Influence of C- and B-content on Solidification and High Temperature Stress Rupture Behavior of Nickel-based Superalloy K417G

doi:10.11901/1005.3093.2020.257

Chinese Journal of Materials Research

2021, Vol. 35

Issue (4): 241-250 DOI: 10.11901/1005.3093.2020.257

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Influence of C- and B-content on Solidification and High Temperature Stress Rupture Behavior of Nickel-based Superalloy K417G

SHU Delong¹, YAN Zhi², WANG Daohong³^,⁴, XIE Jun¹(

), HOU Guichen¹, Naicheng SHENG¹, LI Jinguo¹, YU Jinjiang¹, SUN Xiaofeng¹, ZHOU Yizhou¹

^1.Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
^2.Aecc Aero Science and Technology Co. Ltd. , Metrology Physicochemical Center, Chengdu 610503, China
^3.JiangSu Feiyue Machine & Pump Gruop Co. Ltd. , Jingjiang, 214536, China
^4.JiangSu Jinyan New Material Technology Co. Ltd. , Jingjiang, 214536, China

Cite this article:

SHU Delong, YAN Zhi, WANG Daohong, XIE Jun, HOU Guichen, Naicheng SHENG, LI Jinguo, YU Jinjiang, SUN Xiaofeng, ZHOU Yizhou. Influence of C- and B-content on Solidification and High Temperature Stress Rupture Behavior of Nickel-based Superalloy K417G. Chinese Journal of Materials Research, 2021, 35(4): 241-250.

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Abstract

The influence of C- and B-content on the solidification and high temperature stress rupture behavior of K417G nickel-based superalloy have been investigated by means of DTA analysis, optical microscope, scanning electron microscope, isothermal quenching and stress rupture tests at 950℃/235 MPa. Results show that the precipitation temperature and the amounts of the primary carbide are mainly affected by the C-content, which are both increased with the rise of C-content in the alloy. During stress rupture deformation at 950℃/235 MPa, the fracture mechanism of the alloy can be described as that cracks initiate on and then propagate along grain boundaries. Wherein, the MC-type carbides on the grain boundary could decompose into M₂₃C₆-type carbide enriched in Cr, which will reduce the stability of the boundary. Within the composition range of the tested alloys, raising the B-content could increase the grain boundary strength of the alloy during deformation at high temperature. As a result, the proper decrease C-content, while increase B-content can improve the high temperature stress rupture property of the alloy.

Key words: metallic materials nickel-based superalloy high temperature stress rupture property content of C content of B

Received: 28 June 2020

ZTFLH:

TG27

Fund: National Natural Science Foundation of China(51701212);National Science and Technology Major Project(J2019-VI-0018-0133);Natural Science Foundation of Liaoning Province(2019-MS-336);Key Regional Project of Science and Technology Service Network Program, Chinese Academy of Sciences(KFJ-STS-QYZX-079);2018 Taizhou High-level Innovation and Entrepreneurship Talent Introduction Plan Project, 2020 Youth Innovation Promotion Association Project, Chinese Academy of Sciences

About author: XIE Jun, Tel: (024)83978341, E-mail: junxie@imr.ac.cn

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	Articles by authors
	Delong SHU
	Zhi YAN
	Daohong WANG
	Jun XIE
	Guichen HOU
	SHENG Naicheng
	Jinguo LI
	Jinjiang YU
	Xiaofeng SUN
	Yizhou ZHOU

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https://www.cjmr.org/EN/10.11901/1005.3093.2020.257 OR https://www.cjmr.org/EN/Y2021/V35/I4/241

Table 1 Chemical composition of the alloy (mass fraction, %)

Fig.1 DTA heating curves of the K417G alloys with various C, B contents (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.2 DTA cooling curves of the K417G alloys with various C, B contents (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.3 Precipitation temperature changes of the phases in the K417G alloys with different C and B contents during solidification

Fig.4 Microstructures of the alloys with various C and B contents after isothermal quenching at 1310℃ (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.5 Microstructures of the K417G alloys with various C and B contents after isothermal quenching at 1290℃ (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.6 Microstructures of the alloys with various C and B contents after isothermal quenching at 1240℃ (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.7 Microstructures of the as-cast K417G alloys with various C and B contents (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.8 Stress rupture life of the K417G alloys with different C and B contents under the condition of 950℃/235 MPa

Fig.9 Macrostructures at the fracture of the K417G alloys with various C and B contents after stress rupture at 950℃/235 MPa (a) No.1; (b) No.2; (c) No.3; (d) No.4

Fig.10 Microstructures on the longitudinal section in No.2 alloy after stress rupture to fracture (a) morphology of the grain boundary far from the fracture; (b) morphology of the grain near the fracture; (c) morphology of the grain boundary near the fracture

Fig.11 Microstructures near the fracture (a) and the distributions of Cr and Ti near the crack (b, c) of No.2 alloy after stress rupture to fracture

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