Progress in High Performance Nanocomposites Based ona Strategy of Strain Matching

doi:10.11900/0412.1961.2018.00457

Acta Metall Sin

2019, Vol. 55

Issue (1): 45-58 DOI: 10.11900/0412.1961.2018.00457

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Progress in High Performance Nanocomposites Based ona Strategy of Strain Matching

Lishan CUI(

), Daqiang JIANG

College of Science, China University of Petroleum-Beijing, Beijing 102200, China

Cite this article:

Lishan CUI, Daqiang JIANG. Progress in High Performance Nanocomposites Based ona Strategy of Strain Matching. Acta Metall Sin, 2019, 55(1): 45-58.

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Abstract

Freestanding nanowires have ultrahigh elastic strain limits (4%~7%) and yield strengths, it is expected that composites reinforced by nanowires will have exceptional mechanical properties. However, the results obtained so far have been disappointing, primarily because the intrinsic mechanical properties of nanowires have not been successfully exploited in bulk composites. This is thought to be due to the inelastic strain incompatibilities at typical dislocation-piled-up interfaces. Therefore, we proposed a concept of elastic and transformation strain matching to realize the intrinsic mechanical properties of the nanowires. By creating a nanostructured composite consisting of nano Nb embedded in a NiTi matrix, the intrinsic mechanical properties of Nb nanowires, nano ribbons and nano particles are realized. Besides, this breakthrough triggers a new mechanism of stress coupling that induces the nanocomposite showing excellent mechanical properties. Based on the design strategy, we developed an in situ composite that possesses a large quasi-linear elastic strain of over 6%, a low Young's modulus of less than 28 GPa, and a high yield strength of 1.65 GPa.

Key words: strain matching martensitic transformation shape memory alloy nanocomposite

Received: 28 September 2018

ZTFLH:

TG139

Fund: Supported by National Natural Science Foundation of China (No.51231008)

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00457 OR https://www.ams.org.cn/EN/Y2019/V55/I1/45

Fig.1 Two-dimension lattice schematic of the strain match between the nanowire and the dislocation slip matrix(a) matrix before dislocation slip(b) formed Burgers step (red line) after dislocation slip(c) atomic-scale high stress concentration (dotted circle) was generated when the dislocation moves to the interface between the nanowire and the matrix(d) schematic of the strain (ε) distribution when the dislocation slips to the interface, which shows the inelastic shear strain of matrix (

ε disl matrix

) approaches 100% around dislocation and elastic strain of matrix (

ε el matrix

) of about 0.2% away the dislocation

Fig.2 Two-dimension lattice schematic of the strain match between the nanowire and the lattice shear matrix(a) matrix before lattice shear(b) matrix after lattice shear(c) interface between the nanowire and the matrix after lattice shear, showing no atomic-scale high stress concentration(d) schematic of the strain distribution when the matrix experiences the stress induced martensitic transformation, which shows the elastic strain of matrix (

ε P matrix

) of about 1% around parent and shear strain of matrix (

ε M matrix

) approaches 7% around martensite. This 7% strain matches the elastic strain of the nanowire (

ε el nanowire

) of about 6% (red line)

Fig.3 The macro and micro images of the nanowire Nb/NiTi composite^[12]
(a) a coil of composite wire with a diameter of 0.5 mm
(b) scanning TEM image of the cross section of composite wire (bright regions, cross sections of Nb nanowires; dark regions, NiTi matrix)
(c) TEM image of a longitudinal section of composite wire (NW indicates nanowire)
(d) macroscopic appearance of a bundle of freestanding Nb nanowires
(e, f) SEM images of the freestanding Nb nanowires

Fig.4 The high energy synchrotron XRD of the nanowire Nb/NiTi sample during tensile test and the evolution of the lattice strain with respect to the applied strain of Nb nanowire^[12](a) the diffraction peak of the Nb (220) plane perpendicular to the loading direction shifts obviously when the NiTi showing the stress induced martensitic transformation (SIMT—stress-induced martensitic transformation)(b) the diffraction peak of the Nb (220) plane perpendicular to the loading direction shifts slightly when the NiTi showing plastic deformation(c) evolution of the lattice strain with respect to the applied strain for Nb (220) planes

Fig.5 Comparison of the elastic strain limits of Nb nanowires embedded in the matrix deforming by dislocation slip (1), Nb nanowires embedded in the matrix deforming by SIMT (2), and some freestanding nanowires (3)^[12]

Fig.6 Tensile stress-strain curves of the nanowire in situ composite with shape memory alloy (NICSMA) composite (ε_e—elastic limit, σ_s—yield strength, E—elastic modulus) (a), comparison of strengths and elastic strains of ceramics, metals, polymers and our composite (marked by NICSMA) (b), comparison of the yield strengths and elastic strain limits of different materials (c), comparison of the yield strengths and Young's moduli of different materials (d)^[12]

Fig.7 The cyclic tensile stress-strain curve of the nanowire in situ composite with shape memory alloy sample (a), evolution of the diffraction peaks for Nb (220), B2-NiTi (211) and B19'-NiTi (001) planes perpendicular to the loading direction during loading (b), evolution of the lattice strain with respect to the applied strain for Nb (220) plane perpendicular to the loading direction during the first cycle (c), evolution of the lattice strain with respect to the applied strain for Nb (220) plane perpendicular to the loading direction during the second cycle (d)^[13]

