Low-cycle Fatigue Behavior of a Cast Ni-based Superalloy K4169 at 650oC

doi:10.11901/1005.3093.2023.537

Chinese Journal of Materials Research

2024, Vol. 38

Issue (8): 621-631 DOI: 10.11901/1005.3093.2023.537

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Low-cycle Fatigue Behavior of a Cast Ni-based Superalloy K4169 at 650^oC

LIU Qing'ao¹^,², ZHANG Weihong¹^,²(

), WANG Zhiyuan¹^,², SUN Wenru¹^,²(

)

^1.Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
^2.School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China

Cite this article:

LIU Qing'ao, ZHANG Weihong, WANG Zhiyuan, SUN Wenru. Low-cycle Fatigue Behavior of a Cast Ni-based Superalloy K4169 at 650^oC. Chinese Journal of Materials Research, 2024, 38(8): 621-631.

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Abstract

The low cycle fatigue behavior of nickel based cast superalloy K4169 at 650^oC was studied, while its microstructure variation before and after test was assessed by means of SEM and TEM. The results show that the fatigue life of the alloy gradually decreases with the increasing strain. When the strain is 0.5% and 0.6%, the alloy experiences strain hardening within the early 2~200 cycles, followed by cyclic stability and cyclic softening, respectively; When the strain is 0.8% and 1.0%, the alloy exhibits continuous cyclic softening behavior; Initial cyclic hardening is related to the hindering effect of γ″ strengthening phases on the movement of dislocations, while cyclic softening is attributed to dislocations shearing γ″phases repeatedly. The Coffin-Manson equation for the relationship between the plastic strain amplitude and the reverse number of fatigue failure of the alloy exhibits a bilinear relationship. Observation of the microstructure shows that the cyclic deformation mode of the alloy at high and low strains is all dislocations shearing γ″ phase and slip, and the fatigue failure of the alloy under different strains all exhibits transgranular fracture. Therefore, the reason for the bilinear behavior of the alloy may be the transformation of deformation uniformity, and the non-Masing characteristic exhibited by the alloy also demonstrate the transformation of deformation uniformity.

Key words: metallic materials K4169 alloy low-cycle fatigue fracture behavior Coffin-Manson relationship deformation mechanism

Received: 06 November 2023

ZTFLH:

TG146.1+5

Corresponding Authors: ZHANG Weihong, Tel: (024)23971325, E-mail: whzhang@imr.ac.cn
SUN Wenru, Tel: (024)23971737, E-mail: wrsun@imr.ac.cn

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https://www.cjmr.org/EN/10.11901/1005.3093.2023.537 OR https://www.cjmr.org/EN/Y2024/V38/I8/621

Fig.1 Schematic diagram of low cycle fatigue specimen size

Fig.2 Microstructure characteristics of K4169 alloy after heat treatment (a) SEM images showing precipitates (b) BSE images showing precipitates; (c) Coarsening γ″ phase; (d) Low magnification morphology of alloy structure; (e, f) bright- and dark-field TEM images of γ″-Ni₃Nb，respectively; (g) TEM images of δ-Ni₃Nb (Inset in Fig.2 shows the corresponding SAED pattern)

Table 1 Energy dispersive spectroscopy (EDS) results of precipitates and matrix (mass fraction, %)

Fig.3 Cyclic hysteresis loops of alloy with the first cycle (a), Cyclic hysteresis loops of alloy with the half-life (b) and Masing curve of alloy (c)

Fig.4 Cyclic stress response curve of alloy

Fig.5 Cyclic hardening parameter D of alloy under different strains

Fig.6 Relationship between strain amplitudes (Δε/2) and number of reversals to failure (2N_f)

Fig.7 Macroscopic fracture morphology (a) Δε_t = 0.5%; (b) Δε_t = 0.6%; (c) Δε_t = 1.0%

Fig.8 Microscopic fracture morphology (a, d, g) Δε_t = 0.5%; (b, e, h) Δε_t = 0.6%; (c, f, i) Δε_t = 1.0%; (a~f) Morphology of fatigue propagation zone; (g~i) Morphology of fatigue final rupture

Fig.9 Fracture longitudinal section organization (a, b, c) Δε_t = 0.5%; (d, e, f) Δε_t = 0.6%; (g, h, i) Δε_t = 1.0%

Fig.10 Secondary cracks on the longitudinal section of the fracture with a strain of 0.5%, 0.6%, and 1.0%, respectively (a~c) and the associated EBSD maps of the GB (Grain boundary), IPF and KAM with a strain of 1.0% are shown in (d~f)

Fig.11 HRTEM and IFFT image of the specimen with Δε_t = 0.5%，N_f = 100 cycs: (a) The HRTEM micrograph of interdendritic γ″ and γ-matrix with the FFT pattern; (b, c) the corresponding inverse FFT images of areas b an c in (a), respectively; (d) The HRTEM micrograph of γ″ in matrix and γ-matrix with the FFT pattern; (e) The corresponding inverse FFT image of (d) (dislocation as marked with ‘T’)

Fig.12 TEM micrographs of fracture specimens under different strains (a) Bright field image with SAED pattern, Δε_t = 0.5%；(b) Dark field image, Δε_t = 0.5%; (c) Slip bands distribution, Δε_t = 0.5%; (d) Bright field image with SAED pattern，Δε_t = 1.0%; (e) Dark field image, Δε_t = 1.0%; (f) Slip bands distribution, Δε_t = 1.0%

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