Design of cuboidal<i> γ</i>/<i>γ′</i> coherent microstructure and its stability in low-density Co-Ni-Al-Mo-Cr-Ti/ Nb/Ta superalloys

Lü Meng-Tian; Li Jin-Lin; Sun Jiu-Dong; Wang Zhen-Hua; Wang Qing; Dong Chuang

doi:10.7498/aps.71.20212444

Abstract

Co-base superalloys generally have high strengths, good oxidation- and corrosion-resistances, as well as excellent creep-resistant properties at high temperatures (HTs), which are ascribed to the coherent precipitation of cuboidal γ′ phase into face-centered-cubic (FCC) γ matrix induced by co-alloying of multiple elements. However, the cuboidal γ/γ′ coherent microstructure is liable to be destabilized after a long-time aging at HTs in Co-base superalloys. In the present work, the cluster formula is used to design a series of low-density Co-base superalloys with the composition of [Al-(Co₈Ni₄)]((Al_0.5(Ti/Nb/Ta)_0.5Mo_0.5)(Mo_0.5Cr_0.5Co_0.5)) (=Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5). Alloy ingots are prepared by arc melting under an argon atmosphere, and are solid-solutionized at 1300 ℃ for 15 h and then aged at 900 ℃ for up to 500 h. Microstructural characterizations and mechanical properties of these alloys in different aged states are obtained by using XRD, SEM, EPMA, TEM, and HV. It is found that all these alloys with Ti/Nb/Ta, Ti/Nb, and Ti/Ta in an equi-molar mixing have a special coherent microstructure with cuboidal γ′ phase uniformly-precipitated into the γ matrix, which is contributed to the moderate lattice misfit of γ/γ′ (0.27%–0.34%). Moreover, these cuboidal γ′ phase are coarsened slowly during aging, in which the microhardness does not vary obviously with aging time (275 HV–296 HV). Especially, the alloy with (Ti/Ta)_0.5 exhibits the highest γ/γ′ microstructural stability with a slow coarsening rate after aging 500 h, and no other second phases appear near the grain boundaries. While needle and bulk particles would precipitate on grain boundaries in other alloys after 500 h-aging.

Keywords:

Authors and contacts

Key Laboratory of Materials Modification by Laser, Ion and Electron Beams, Ministry of Education, Dalian University of Technology, Dalian 116024, China

Corresponding author: Wang Qing, wangq@dlut.edu.cn

Funds: Project supported by the National Natural Science Foundation of China (Grant Nos. 91860108, U1867201) and the Key Discipline and Major Project of Dalian Science and Technology Innovation Foundation, China (Grant No. 2020JJ25CY004 ) .

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References

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Cited By

图 1 设计的Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5 3种合金在900 ℃ /50 h时效后的XRD图谱

Figure 1. XRD patterns of the three designed Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5 alloys after aging at 900 ℃ for 50 h.

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图 2 Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5 3种合金900 ℃/50 h时效后的SEM微观组织观察　(a) S1-TNT; (b) S2-TN; (c) S3-TT

Figure 2. SEM observations of three Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5 alloys at 900 ℃ for 50 h: (a) S1-TNT; (b) S2-TN; (c) S3-TT

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图 3 Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Ta)_0.5合金(S3-TT)时效50 h后的TEM结果　(a) TEM明场(BF)像; (b) TEM暗场(DF)像; (c)TEM高分辨(HRTEM)像及其对应的FFT图谱

Figure 3. TEM characterization of 50 h aged Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Ta)_0.5 alloy (S3-TT): (a) The bright-field (BF) image; (b) the corresponding dark-field (DF) image; (c) the HRTEM image and FFT patterns.

DownLoad: Full-Size Img PowerPoint

图 4 设计的3种合金在900 ℃长期时效过程中γ/γ′共格组织形貌演变　(a-1)—(c-1) S1-TNT时效100, 200, 500 h; (a-2)—(c-2) S2-TN时效100, 200, 500 h; (a-3)—(c-3) S3-TT时效100, 200, 500 h

Figure 4. Microstructural evolutions with the aging time at 900 ℃ of the three alloys: (a-1)−(c-1) Aged S1-TNT for 100, 200, and 500 h, respectively; (a-2)−(c-2) aged S2-TN for 100, 200, and 500 h, respectively; (a-3)−(c-3) aged S3-TT for 100, 200, and 500 h, respectively.

