Toughening of Nanostructured Metals

doi:10.11900/0412.1961.2022.00191

Acta Metall Sin

2022, Vol. 58

Issue (11): 1385-1398 DOI: 10.11900/0412.1961.2022.00191

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Toughening of Nanostructured Metals

ZHAO Yonghao(

), MAO Qingzhong

Nano and Heterogeneous Materials Center, School of Materials Science and Engineering, Nanjing Universityof Science and Technology, Nanjing 210094, China

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ZHAO Yonghao, MAO Qingzhong. Toughening of Nanostructured Metals. Acta Metall Sin, 2022, 58(11): 1385-1398.

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Abstract

Metallic structural materials have a wide range of industrial applications (including in the aviation, aerospace, navigation, military industry, nuclear power, chemical industry, construction, and bridge-building fields) due to their unique properties (such as heat resistance and high strength and toughness). At present, there are development opportunities for metallic structural materials, but these materials are also facing challenges due to the gradual substitution of carbon fiber composites and the increasing shortage of metal mineral resources. China's metallic structural material industry is facing development roadblocks and opportunities. Nanostructured metals and alloys have a wide range of potential industrial applications in the field of aviation, aerospace, navigation, military industry with requirements for energy conservation and weight reduction due to their high strength, but their low fracture elongation is a major limitation. The low ductility of nanostructured metals is caused by their low strain hardening rate; the strain hardening rate is caused by the difficulty of dislocation accumulation. This is because the small grain size limits dislocation propagation and reaction. After more than 20 years of research, the low ductility of nanostructured metals has been improved by tailoring the metal microstructures, such as by introducing nano-precipitation, twin boundaries, multi-scale grain distribution, twinning, or phase transformation, nano-gradient structure, and heterogeneous structure, or by lowering dislocation density, etc. These toughening schemes improve the dislocation accumulation capacity and strain hardening rate of nanostructured metals, and ultimately improve their toughness. The tensile properties of nanostructured metals are closely related to their microstructures and deformation temperature, strain rate, tensile sample size, and loading state.

Key words: nanostructured metal strength ductility strain hardening toughening

Received: 24 April 2022

ZTFLH:

TG113

Fund: National Key Research and Development Program of China(2021YFA1200203);National Natural Science Foundation of China(51971112);Fundamental Research Funds for the Central Universities(30919011405)

About author: ZHAO Yonghao, professor, Tel: (025)84315304, E-mail: yhzhao@njust.edu.cn

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Fig.1 Comparison of fracture toughness-strength of metallic, ceramic and organic polymer materials^[1] (PP—polypropylene, PE—polyethylene, PC—polycarbonate, PS—polystyrene, PET—poly(ethylene terephthalare), PTFE—poly tetra fluoroethylene)

Fig.2 Proportion of composite and metallic structural materials used in the U.S. Boeing 787 airliner

Fig.3 Relationship between metal strength and dislocation density

Fig.4 Schematic of tensile curves of ceramics, metals, and organic polymers and the relationship between static toughness and strength, fracture elongation, and work hardening rate (PMCs—polymer matrix composites; ε—strain, σ—stress)

Fig.5 Tensile curves of coarse-grained copper (CG Cu) and annealed nano/ultrafine-grained copper (Insets show the corresponding dislocation accumulation)^[48]

Fig.6 Dependence of the strengthening effect on the radii of precipitates

Fig.7 Tensile curves of CG solid solution, liquid nitrogen rolling (NS), and low-temperature aging (NS + P) 7075 aluminum alloys (a), dislocation accumulation near the precipitated phase after tension (b-d), and nano-precipitated phase before tension (e-g)^[56] (The inset shows dimension of the tensile sample with a thickness of 1 mm)

Fig.8 Tensile curves of equal channel angular pressing (ECAP) and subsequent liquid nitrogen drawing and rolling (ECAP + D + R) of ultrafine grained (UFG) copper (a), nano deformation twins introduced by liquid nitrogen deformation (b), and interaction of twin boundaries and dislocations (c)^[82] (Inset in Fig.8a shows dimension of tensile sample with a thickness of 0.1 mm, b—Burgers vector)

Fig.9 Microstructures (a, b) and tensile curves (c) of high-purity and dense bi/multi-modal nickel (Bi-Ni/multi-Ni) and review of yield strength-tensile ductility of nickel (d)^[87] (The twins in Figs.9a and b are indicated by black arrows; the inset in Fig.9c shows the picture of the fractured tensile specimens; ED—electro-deposition, HPT—high pressure torsion)

Fig.10 Tensile curves (a) and X-ray diffraction spectra (b) of ultrafine grained Fe-Mn alloy^[89]

Fig.11 Gradient nano-grained (GNG) structured copper prepared by surface mechanical grinding treatment^[95]
(a) schematic of the tensile bar sample of which the gauge section was processed by means of surface mechanical grinding treatment (SMGT)
(b, c) schematics of the cross-sectional microstructure of the gauge consisting of a gradient nano-grained layer (dark blue) and a deformed coarse grained layer (blue) on a coarse grained core (light blue)
(d) a typical cross-sectional SEM image of a SMGT Cu sample
(e) a cross-sectional bright-field TEM image of microstructures 3 mm below the treated surface (The arrow indicates the processing direction, and the inset shows the electron diffraction pattern)
(f) a transversal grain size distribution from TEM measurements in the top 5-mm-deep layer
(g) variation of average transversal grain (subgrain or cell) sizes along depth from the surface (Error bars represent the standard deviation of grain-size measurements)

Fig.12 Tensile engineering stress-strain (σ_e-ε_e) curves (a), strain hardening curves (b-d), and complex stress states (e, f) of nano-gradient stainless steel^[96] (GS—gradient-structured, NS—nanostructured; Θ—strain hardening rate, ε_T—true strain, σ_T—true stress, H—microhardness, ΔH—H increment; inset in Fig.12b shows transient response on the σ_T-ε_T curve of the GS-CG sample between two inflection points marked by "×" corresponding to the Θ-up-turn on its Θ-ε_T curve)

Fig.13 Effects of thickness (T) and length (L) of ultrafine grained Cu tensile samples on tensile curves and deformation mechanisms (W—width of gauge, PEEQ—equivalent plastic strain)^[109]

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