SECOND PHASE STRENGTHENING IN ADVANCED METAL MATERIALS

doi:10.11900/0412.1961.2016.00383

Acta Metall Sin

2016, Vol. 52

Issue (10): 1183-1198 DOI: 10.11900/0412.1961.2016.00383

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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.

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Abstract

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.

Key words: metal material second phase strengthening phase boundary mechanical property

Received: 26 August 2016

ZTFLH:

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)

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	Articles by authors
	Zhaoping LU
	Suihe JIANG
	Junyang HE
	Jie ZHOU
	Wenli SONG
	Yuan WU
	Hui WANG
	Xiongjun LIU

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https://www.ams.org.cn/EN/10.11900/0412.1961.2016.00383 OR https://www.ams.org.cn/EN/Y2016/V52/I10/1183

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 (Cu_0.5Zr_0.5)_100-_xAl_x alloys^[18]

Fig.13 Typical SEM image (a) and XRD spectra of the as-cast and fractured samples (b) of Zr₄₈Cu_47.5Al₄Co_0.5^[8]

Fig.14 Microhardnesses of the crystalline phase and amorphous matrix in the as-cast and tensioned samples of Zr₄₈Cu_47.5Al₄Co_0.5 bulk metallic glass (BMG) composite^[8]

Fig.15 Compressive stress-strain curve of the Ti_43.2Cu₃₈Ni₁₀Zr_7.8Al_0.5Si_0.5 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.16 DSC heating and cooling curves (a) and schematic time-temperature-transformation (TTT) diagram (b) of (Cu_0.5Zr_0.5)_100-_xAl_x (x=0, 4, 6, atomic fraction, %) alloy^[18] (M_s—martensitic transformation start temperature, A_s—autensite transformation start temperature, T_g—glass transition temperature, T_L—liquidus temperature)

Fig.17 HRTEM images of the B2 nanocrystals embedded in Zr₄₈Cu₄₈Al₄ (a) and Zr₄₈Cu_47.5Al₄Co_0.5 (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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