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图 5 3种合金在900 ℃长期时效时γ′相的尺寸r和体积分数f的变化

Figure 5. Variations of particle size r and volume fraction f of γ′ precipitates with the aging time at 900 ℃ in the designed alloys.

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图 6 Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb)_0.5合金(S2-TN)在900 ℃/500 h长期时效后γ/γ′共格组织中的元素分布

Figure 6. Elemental distribution in the γ/γ′ coherent microstructure of 500 h aged Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb)_0.5 alloy (S2-TN) at 900 ℃ with STEM-EDS.

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图 7 设计的3种合金900 ℃时效500 h后晶界处的微观组织　(a) S1-TNT; (b) S2-TN; (c) S3-TT

Figure 7. SEM observations on the microstructure on the grain boundaries in 500 h aged alloys at 900 ℃: (a) S1-TNT; (b) S2-TN; (c) S3-TT.

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图 8 Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5合金(S1-TNT) 900 ℃时效500 h后晶界处析出相的TEM暗场(DF)像及其对应的SAED花样

Figure 8. TEM dark-field (DF) images and the corresponding SAED patterns of precipitated phases on grain boundaries in 500 h aged Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5 alloy (S1-TNT) at 900 ℃.

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图 9 500 h时效后Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5合金(S1-TNT)晶界处的元素分布图

Figure 9. Elemental distribution on the grain boundaries in 500 h aged Co_8.5Ni₄Al_1.5Mo_1.0Cr_0.5(Ti/Nb/Ta)_0.5 alloy (S1-TNT) mapped with EPMA.

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图 10 3种合金在900 ℃时效时显微硬度随时间的变化(a)及合金的密度(b)

Figure 10. Variation of microhardness of the 900 ℃-aged alloys with the aging time (a) and their densities (b).

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图 11 设计的3种合金在900 ℃时效过程中γ′相的尺寸r³随时效时间t的变化

Figure 11. Variation of the average particle size r³ with the aging time at 900 ℃ in the three designed alloys.

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表 1 设计的3种合金的成分(团簇式和原子百分比)、以及900 ℃/50 h时效后γ和γ′两相的晶格常数(a_γ, a_γ′)和点阵错配度(ε)

Table 1. Related data of the designed series of alloys, including cluster formulas, alloy composition, lattice constant (a), lattice misfit (ε) between γ and γ′ phases after aging at 900 ℃ for 50 h.

Alloy	Cluster formulas	Alloy composition/%	a/nm	ε/%
S1-TNT	[Al-(Co₈Ni₄)]((Al_0.5(Ti, Nb, Ta)_0.5Mo_0.5)(Mo_0.5Cr_0.5Co_0.5))	Co_53.13Ni_25.00Al_9.38Ti_1.04Nb_1.04Ta_1.04Cr_3.12Mo_6.25	a_γ = 0.3570 ± 0.0003 a_γ′ = 0.3583 ± 0.0002	0.34 ± 0.05
S2-TN	[Al-(Co₈Ni₄)]((Al_0.5(Ti, Nb)_0.5Mo_0.5)(Mo_0.5Cr_0.5Co_0.5))	Co_53.13Ni_25.00Al_9.38Ti_1.56Nb_1.56Cr_3.12Mo_6.25	a_γ = 0.3575 ± 0.0004 a_γ′ = 0.3584 ± 0.0002	0.27 ± 0.05
S3-TT	[Al-(Co₈Ni₄)]((Al_0.5(Ti, Ta)_0.5Mo_0.5)(Mo_0.5Cr_0.5Co_0.5))	Co_53.13Ni_25.00Al_9.38Ti_1.56Ta_1.56Cr_3.12Mo_6.25	a_γ = 0.3575 ± 0.0004 a_γ′= 0.3586 ± 0.0003	0.29 ± 0.07