Fig.8 TEM analyses of two NiTi shape memory alloy composites with 10% and 20% volume fraction Nb nanowire^[14]
(a, b) SAED patterns of longitudinal view of the two samples(c, d) TEM bright field images of the two samples corresponding to Figs.8a and b(e, f) HAADF images of the two sample(g, h) HRTEM image revealing the interfaces between a Nb nanowire and NiTi matrix

Fig.9 TEM study of lattice strain matching between Nb nanowires and the NiTi matrix^[15]
(a) bright feld image of a microbeam fabricated by means of focus ion beam milling(b) enlarged view of a Nb nanowire in the beam(c) HRTEM image of the region marked as c in Fig.9b(d) TEM image of the microbeam upon loading to about 3.23% strain(e) enlarged TEM image of the region marked as e in Fig.9d, showing the three martensite plates (marked as M1, M2 and M3) nucleated in the NiTi matrix(f~h) HRTEM images of the regions marked as f, g and h in Fig.9e(i~l) filtered HRTEM images of the regions marked as i in Fig.9c and as j~l in Figs.9f~h

Fig.10 HRTEM image of the region covering martensite plates M1 and M3. The interplanar spacing variation was calculated at an interval of seven (110)Nb planes (a) and distribution of the lattice strain as a function of distance from the start plane (b)^[15]

Fig.11 STEM images of a cross-section (a) and a longitudinal-section (b) of a ribbion Nb/NiTi composite, evolution of the d-spacing strain with respect to the applied macroscopic strain for the Nb (220) plane perpendicular to the loading direction (Inset shows the stress-strain curve of the sample at room temperature) (c)^[12]

Fig.12 Evolution of d-spacing strain with respect to applied strain for the Nb (110) plane perpendicular to the wire axial direction during tensile loading (Inset is the macroscopic stress-strain curve of the NICSMA composite) (a), evolution of X-ray diffraction intensity of B19′-NiTi <001> planes versus the azimuth angle during tensile loading (b), TEM micrographs of twin morphologies of the martensitic NiTi matrix before and after a tensile deformation cycle to 8.7% (c), comparison of the elastic strain limits of Nb nanowires embedded in the matrix deforming by dislocation slip (1), Nb nanowires embedded in the matrix deforming by detwinning (2), and some freestanding nanowires (3) (d)^[16]

Fig.13 The d-spacing strain with respect to applied macroscopic strain for the Nb (110) planes perpendicular to the loading direction in the NiTi-Nb composite (a), comparison of tensile stress-strain curves of the composite wire (red curve) and a commercial superelastic NiTi wire (yellow curve) (b)^[17]

Fig.14 The tensile cyclic stress-strain curves of the nanostructured Nb reinforced NiTi shape memory alloy composite wire (strain: 4% and 5%); the tensile cyclic stress-strain curve of a commercial superelastic NiTi shape memory alloy wire^[18]

Fig.15 Typical microstructure of the TiNi-Ti₃Sn composite^[19]
(a) SEM backscattered electron images of the composite. The inset shows the Ti₃Sn (light)-TiNi (dark) lamellar structure at high magnification
(b) TEM bright-field image of the composite. The inset shows the button ingot of the composite
(c) HRTEM image of the interface between TiNi and Ti₃Sn
(d, e) display selected-area electron diffraction patterns of the Ti₃Sn and TiNi lamellae, respectively, shown in Fig.15b
(f) one-dimensional high-energy X-ray diffraction (HE-XRD) pattern of the composite. The inset contains its corresponding two-dimensional HE-XRD pattern

Fig.16 Deformation behavior of the TiNi-Ti₃Sn composite^[19]
(a) the lattice strain evolutions of B19'-TiNi (022) and Ti₃Sn (201) planes perpendicular to the loading direction as a function of the applied macroscopic strain. The inset shows an enlarged view of the lattice strain curve of the TiNi in the initial stages of deformation
(b) the comparison of the elastic strains of Ti₃Sn achieved in our composite with different reinforcements (such as nanowires, laminates, and particles) embedded in conventional metal matrices, which are deformed by dislocation slip

Fig.17 Room-temperature compressive stress-strain curve of the composite (a), comparison of the mechanical properties of our composite with those of other high-performance metal-based lamellar composites in which the soft component is a conventional metal (without the "J-curve" deformation attributes) rather than the biopolymer-like metal ("J-curve" deformation attributes) (b)^[19]

Fig.18 Two-way actuated properties of the composite wire^[20]
(a) output strain-temperature curve of the composite without external load
(b) evolution of d-spacing strain with respect to temperature for the Nb (110) plane perpendicular to the wire axial direction

Fig.19 Evolution of high-energy X-ray diffraction peaks for Nb (110) and B19′-NiTi (001) planes through the multiple-step tensile cycles (a), evolution of d-spacing strain with respect to applied strain for the Nb (110) plane perpendicular to the wire axial direction during the multiple-step tensile cycles (b), comparison of the retained tensile and compressive elastic strains of large quantity Nb nanowires in the composite without external load and those of the reported thin films on substrates and embedded nanoinclusions in films (c)^[16]

Fig.20 Polarization curves of the oxygen reduction reaction (ORR) of 10 and 5 nm Pt nanofilm under different strain states at a scan rate of 0.3 V/s. The data of 10 nm Pt nanofilm are shown with standard deviation^[28]

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