SECOND PHASE STRENGTHENING IN ADVANCED METAL MATERIALS
Zhaoping LU(),Suihe JIANG,Junyang HE,Jie ZHOU,Wenli SONG,Yuan WU,Hui WANG,Xiongjun LIU
State Key Laboratory for Advanced Metals and Materials, University of Science and Technology Beijing, Beijing 100083, China
Cite this article:
Zhaoping LU, Suihe JIANG, Junyang HE, Jie ZHOU, Wenli SONG, Yuan WU, Hui WANG, Xiongjun LIU. SECOND PHASE STRENGTHENING IN ADVANCED METAL MATERIALS. Acta Metall Sin, 2016, 52(10): 1183-1198.
Second phase strengthening is a conventional, yet effective hardening methods for metallic materials. However, the resultant improvements on strength always associated by dramatic decreases in toughness. In this paper, the recent research work on applications of such mechanism into several typical advanced metallic materials including high-performance steels, high-entropy alloys and bulk metallic glasses were summarized. It was found that the characteristics of precipitates, i.e., sizes, volume fractions, morphology, etc., could be manipulated by controlling the interface features and mechanical mismatch of the precipitates and matrix, which eventually give rise to much enhanced mechanical performance.
Fund: Supported by National Natural Science Foundation of China (Nos.51531001, 51422101, 51271212 and 51371003), Program of Introducing Talents of Discipline to University of China (No.B07003), International Science & Technology Cooperation Program of China (No.2015DFG52600), Program for Changjiang Scholars and Innovative Research Team in University (No.IRT_14R05), Top-Notch Young Talents Program, Program for New Century Excellent Talents in University (No.NCET-13-0663) and Fundamental Research Fund for the Central Universities (No.FRF-TP-15-004C1)
Fig.1 Effects of Al and Mo additions on the formation of low-temperature precipitates (a) and the lattice parameter (b) of the newly developed maraging steels[14]
Fig.2 Ageing behavior at different temperatures (a) and stress-strain curves of the solution-treated and the peak-aged Ni(Fe, Al)-maraging steels (UE—uniform elongation) (b)[14] (Inset in Fig.2b shows the change in elongation and yield strength of traditional maraging steels caused by ageing process[33])
Fig.3 TEM images of Ni(Fe, Al)-maraging steels before (a) and after (b) the peak aged condition, and 3D atom map of precipitates (c)[14] (Inset in Fig.3b show corresponding SAED pattern)
Fig.4 Dislocation configuration after the peak ageing (a), the elemental segregation of the solutes (b) and Ni(Fe, Al) particles of Ni(Fe, Al)-maraging steels on/around the dislocation (c)[14]
Fig.5 TEM image of the (FeCoNiCr)97Ti3 (TA30) high entropy alloy (HEA) aged at 700 ℃ for 80 h
Fig.6 SEM images of the aged HEAs TA39 (a) and TA14 (b)
Fig.7 SEM images of the aged HEAs TA15 (a), TA33 (b) and TA24 (c)
Fig.8 Tensile properties of the HEAs with Ti and Al additions[16]
Fig.9 Characterization of the precipitates of the HEAs with Ti and Al additions[16]
Fig.10 Precipitation behaviors in TA24 HEA aged at 700 ℃ (a), 800 ℃ (b) and 900 ℃ (c) for 18 h
Fig.11 Precipitation behaviors in TA24 HEA aged at 800 ℃ for 1 h (a), 8 h (b) and 48 h (c)
Fig.12 Microstructure dependence on the Al content in (Cu0.5Zr0.5)100-xAlx alloys[18]
Fig.13 Typical SEM image (a) and XRD spectra of the as-cast and fractured samples (b) of Zr48Cu47.5Al4Co0.5[8]
Fig.14 Microhardnesses of the crystalline phase and amorphous matrix in the as-cast and tensioned samples of Zr48Cu47.5Al4Co0.5 bulk metallic glass (BMG) composite[8]
Fig.15 Compressive stress-strain curve of the Ti43.2Cu38Ni10Zr7.8Al0.5Si0.5 BMG composite (Inset shows the true stress-strain curve) (a), SEM image of the lateral surface (b), enlarged view of Fig.15b (c), and fractured surface of the current BMG composite (d)[21]
Fig.17 HRTEM images of the B2 nanocrystals embedded in Zr48Cu48Al4 (a) and Zr48Cu47.5Al4Co0.5 (b) BMG composites, enlargement of a nanocrystal in Fig.19a (c) and Fig.19b (d)[20] (Insets are the SAED patterns corresponding to the square areas, TB—twin boundary, SF—stacking fault)
Fig.18 Schematic illustration of the concept for developing large-sized high-performance BMG composites with a homogeneous dispersion of transformable austenitic phase via heterogeneous nucleation[25]
Fig.19 Atomic-resolution HAADF-STEM image of the interface between B2-CuZr and Zr5Sn3 (a) and the atomic model of B2-CuZr/Zr5Sn3 interface (b)[25]
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