Research Progress on Controlled Solidificationand Its Applications

doi:10.11900/0412.1961.2017.00541

Acta Metall Sin

2018, Vol. 54

Issue (5): 669-681 DOI: 10.11900/0412.1961.2017.00541

Special Issue for the Solidification of Metallic Materials

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Research Progress on Controlled Solidificationand Its Applications

Guang CHEN¹(

), Gong ZHENG¹, Zhixiang QI¹, Jinpeng ZHANG¹, Pei LI¹, Jialin CHENG², Zhongwu ZHANG³

1 Engineering Research Center of Materials Behavior and Design, Ministry of Education, MIIT Key Laboratory of Advanced Metallic and Intermetallic Materials Technology,Nanjing University of Science and Technology, Nanjing 210094, China
2 School of Materials Engineering, Nanjing Institute of Technology, Nanjing 211167, China
3 Key Laboratory of Superlight Materials and Surface Technology, Ministry of Education, Harbin Engineering University, Harbin 150001, China

Cite this article:

Guang CHEN, Gong ZHENG, Zhixiang QI, Jinpeng ZHANG, Pei LI, Jialin CHENG, Zhongwu ZHANG. Research Progress on Controlled Solidificationand Its Applications. Acta Metall Sin, 2018, 54(5): 669-681.

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Abstract

This paper reviews the study of our group on controlled solidification and its applications in recent 20 years, including melt heat treatment before solidification, semi-solid processing between liquidus and solidus, rapid progressive solidification of nonequilibrium materials, semi-solid progressive solidification, and directional heat treatment in solid phase transformation. Furthermore, a new technique of material preparation is proposed with the combination of directional solidification and directional heat treatment. In addition, an outlook of controlled solidification technology and its applications are provided.

Key words: controlled solidification melt heat treatment semi-solid progressive solidification directional solidification directional heat treatment

Received: 20 December 2017

ZTFLH:

TG244

Fund: Supported by National Natural Science Foundation of China (Nos.51731006, 51771093 and 51571117), China Postdoctoral Science Foundation (No.2017M620212) and National Postdoctoral Program for Innovative Talents (No.BX201700120)

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	Guang CHEN
	Gong ZHENG
	Zhixiang QI
	Jinpeng ZHANG
	Pei LI
	Jialin CHENG
	Zhongwu ZHANG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2017.00541 OR https://www.ams.org.cn/EN/Y2018/V54/I5/669

Fig.1 Influences of melt superheat temperature on interface morphology of Ni-based superalloy in directional solidification^[17]
(a) 1400 ℃ (b) 1500 ℃ (c) 1600 ℃ (d) 1700 ℃

Fig.2 Macrostructures of Ti-48Al-2Cr-2Nb alloys after different cycles of cyclic melt heat treatment^[23]
(a) 0 cyc (b) 10 cyc (c) 15 cyc (d) 20 cyc

Fig.3 Microstructure (a) and room temperature compressive stress-strain curves (b) of bulk metallic glasses (BMG) composites synthesised by semi-solid processing^[24] (Vit.1 monolithic BMG; S1 (Zr56.2Ti13.8- Nb5.0Cu6.9Ni5.6Be12) with spherical crystalline; S2 (Zr60Ti14.7Nb5.3Cu5.6Ni4.4Be10) with spherical crystalline)

Fig.4 Microstructures of the Zr-BMG composites held at 850 ℃^[30]
(a) 0 min (b) 1 min (c) 3 min (d) 5 min (e) 10 min (f) 20 min (g) 40 min (h) 200 min

Fig.5 Average equivalent diameter D_eq, average shape factor SF (a) and inverse specific surface area S_v^-1 (b) of precipitated β-Zr phase as a function of the holding time^[30]

Fig.6 Microstructures of the Mg-BMG composites prepared by different method^[32]
(a, b) copper mold casting (c, d) rapid progressive solidification

Fig.7 Microstructures (a~e) and compressive stress-strain curves (f) of Zr-BMG composites prepared by rapid progressive solidification at different withdrawal velocities of 8 mm/s (a), 4 mm/s (b), 2 mm/s (c), 1 mm/s (d) and 0.46 mm/s (e)^[34]

Fig.8 W_f/Zr-BMG composites prepared by infiltration casting (a) and rapid progressive solidification (b)

Fig.9 Appearance (a) and OM images take from the surface (b) and center (c) for the Zr-BMG composites prepared by semi-solid progressive solidification (SSPS)^[34,35]

Fig.10 Engineering tensile stress-strain curve of the Zr-BMG composites prepared by SSPS (Inset show the samples after tension)^[35]

Fig.11 Typical microstructures of iron directionally annealed at 900 ℃ with various withdrawing velocities (The direction of columnar grain growth is from left to right)^[77]
(a) 0.5 μm/s (b) 0.8 μm/s (c) 3 μm/s (d) 8 μm/s (e) 15 μm/s (f) 30 μm/s

Fig.12 Relationship between lamellar and crystal orientation for primary β phase TiAl alloy (a) and primary α phase TiAl alloy (b)^[87]

Fig.13 Illustration of fully lamellar TiAl alloy with parallel orientation
(a) single crystal (b) bi-crystals (c) poly-crystals

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