Supplementary Information
A biopolymer-like metal enabled hybrid material with
exceptional mechanical 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 Ren5 & Xiaodong Li9*
1State
Key Laboratory of Heavy Oil Processing and Department of Materials Science and
Engineering, China University 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, Illinois 60439, USA
4Institute
of Microstructure and Properties of Advanced Materials, Beijing University 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 Ohio State University, Columbus, OH
43210, USA
7State
Key Laboratory of Nonlinear Mechanics (LNM), Institute of Mechanics, Chinese Academy
of Sciences, Beijing 100190, China
8School
of Materials Science and Engineering, Beihang University, Beijing 100191, China
9Department
of Mechanical & Aerospace Engineering, University of Virginia, Charlottesville,
Virginia 22904-4746, USA
Correspondence and requests for materials should be addressed to L.C. (lscui@cup.edu.cn) or Y.L.
(yinong.liu@uwa.edu.au) or X.L. (xl3p@virginia.edu)
Figure 1. Schematic illustration of the stress-induced martensitic transformation in
shape memory alloys.
Figure 2. Microstructure of the TiNi-Ti3Sn composite prepared by directional
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 the composite. The inset shows its corresponding
two-dimensional HE-XRD pattern.
Figure 3. Schematic illustration of the experimental set-up for in situ high-energy
synchrotron X-ray diffraction measurement during compression testing.
Figure 4. Lattice strain evolutions as a function 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) Longitudinal direction (parallel to the
loading direction). (b) Transverse direction (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-Ti3Sn composite. (c)
Longitudinal direction (parallel to the loading direction). (d) Transverse direction
(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 in the 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, whereas
the relative peak intensities of ( 1 11), (020), (011), and (001) decreased. In the
transverse direction (Fig. 5d), the opposite behavior is observed, with the exception of
( 1 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 ( 1 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 are approximately
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–strain curve of the composite prepared by directional
solidification.
Figure 7. Damping capacity (indexed by tanδ) of the composite as a function of
temperature during the heating process.
Figure 8. Ultrasonic signal attenuation spectra. (a) TiNi-Ti3Sn composite. (b) 1045
carbon steel.