EFFECTS OF Hf ON HIGH TEMPERATURE LOW STRESS RUPTURE PROPERTIES OF A SECOND GENERATION Ni-BASED SINGLE CRYSTAL SUPERALLOY DD11

doi:10.11900/0412.1961.2015.00363

Acta Metall Sin

2015, Vol. 51

Issue (10): 1261-1272 DOI: 10.11900/0412.1961.2015.00363

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EFFECTS OF Hf ON HIGH TEMPERATURE LOW STRESS RUPTURE PROPERTIES OF A SECOND GENERATION Ni-BASED SINGLE CRYSTAL SUPERALLOY DD11

Yunsong ZHAO^1,²,Jian ZHANG²,Yushi LUO²,Dingzhong TANG²,Qiang FENG^1,³(

)

1 State Key Laboratory for Advanced Metals and Materials, University of Science and Technology Beijing, Beijing 100083
2 Science and Technology on Advanced High Temperature Structural Materials Laboratory, Beijing Institute of Aeronautical Materials, Beijing 100095
3 Beijing Key Laboratory of Special Melting and Reparation of High-end Metal Materials, Beijing 100083

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Yunsong ZHAO,Jian ZHANG,Yushi LUO,Dingzhong TANG,Qiang FENG. EFFECTS OF Hf ON HIGH TEMPERATURE LOW STRESS RUPTURE PROPERTIES OF A SECOND GENERATION Ni-BASED SINGLE CRYSTAL SUPERALLOY DD11. Acta Metall Sin, 2015, 51(10): 1261-1272.

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Abstract

The effect of Hf on the as-cast, heat-treated microstructures and stress rupture properties under 1100 ℃ and 140 MPa was investigated in four second generation Ni-based single crystal superalloys DD11 with various levels of Hf (0~0.80%, mass fraction) additions. The results indicate that increasing Hf addition resulted in decreasing the solidus and liquidus temperatures, while it enhanced the volume fraction of (γ+γ’) eutectic and MC carbide as well as solidification segregation. The number of micropores reduced significantly and the volume fraction of residual (γ+γ’) eutectic and MC carbide increased after heat treatment as Hf content increased. Compared to the Hf-free alloy, the stress rupture life was observed to increase in the alloys with 0.40%Hf, but dropped in the alloy containing 0.80%Hf. Hf addition increased the elemental partitioning ratio of Re, Mo, Cr, resulting in increasing γ/γ’ misfit and decreasing the spacing of γ/γ’ interfacial dislocation networks. The solution strengthing effect was also improved with the enhanced concentration of Re, Mo and Cr in γ phase in Hf-modified alloys. However, when the Hf content was 0.80% in DD11 alloy, the stress rupture properties was decreased obviously due to high volume fraction of residual (γ+γ’) eutectic and MC carbide in heat-treated microstructures.

Key words: single crystal superalloy Hf elemental partitioning ratio micrstructure stress rupture property

Fund: Supported by National High Technology Research and Development Program (Nos.2012AA03-A513 and 2012AA03A511), National Basic Research Program of China (No.2010-CB631201) and Science Foundation of Ministry of Education of China (No.625010337)

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	Yunsong ZHAO
	Jian ZHANG
	Yushi LUO
	Dingzhong TANG
	Qiang FENG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2015.00363 OR https://www.ams.org.cn/EN/Y2015/V51/I10/1261

Fig.1 OM images of as-cast alloys Hf-1 (a), Hf-2 (b), Hf-3 (c) and Hf-4 (d)

Fig.2 BSE-SEM images of the eutectic region of as-cast alloys Hf-3 (a) and Hf-4 (b)

Table 1 Microstructures characterization of as-cast alloys

Fig.3 Solidification segregation coefficients of alloying elements in the as-cast alloys

Fig.4 DSC heating curves of four as-cast alloys (T_L—liquidus temperature, T_S—solidus temperature)

Fig.5 OM image (a) and interdendrite region BSE-SEM image (b) of alloy Hf-4 after heat treatment at 1320 ℃ for 6 h and then A.C.

Fig.6 Typical microstructures in the dendrite core of alloys Hf-1 (a) and Hf-4 (b) after fully heat treatment

Table 2 Size and volume fraction of γ’ phase, channel width of γ phase in the dendrite cores of alloys after fully heat treatment

Fig.7 OM images of alloys Hf-1 (a), Hf-3 (b) and Hf-4 (c) after fully heat treatment

Fig.8 OM images of un-etched alloys Hf-1 (a), Hf-3 (b) and Hf-4 (c) after fully heat treatment

Table 3 Volume fractions of residual eutectic, carbides and micropores in the interdendrite regions of alloys after fully heat treatment

Fig.9 Elemental partitioning ratio in γ/γ’ phase of alloys after fully heat treatment

Fig.10 γ/γ’ interfacial dislocation networks in alloys Hf-1 (a), Hf-2 (b), Hf-3 (c) and Hf-4 (d) after stress-rupture under 1100 ℃ and 140 MPa

Fig.11 Relationship of average interfacial dislocation spacing and average stress rupture life of alloys under 1100 ℃ and 140 MPa

Fig.12 OM images (a, c) and BSE-SEM images (b, d) of longitudinal sections of stress ruptured fracture of alloys Hf-1(a, b) and Hf-4 (c, d) under 1100 ℃ and 140 MPa

Fig.13 Schematic diagram of MC carbides blocking the diffusion passageways during solution treatment

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