Effects of Rhenium and Tantalum on Microstructural Stability of Hot-Corrosion Resistant Single Crystal Superalloys Aged at 900 ℃

doi:10.11900/0412.1961.2019.00091

Acta Metall Sin

2019, Vol. 55

Issue (11): 1427-1436 DOI: 10.11900/0412.1961.2019.00091

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Effects of Rhenium and Tantalum on Microstructural Stability of Hot-Corrosion Resistant Single Crystal Superalloys Aged at 900 ℃

HUANG Taiwen¹,LU Jing¹,XU Yao¹,WANG Dong²,ZHANG Jian²,ZHANG Jiachen¹,ZHANG Jun¹,LIU Lin¹(

)

1. State Key Laboratory of Solidification Processing, Northwestern Polytechnical University, Xi'an 710072, China
2. Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Cite this article:

HUANG Taiwen,LU Jing,XU Yao,WANG Dong,ZHANG Jian,ZHANG Jiachen,ZHANG Jun,LIU Lin. Effects of Rhenium and Tantalum on Microstructural Stability of Hot-Corrosion Resistant Single Crystal Superalloys Aged at 900 ℃. Acta Metall Sin, 2019, 55(11): 1427-1436.

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Abstract

The development of gas turbines urgently requires the development of new single crystal superalloys with capacity to service for long time at higher temperature and under hot corrosion environment. In order to take into account both the strength and structural stability of the alloy, it is an effective way to increase the content of key strengthening elements Re and Ta reasonably, and control the mismatch of γ/γ' to delay the growth kinetics of γ'. In this work, the long-term thermal exposure (LTTE) experiments of single crystal superalloys with different Re and Ta contents at 900 ℃ were carried out. The evolution of morphology and size of γ', and the precipitation of topological close-packed (TCP) phase during 0~7500 h ageing process were quantitatively analyzed. The results show that the size and the coarsening rate of γ' phase decreases with the increase of Ta and Re content in 2Ta2Re, 5Ta0Re, 5Ta2Re, 8Ta0Re and 8Ta2Re alloys. The coarsening rates are 1.445×10^-5, 1.569×10^-5, 1.390×10^-5, 1.465×10^-5and 1.384×10^-5 μm³/h respectively. With the increase of Ta and Re content, the effective diffusion coefficient decreases and the diffusion activation energy increases, thus of the coarsening rate of precipitated phase decreases. After ageing for 2000 h, TCP phase was precipitated in turn in alloys containing Re, and the precipitation of TCP phase was more serious in alloys containing higher content of Ta. The interaction between Ta and Re affects the atomic distribution behavior of elements in γ and γ', in which 8Ta2Re alloy Ta enters the γ' phase to increase its lattice constant, and at the same time promotes the distribution of elements such as Re, W and Cr in the γ matrix, which results in more negative γ/γ' mismatch and promotes the precipitation of TCP phase.

Key words: hot-corrosion resistant single crystal superalloy long-term thermal exposure microstructural stability

Received: 01 April 2019

ZTFLH:

TG132.3

Fund: National Key Research and Development Program No(2016YFB0701400);National Natural Science Foundation of China(51331005);National Natural Science Foundation of China(51631008)

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	Taiwen HUANG
	Jing LU
	Yao XU
	Dong WANG
	Jian ZHANG
	Jiachen ZHANG
	Jun ZHANG
	Lin LIU

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https://www.ams.org.cn/EN/10.11900/0412.1961.2019.00091 OR https://www.ams.org.cn/EN/Y2019/V55/I11/1427

Fig.1 Atomic distribution maps of elements in γ and γ′ phases of 2Ta2Re

Fig.2 Concentration distribution of elements in the region near γ/γ′ interface in 2Ta2Re

Fig.3 Partition ratios of alloying elements between γ and γ′ phases (k_i^γ^/^γ′) of the five alloys

Fig.4 Microstructure morphologies at dendritic core of 2Ta2Re (a1~a4), 5Ta0Re (b1~b4), 5Ta2Re (c1~c4), 8Ta0Re (d1~d4) and 8Ta2Re (e1~e4) alloys during long-term thermal exposure (LTTE) at 900 ℃ for 100 h (a1~e1), 1000 h (a2~e2), 2000 h (a3~e3) and 5000 h (a4~e4)

