Effects of Grain Size on Fatigue Properties of K492 Superalloy

doi:10.11901/1005.3093.2018.277

Chinese Journal of Materials Research

2018, Vol. 32

Issue (11): 834-842 DOI: 10.11901/1005.3093.2018.277

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Effects of Grain Size on Fatigue Properties of K492 Superalloy

Zhiyuan LIU¹, Yongjun LIU¹, Peng LIU^2,³, Chuanyong CUI²(

)

1 China Aviation Development Hunan Institute of Power Machinery, Zhuzhou 412002, China
2 Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
3 School of Materials Science and Engineering, University of Science and Technology of China, Hefei 230026, China

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Zhiyuan LIU, Yongjun LIU, Peng LIU, Chuanyong CUI. Effects of Grain Size on Fatigue Properties of K492 Superalloy. Chinese Journal of Materials Research, 2018, 32(11): 834-842.

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Abstract

Effects of grain size on the fatigue properties of Ni-base superalloy K492 at 700℃ and 800℃ with various grain sizes were investigated. The fatigue fracture mechanism is analyzed by scanning electron microscopy and transmission electron microscopy. The results show that grain refinement improves the fatigue properties of K492 at 700℃ and 800℃. For high-cycle fatigue (HCF) at 700℃, fatigue cracks occur at the metallurgical defect or at a certain crystal plane. The distribution of dislocation configuration is band-like and the morphology of γ' phase does not change. The dislocations pass through the γ' phase by shearing or Orowan loops passing. For HCF at 800℃ the fatigue cracks generated at the defects. In some regions the morphology of dislocation configuration was similar to that at 700℃ HCF and the morphology of γ' phase does not change; In the other region, the γ' phase rafts and dislocations distribute in the matrix channel, and the γ' phase loses the pinning effect of dislocations. For low-cycle fatigue (LCF) at 700℃, fatigue cracks mainly originate from the surface. For LCF at 800℃, fatigue cracks mainly occur at the secondary surface or at a certain crystal plane.

Key words: metallic materials superalloy grain refinement fatigue property dislocation configuration fracture mechanism

Received: 18 April 2018

ZTFLH:

TG146

Fund: Supported by National Natural Science Foundation of China (No. 51671189)

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	Zhiyuan LIU
	Yongjun LIU
	Peng LIU
	Chuanyong CUI

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https://www.cjmr.org/EN/10.11901/1005.3093.2018.277 OR https://www.cjmr.org/EN/Y2018/V32/I11/834

Fig.1 Grain distribution of the as-cast state samples with two different grain sizes (a) coarse-grained samples, (b) fine-grained samples

Fig.2 Microstructures of the samples with two different grain size after heat treatment (a) (b) (c) the γ' phase, carbide and eutectic structure of the coarse-grained samples, (d) (e) (f) The γ' phase, carbide and eutectic structure of the fine-grained samples

Fig.3 Porosities distribution in the specimens

Fig.4 High-cycle S-N curve of the two specimens tested at 700℃ (a) and 800℃ (b) in the double logarithmic coordinate (

N f

—Number of cycles to failure)

	700℃		800℃
	$σ f'$ /MPa	b	$σ f'$ /MPa	b
Coarse-grained	853	-0.082	1241	-0.104
Fine-grained	855	-0.04	902	-0.07

Table 1 High cycle fatigue parameters of K492 alloy at different temperatures for coarse-grained and fine-grained specimens

Fig.5 Porosities in the subsurface of the sample (a) the fracture surface of the coarse-grained samples after the 700℃ HCF experiments, (b) the fracture surface of the coarse-grained samples after the 800℃ HCF experiments

Fig.6 Fatigue cracks formed in the crystal surface in the sample (a) the fracture surface of the coarse-grained samples after the 700℃ HCF experiments, (b) the fracture surface of the fine-grained samples after the 700℃ HCF experiments

Fig.7 Dislocation configurations of the fine-grained K492 samples after the HCF test at different temperatures (a) (b) (c) at 700℃; (d) (e) (f) at 800℃

Fig.8 Cyclic stress response curves of the two specimens under various total strain tested at 700℃

Fig.9 Cyclic stress response curves of the two specimens under various total strain tested at 800℃

Fig.10 Fatigue cracks in the sample after the 700℃ LCF experiments (a) (b) the fracture surface of the coarse-grained samples, (c) (d) the fracture surface of the fine-grained samples

Fig.11 The fatigue cracks in the sample after the 800℃ LCF experiments (a) (b) the fracture surface of the coarse-grained samples, (c) (d) the fracture surface of the fine-grained samples

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