MICROSTRUCTURAL DEGRADATION AND MECHANI- CAL PROPERTIES OF GH4033 ALLOY AFTER OVERHEATING FOR SHORT TIME

doi:10.11900/0412.1961.2015.00265

Acta Metall Sin

2015, Vol. 51

Issue (10): 1242-1252 DOI: 10.11900/0412.1961.2015.00265

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MICROSTRUCTURAL DEGRADATION AND MECHANI- CAL PROPERTIES OF GH4033 ALLOY AFTER OVERHEATING FOR SHORT TIME

Jinyan TONG^1,²,Wei FENG^1,³,Chao FU²,Yunrong ZHENG²,Qiang FENG^1,²(

)

1 National Centre for Materials Service Safety, University of Science and Technology Beijing, Beijing 100083
2 State Key Laboratory for Advanced Metals and Materials, University of Science and Technology Beijing, Beijing 100083
3 Casting Center, Beijing Institute of Aeronautical Materials, Beijing 100095

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Jinyan TONG,Wei FENG,Chao FU,Yunrong ZHENG,Qiang FENG. MICROSTRUCTURAL DEGRADATION AND MECHANI- CAL PROPERTIES OF GH4033 ALLOY AFTER OVERHEATING FOR SHORT TIME. Acta Metall Sin, 2015, 51(10): 1242-1252.

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Abstract

Service safety of turbine blades in aircraft engines are threatened by microstructural and property degradation instantly caused by overheating during service. Systematic investigations about microstructural degradation during overheating exposures and its influence on mechanical properties of turbine blades during service are limitedly reported. In this work, microstructure and mechanical properties of GH4033 alloy, which was sectioned from the shank of a serviced 2^nd stage turbine blade in an aircraft engine, were studied after overheating at 900~1100 ℃ for 3 min. Microstructural degradation during overheating exposures as well as its influence on room temperature hardness and stress rupture life at 700 ℃, 430 MPa were analyzed. The results of microstructural characterization indicated that the coarsening and dissolution of γ’ precipitates were introduced by overheating exposures, and all of the γ’ precipitates dissolved at 980 ℃ for 3 min. Gradual dissolution of grain boundary (GB) carbides was observed with the increase of overheating temperature. Complete dissolution of GB carbides at 1100 ℃ resulted in grain growth. The room temperature hardness after overheating exposures decreased grossly with the dissolution of γ’ phase. Due to the dissolution and re-precipitation of γ’ phase as well as the dissolution of GB carbides, the stress rupture life under 700 ℃, 430 MPa of GH4033 alloy was initially increased and then decreased significantly.

Key words: GH4033 wrought alloy turbine blade overheating microstructure rupture property

Fund: Supported by National High Technology Research and Development Program of China (No.2012-AA03A513) and Key Project of Chinese Ministry of Education (No.625010337)

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	Jinyan TONG
	Wei FENG
	Chao FU
	Yunrong ZHENG
	Qiang FENG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2015.00265 OR https://www.ams.org.cn/EN/Y2015/V51/I10/1242

Fig.1 Profile and temperature distribution during service of the 2^nd stage turbine blade made of GH4033 alloy

Fig.2 Sketch of non-standard plate-type specimen for stress rupture test (unit: mm)

Fig.3 Microstructures of as-received GH4033 alloy
(a) carbides along grain boundaries (GBs) and interior grain
(b) morphology of γ’ precipitates

Fig.4 DSC curve of as-received GH4033 alloy

Fig.5 OM images of as-received GH4033 alloy (a) and after overheating at 1100 ℃ for 3 min (b)

Fig.6 Carbide morphologies along grain boundaries in as-received GH4033 alloy (a) and after overheating at 900 ℃ (b),950 ℃ (c), 980 ℃ (d), 1050 ℃ (e) and 1100 ℃ (f) for 3 min followed by water quenching

Fig.7 γ’ morphologies in GH4033 alloy after overheating at 900 ℃ (a), 950 ℃ (b), 980 ℃ (c) for 3 min followed by water quenching

Fig.8 Vickers hardness of as- received GH4033 alloy and after overheating at different temperatures for 3 min

Fig.9 Stress rupture life of GH4033 alloy after overheating at different temperatures for 3 min under 700 ℃ ,430 MPa

Table 1. Average size and volume fraction of γ’ precipitates in GH4033 alloy after overheating at different temperatures for 3 min

Fig.10 Morphologies of GB carbides (a, c) and γ’ phases (b, d) in GH4033 alloy after overheating at 950 ℃ (a, b) and 980 ℃ (c, d) for 3 min followed by heat treatment at 700 ℃ for 2 h and then water quenching

Fig.11 Morphologies of GB carbides (a, c) and γ’ phases (b, d) of GH4033 alloy after overheating at 950 ℃ (a, b) and 980 ℃ (c, d) for 3 min followed by stress rupture at 700 ℃, 430 MPa

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