Table1 Feret Ratio of the γ' precipitates during LTTE at 900 ℃ of five alloys

Fig.5 Size of γ′ precipitates at different thermal exposure time (a) and coarsening rate of γ′ phase (b) for five alloys during LTTE at 900 ℃ (r—size of γ′)

Fig.6 Area fraction of TCP precipitates of 5Ta2Re and 8Ta2Re alloys after LTTE for different time

Fig.7 Morphologies of TCP phase precipitated after LTTE at 900 ℃ for different time(a) 5Ta2Re, 7500 h (b) 8Ta2Re, 2000 h (c) 8Ta2Re, 7500 h (d) 8Ta2Re, 10000 h

Table 2 Lattice parameter of γ and γ′ phases and γ/γ′ misfit at room temperature of five alloys after standard heat treatment

Table 3 A qualitative listing of the γ' precipitates morphology during LTTE at 900 ℃ and misfit of the five alloys

Element	$D 0 m . N i$ / (m²·s^-1)	$Q m, N i$ / (kJ·mol^-1)
Cr	3×10^-6	170.7
Co	7.5×10^-5	285.1
Mo	1.15×10^-4	281.3
Re	8.2×10^-7	255.0
W	8.0×10^-6	264.0
Ni	1.9×10^-4	284.0

Table 4 Pre-exponential factor (

D 0 m . N i

) and diffusion activation energy (

Q m . N i

) for solute atoms in Ni^[23]

Alloy	$D e f f$ / (m²·s^-1)	$Q e f f$ / (kJ·mol^-1)
2Ta2Re	9.98×10^-6	368.63
5Ta0Re	1.15×10^-5	369.83
5Ta2Re	8.67×10^-6	378.76
8Ta0Re	9.29×10^-6	385.05
8Ta2Re	7.66×10^-6	387.89

Table 5 Calculated effective diffusivity (

D e f f

) and diffusion activation energy (

Q e f f

) of five alloys

Alloy	$N V ˉ$	Tendency	$M d ˉ$	Tendency	$? S$	Tendency	V_TCP / %	S_TCP / %
2Ta2Re	1.78	No	0.954	No	-4.47	No	0.79	0.1
5Ta0Re	1.85	No	0.966	No	-4.29	No	0	0
5Ta2Re	1.95	No	0.973	No	0.73	Yes	2.42	1.8
8Ta0Re	2.05	No	0.986	Yes	3.44	Yes	0	0
8Ta2Re	2.18	No	0.993	Yes	5.58	Yes	4.28	5.6

Table 6 Values of

N V ˉ

、

M d ˉ

、

? S

and TCP phase volume fraction calculated by JMatPro，and measured value of TCP phase area fraction of five kinds of experimental alloys

