Xiaodong Li9*
1State Key Laboratory of Heavy Oil Processing and Department of Materials Science and Engineering,ChinaUniversity of Petroleum, Beijing 102249, China
2School of Mechanical and Chemical Engineering, The University of Western Australia, Crawley, WA 6009, Australia
3X-ray Science Division, Argonne National Laboratory, Argonne, Illinois60439, USA
4Institute of Microstructure and Properties of Advanced Materials, BeijingUniversity of Technology, Beijing 100124, China
5State Key Laboratory for Mechanical Behavior of Materials and Frontier Institute of Science and Technology, Xi’an Jiaotong University, Xi’an 710049, China
6Department of Materials Science and Engineering,The OhioStateUniversity,Columbus, OH43210, USA
7State Key Laboratory of Nonlinear Mechanics (LNM), Institute of Mechanics, ChineseAcademy of Sciences, Beijing 100190, China
8School of Materials Science and Engineering, BeihangUniversity, Beijing 100191, China
9Department of Mechanical & Aerospace Engineering, University of Virginia, Charlottesville, Virginia22904-4746, USA
Correspondence and requests for materials should be addressed to L.C. () or Y.L. () or X.L. ()
Figure 1. Schematic illustration of the stress-induced martensitic transformation in shape memory alloys.
Figure 2.Microstructure of the TiNi-Ti3Sn compositeprepared bydirectional solidification. (a)Macroscopic ingot of the composite. (b)and (c) Scanning electron microscopy backscattered electron images of longitudinal (parallel to the drawing direction) section of the sample and transverse (perpendicular to the drawing direction) section of the sample, respectively. The inset shows the Ti3Sn (light)- TiNi (dark) lamellar structure at a higher magnification. (d)One-dimensional high-energy X-ray diffraction (HE-XRD) pattern of thecomposite. The inset showsits corresponding two-dimensional HE-XRD pattern.
Figure 3.Schematic illustration of the experimental set-up for in situ high-energy synchrotron X-ray diffraction measurementduring compression testing.
Figure 4. Lattice strain evolutions asafunction of the applied macroscopic strain in the loading direction for Ti3Sn and TiNi in the composite prepared by directional solidification.
Figure 5. Synchrotron HE-XRD analysis of the detwinning process of TiNi in the composite. The upper figures ((a) and (b)) show two sections of the diffraction pattern, which reveal the B19′-TiNi (111), B19′-TiNi (020) and B19′-TiNi (001) peaks and their evolution during compression.(a)Longitudinaldirection(parallel to the loading direction).(b)Transversedirection(perpendicular to the loading direction). The lower figures ((c) and (d)) show the evolutions of the relative peak intensities upon loading as a function of the applied strain for the TiNi-Ti3Sncomposite.(c)Longitudinal direction(parallel to the loading direction). (d)Transversedirection(perpendicular to the loading direction).
Note:Fig. 5 shows the diffraction patterns of the composite during compressive loading in the direction parallel (longitudinal;Fig. 5a) and perpendicular (transverse;Fig. 5b) to the compression axis, which reveal the B19′-TiNi (111), B19′-TiNi (020), and B19′-TiNi (001) diffraction peaks. TiNi martensite detwinning occurs in the initial stage of deformation (low applied strains), as evidenced by the decrease in diffraction intensity of the (020) and (001) planes and the concomitant increase inthe diffraction intensity of the (111) planes in the loading direction (Fig. 5a). In the transverse direction (Fig. 5b), the opposite behavior is observed, with the exception of the (020) plane. To describe the volume fraction evolution of the martensite variants detwinned, the relative peak intensities, which are defined as Ihkl/I where I is the peak intensity at zero load, are determined from the diffraction patterns. Figs. 5c and 5d show the relative peak intensities upon loading as functions of the applied strain in the longitudinal direction and transverse direction, respectively. In the longitudinal direction (Fig. 5c), the relative peak intensities of (100) and (111) increased, whereasthe relative peak intensities of (11), (020), (011), and (001) decreased. In the transverse direction (Fig. 5d), the opposite behavior is observed, with the exception of(11) and (020). This implies that detwinning occurred such that martensitic variants with (100) and (111) planes perpendicular to the loading direction grew at the expense of variants with (11), (020), (011), and (001) planes perpendicular to the loading direction. The increases in the integrated intensities, which are taken as an indicator of the volume fractions, of variants with the (100) and (111) planes areapproximately 95% and 50% respectively in the loading direction, whereas the decreases of the volume fraction of variants with (100) and (111) planes are about 50% and 18%, respectively, in the direction perpendicular to the loading direction.
Figure 6. Compressive stress–straincurve of thecomposite prepared by directional solidification.
Figure 7.Damping capacity (indexed by tanδ) of the compositeasa function of temperature during the heating process.
Figure 8. Ultrasonic signal attenuation spectra.(a)TiNi-Ti3Sn composite. (b) 1045 carbon steel.