Research Progress of Wrought Superalloys in China

doi:10.11900/0412.1961.2019.00142

Acta Metall Sin

2019, Vol. 55

Issue (9): 1115-1132 DOI: 10.11900/0412.1961.2019.00142

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Research Progress of Wrought Superalloys in China

DU Jinhui¹,LV Xudong^1,²(

),DONG Jianxin³,SUN Wenru⁴,BI Zhongnan^1,²,ZHAO Guangpu¹,DENG Qun¹,CUI Chuanyong⁴,MA Huiping¹,ZHANG Beijiang¹

1. High-Temperature Materials Institute, Central Iron and Steel Research Institute, Beijing 100081, China
2. Beijing Key Laboratory of Advanced High Temperature Materials, Central Iron and Steel Research Institute, Beijing 100081, China
3. School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing 100083, China
4. Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Cite this article:

DU Jinhui,LV Xudong,DONG Jianxin,SUN Wenru,BI Zhongnan,ZHAO Guangpu,DENG Qun,CUI Chuanyong,MA Huiping,ZHANG Beijiang. Research Progress of Wrought Superalloys in China. Acta Metall Sin, 2019, 55(9): 1115-1132.

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Abstract

Wrought superalloys are high temperature alloys produced by casting-forging-hot rolling-cold drawing, including disc, plate, bar, wire, tape, pipe etc. These products are widely used in aviation, aerospace, energy, petrochemical, nuclear power and other industrial fields. In this paper, domestic progress of wrought superalloys in recent ten years was reviewed, including advances in fabrication process, research in new alloys (GH4169G, GH4169D, GH4065 and GH4068 alloy et al.) and new techniques (deforming of FGH4096 alloy, nitriding of NGH5011 alloy and 3D printing of In718 alloy et al.).

Key words: wrought superalloy melting forging inspection 3D printing

Received: 05 May 2019

ZTFLH:

TG132.2

Fund: Supported by National Basic Research Program of China(2010CB631203);China Postdoctoral Science Foundation(2005037323)

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	Jinhui DU
	Xudong LV
	Jianxin DONG
	Wenru SUN
	Zhongnan BI
	Guangpu ZHAO
	Qun DENG
	Chuanyong CUI
	Huiping MA
	Beijiang ZHANG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2019.00142 OR https://www.ams.org.cn/EN/Y2019/V55/I9/1115

Fig.1 Comparisons before and after optimization of vacuum induction melting launder(a) removal ability of inclusions in square flow slots designed by steel works(b) removal ability of inclusions in self-designed square flume(c) residence time distribution (RTD) curves of square flume design in steel works(d) RTD curves of self-designed square flume

Fig.2 Schematic diagram of heat transfer in vacuum arc remelting

Fig.3 Distributions of primary dendrite arm spacing (PDAS) (a) and secondary dendrite arm spacing (SDAS) (b) of ingots (longitudinal section)

Table 1 Comparisons of the SDAS and Ti element segregation coefficient (K) of different ingot center longitudinal section

Fig.4 Longitudinal section microstructures of centers of GH4720Li ingots(a1~a3) diameter 406 mm ingot (b1~b3) diameter 508 mm ingot

Table 2 Comparisons of K for Ti element after different homogenization schedules

Fig.5 Simulation of cogging of GH4720Li alloy

Fig.6 Simulation of radial forging of GH4720Li alloy

Fig.7 Photo of the supersize GH4706 alloy turbine disc with a diameter 2100 mm

Fig.8 Measurement penetration vs spatial resolution for various residual stress measurement methods^[31]

Fig.9 Relationship between γ" variant selection and grain orientation after thermo-mechanical coupling experiment in GH4169 alloy^[33](a) EBSD figure of grain orientation (b) [001] grain orientation (c) [111] grain orientation (d) [101] grain orientation

Fig.10 C-scan images of the turbine disk(a) C-scan of clutter distribution (b) time of flight (TOF) of clutter distribution (c) C-scan of bottom echo distribution

Table 3 Comparisons of local ultrasonic clutter and bottom echo loss of different heat treatment temperature samples^[37,38,39]

Fig.11 The microstructures of GH4169D (a) and GH4169 (b) alloys after standard heat treatment^[42]

Table 4 Chemical compositions of high performance disc superalloys^{[46,47,48,49,50,51,52]} (mass fraction / %)

Fig.12 TEM image of an aged reinforced cobalt-based alloy annealed at 900 ℃ for 72 h^[60](a) dark field image(b) selected area electron diffraction pattern

Fig.13 Chemical composite design of GH4068 alloy^[59]

Fig.14 Deformation mechanism of GH4068 alloy under different creep conditions^[65]

Fig.15 Deformation microstructures of GH4068 alloy at intermediate temperature creep^[65](a) 725 ℃, 480 MPa (b) 725 ℃, 630 MPa

Fig.16 Central macrostructure of low-magnification in electroslag remelting continuous directional solidification ingots (diameter 270 mm) of FGH4096 alloy^[68]

Fig.17 Microstructures at R/2 region in directional solidification ingots of FGH4096 alloy (R—radius of ingot)^[68](a) primary dendrite (b) secondary dendrite

Fig.18 Longitudinal section microstructures of isothermal forging turbine discs of FGH4096 alloy (diameter 630 mm)^[68]

Table 5 Comparisons of mechanical properties of various alloys^[60]

Fig.19 Gas turbine discs (diameter 150 mm) (a) and integral blade rings (diameter 220 mm) (b) fabricated by additive manufacturing of In718 alloy

Table 6 Mechanical properties of gas turbine discs fabricated by additive manufacturing of In718 alloy

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