[1]	PollockT M, TinS. Nickel-based superalloys for advanced turbine engines: Chemistry, microstructure and properties [J]. J. Propuls. Power, 2006, 22: 361
[2]	KonterM, ThumannM. Materials and manufacturing of advanced industrial gas turbine components [J]. J. Mater. Process. Technol., 2001, 117: 386
[3]	SatoA, MoverareJ J, HasselqvistM, et al. On the mechanical behavior of a new single-crystal superalloy for industrial gas turbine applications [J]. Metall. Mater. Trans., 2012, 43A: 2302
[4]	SinghK. Advanced materials for land based gas turbines [J]. Trans. Indian Inst. Met., 2014, 67: 601
[5]	LiM S. High Temperature Corrosion of Metals [M]. Beijing: Metallurgical Industry Press, 2001: 34
[5]	李美栓. 金属的高温腐蚀 [M]. 北京: 冶金工业出版社, 2001: 34
[6]	SidhuR K, OjoO A, ChaturvediM C. Sub-solidus melting of directionally solidified René 80 superalloy during solution heat treatment [J]. J. Mater. Sci., 2008, 43: 3612
[7]	GordonA P, TrexlerM D, NeuR W, et al. Corrosion kinetics of a directionally solidified Ni-base superalloy [J]. Acta Mater., 2007, 55: 3375
[8]	GiameiA F, AntonD L. Rhenium additions to a Ni-base superalloy: Effects on microstructure [J]. Metall. Trans., 1985, 16A: 1997
[9]	WangW Z, JinT, LiuJ L, et al. Role of Re and Co on microstructures and γ′ coarsening in single crystal superalloys [J]. Mater. Sci. Eng., 2008, A479: 148
[10]	PyczakF, DevrientB, NeunerF C, et al. The influence of different alloying elements on the development of the γ/γ′ microstructure of nickel-base superalloys during high-temperature annealing and deformation [J]. Acta Mater., 2005, 53: 3879
[11]	Booth-MorrisonC, NoebeR D, SeidmanD N. Effects of tantalum on the temporal evolution of a model Ni-Al-Cr superalloy during phase decomposition [J]. Acta Mater., 2009, 57: 909
[12]	DurstK, G?kenM. Micromechanical characterisation of the influence of rhenium on the mechanical properties in nickel-base superalloys [J]. Mater. Sci. Eng., 2004, A387-389: 312
[13]	WangB, ZhangJ, HuangT W, et al. Effect of Co on microstructural stability of the third generation Ni-based single crystal superalloys [J]. J. Mater. Res., 2016, 31: 1328
[14]	WangB, ZhangJ, PanX J, et al. Effects of W on microstructural stability of the third generation Ni-based single crystal superalloys [J]. Acta Metall. Sin., 2017, 53: 298
[14]	王博, 张军, 潘雪娇等. W对第三代镍基单晶高温合金组织稳定性的影响 [J]. 金属学报, 2017, 53: 298
[15]	WangJ. Microstructure stability of a rhenium-containing nickel-based single crystal superalloy and thermodynamical design of low rhenium-containing alloys [D]. Shanghai: Shanghai Jiaotong University, 2011
[15]	王静. 含铼镍基单晶高温合金组织稳定性及低铼成分的热力学设计 [D]. 上海: 上海交通大学, 2011
[16]	PyczakF, DevrientB, MughrabiH. The effects of different alloying elements on the thermal expansion coefficients, lattice constants and misfit of nickel-based superalloys investigated by X-ray diffraction [A]. Superalloys 2004 [C]. Warrendale, PA: TMS, 2004: 827
[17]	JiangX W, WangD, XieG, et al. The effect of long-term thermal exposure on the microstructure and stress rupture property of a directionally solidified Ni-based superalloy [J]. Metall. Mater. Trans., 2014, 45A: 6016
[18]	PanJ S, TongJ M, TianM B. Fundamentals of Materials Science [M]. Beijing: Tsinghua University Press, 1998: 550
[18]	潘金生, 仝健民, 田民波. 材料科学基础 [M]. 北京: 清华大学出版社, 1998: 550
[19]	WangT, ChenL Q, LiuZ K. First-principles calculations and phenomenological modeling of lattice misfit in Ni-base superalloys [J]. Mater. Sci. Eng., 2006, A431: 196
[20]	ZhouN, ShenC, MillsM J, et al. Phase field modeling of channel dislocation activity and γ′ rafting in single crystal Ni-Al [J]. Acta Mater., 2007, 55: 5369
[21]	JenaA K, ChaturvediM C. The role of alloying elements in the design of nickel-base superalloys [J]. J. Mater. Sci., 1984, 19: 3121
[22]	ShuD L, TianS G, NingT, et al. Influence of Re/Ru on concentration distribution in the γ/γ′ phases of nickel-based single crystal superalloys [J]. Mater. Des., 2017, 132: 198
[23]	ZhuZ, BasoaltoH, WarnkenN, et al. A model for the creep deformation behaviour of nickel-based single crystal superalloys [J]. Acta Mater., 2012, 60: 4888
[24]	HobbsR A, ZhangL, RaeC M F, et al. Mechanisms of topologically close-packed phase suppression in an experimental ruthenium-bearing single-crystal nickel-base superalloy at 1100 ℃ [J]. Metall. Mater. Trans., 2008, 39A: 1014
[25]	ShuD L, TianS G, TianN, et al. Influence of Re/Ru on concentration distribution in the γ/γ′ phase of nickel-based single crystal superalloys [J]. Mater. Des., 2017,132: 198
[26]	ChenZ Q, HanY F, ZhongZ G, et al. Solubility prediction of multiple-component superalloys [J]. J. Aeronaut. Mater., 1998, 18(3): 8
[26]	陈志强, 韩雅芳, 钟振纲等. 多元高温合金固溶极限预测 [J]. 航空材料学报, 1998, 18(3): 8

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