Effect ofγ'-phase on Tensile and Stress Rupture Deformation Behavior of High W-containing Ni-based Superalloys

doi:10.11901/1005.3093.2022.261

Chinese Journal of Materials Research

2023, Vol. 37

Issue (1): 29-38 DOI: 10.11901/1005.3093.2022.261

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Effect ofγ'-phase on Tensile and Stress Rupture Deformation Behavior of High W-containing Ni-based Superalloys

WEI Lin¹, ZHOU Sigeng², Naicheng SHENG²(

), YU Jinjiang², HOU Guichen², WANG Biao¹, QUAN Jia¹, ZHOU Yizhou², SUN Xiaofeng², KANG Yong¹

^1.AECC Sichuan Gas Turbine Research Establishment, Chengdu 610500, China
^2.Shi -changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Cite this article:

WEI Lin, ZHOU Sigeng, Naicheng SHENG, YU Jinjiang, HOU Guichen, WANG Biao, QUAN Jia, ZHOU Yizhou, SUN Xiaofeng, KANG Yong. Effect ofγ'-phase on Tensile and Stress Rupture Deformation Behavior of High W-containing Ni-based Superalloys. Chinese Journal of Materials Research, 2023, 37(1): 29-38.

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Abstract

Ni-based superalloys with high W content are widely used to fabricate gas turbine blades because of their high temperature mechanical properties and lower cost. The γ΄-phase is the most important strengthening phase in Ni-based superalloys, which affects the deformation behavior during tensile process. Although the influence of γ΄-phase has been studied extensively, there are few investigations on the deformation mechanism of K416B superalloy with different morphologies of γ΄-phase. Hence, the effect of γ΄-phase morphology on the mechanical behavior of K416B superalloy was assessed in the present work. The average size of γ΄-phase scattered in the as-cast alloy was about 200 nm, which could impede the mobility of dislocations in the matrix so that the yield strength increased. After heat treatment, two sizes of γ΄-phase precipitated from the matrix, the size of them were 1 μm and 100 nm respectively. During room temperature tensile deformation of the alloy after being subjected to heat treatment, dislocations could fully share the primary γ΄-phase particles, and even detour the secondary γ΄-phase particles per Orowan mechanism, therewith the yield strength of the alloy decreased. The life of as-cast K416B is longer than that of the heat-treatment counterpart. It can be interpreted that the secondary γ΄-phase particles coarsened rapidly during the durable test. Additionally, the precipitation of nano W₆C particles along the γ-γ΄ interface depleted tungsten in the alloy, which reduced the mismatch between γ and γ΄ phases, resulting in the damage of the durable life of K416B alloy.

Key words: metallic materials K416B alloy γ? precipitation tensile behavior duration dislocation

Received: 07 May 2022

ZTFLH:

TG132.3+2

Fund: National Natural Science Foundation of China(51971214);Natural Science Foundation of Liaoning Province(2020-MS-014)

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	Articles by authors
	Lin WEI
	Sigeng ZHOU
	SHENG Naicheng
	Jinjiang YU
	Guichen HOU
	Biao WANG
	Jia QUAN
	Yizhou ZHOU
	Xiaofeng SUN
	Yong KANG

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https://www.cjmr.org/EN/10.11901/1005.3093.2022.261 OR https://www.cjmr.org/EN/Y2023/V37/I1/29

Fig.1 Schematic diagram of mechanical test samples (a) tensile (b) durable (unit: mm)

Fig.2 OM micrographs of as-cast K416B alloy (a) low magnification, (b) high magnification

Fig.3 DSC results of as-cast K416B (a) heating, (b) cooling

Fig.4 Heat treatment process

Fig.5 Morphologies of γ? phase in K416B (a) as-cast state, (b) heat treatment

Table 1 Tensile properties of K416B alloy

Fig.6 Stress-strain curves of K416B alloy with different microstructures of γ?

Fig.7 Fracture morphologies of K416B alloy with different microstructures of γ? (a, b) as-cast state; (c, d) heat treatment

Fig.8 SEM images of K416B alloy with different microstructures of γ? after fracture (a) as-cast state, (b) heat treatment

Fig.9 TEM images of as-cast K416B alloy after tensile fracture

Fig.10 STEM-EDS images of heat-treatment K416B alloy

Fig.11 TEM images of heat-treatment K416B alloy after tensile fracture

Fig.12 Durable rupture curves of K416B alloys with different morphologies under the condition of 975℃/235 MPa

Fig.13 Cross-sectional view of the alloys under the condition of 975℃/235 MPa (a, b) as-cast state; (c, d) heat treatment

Fig.14 Dislocation structures of K416B after rupture under 975℃/235 MPa

Fig.15 STEM bright field image (a) and corresponding elemental mapping (b) of K416B after creep rupture under 975℃/235 MPa

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