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map

[1]	Meyers M A, Chawla K K 2008 Mechanical Behavior of Materials (2nd Ed.) (New York: Cambridge University Press) p1
[2]	Gleiter H, Hornbogen E 1968 Mater. Sci. Eng. 2 285 Google Scholar
[3]	Reed R C 2006 The Superalloys: Fundamentals and Applications (Cambridge: Cambridge University Press) p19
[4]	Kobayashi S, Tsukamoto Y, Takasugi T, Chinen H, Omori T, Ishida K, Zaefferer S 2009 Intermetallics 17 1085 Google Scholar
[5]	Tsukamoto Y, Kobayashi S, Takasugi T 2010 Mater. Sci. Forum. 654 448
[6]	Lass E A, Williams M E, Campbell C E, Moon K W, Kattner U R 2014 J. Phase Equilib. Diffus. 35 711 Google Scholar
[7]	Lass E A, Grist R D, Williams M E 2016 J. Phase equilib. Diffus. 37 387 Google Scholar
[8]	Bauer A, Neumeier S, Pyczak F, Göken M 2010 Intermetallics 63 1197
[9]	Chen Y, Wang C, Ruan J, Omori T, Kainuma R, Ishida K, Liu X 2019 Acta Mater. 170 62 Google Scholar
[10]	Ng D S, Chung D W, Toinin J P, Seidman D N, Dunand D C, Lass E A 2020 Mater. Sci. Eng. A 778 139108 Google Scholar
[11]	Pandey P, Makineni S K, Samanta A, Sharma A, Das S M, Nithin B, Srivastava C, Singh A K, Raabe D, Gault B, Chattopadhyay K 2019 Acta Mater. 163 140 Google Scholar
[12]	Pyczak F, Bauer A, Göken M, Lorenz U, Neumeier S, Oehring M, Paul J, Schell N, Schreyer A, Stark A, Symanzik F 2015 J. Alloy. Compd. 632 110 Google Scholar
[13]	Feng G, Li H, Li S S, Sha J B 2012 Scr. Mater. 67 499 Google Scholar
[14]	Liu X, Chen Z, Chen Y, Yang S, Pan Y, Lu Y, Qu S, Li Y J, Yang Y S, Wang C 2021 Mater. Lett. 284 128910 Google Scholar
[15]	Vorontsov V A, Barnard J S, Rahman K M, Yan H Y, Midgley P A, Dye D 2016 Acta Mater. 120 14 Google Scholar
[16]	Tian L Y, Lizárraga R, Larsson H, Holmström E, Vitos L 2017 Acta Mater. 136 215 Google Scholar
[17]	Naghavi S S, Hegde V I, Wolverton C 2017 Acta Mater. 132 467 Google Scholar
[18]	Neumeier S, Rehman H U, Neuner J, Zenk C H, Michel S, Schuwalow S, Rogal J, Drautz R, Göken M 2016 Acta Mater. 106 304 Google Scholar
[19]	Liu X J, Yu Y, Liu Y H, Huang W L, Lu Y, Guo Y H, Wang C P 2017 J. Phase Equilib. Diffus. 38 733 Google Scholar
[20]	Wang C, Zhao C, Lu Y, Li T, Peng D, Shi J, Liu X 2015 Mater. Chem. Phys. 162 555 Google Scholar
[21]	Ruan J J, Wang C P, Yang S Y, Omori T, Yang T, Kimura Y, Liu X J, Kainuma R, Ishida K 2016 J. Alloy. Compd. 664 141 Google Scholar
[22]	Wang C P, Yang S, Yang S Y, Wang D, Ruan J J, Li J, Liu X J 2015 J. Phase Equilib. Diffus. 36 592 Google Scholar
[23]	Ruan J, Xu W, Yang T, Yu J, Yang S, Luan J, Omori T, Wang C, Kainuma R, Ishida K, Liu C T, Liu X 2020 Acta Mater. 186 425 Google Scholar
[24]	宿彦京, 付华栋, 白洋, 姜雪, 谢建新 2020 金属学报 56 1313 Google Scholar Su Y J, Fu H D, Bai Y, Jiang X, Xie J X 2020 Acta. Metall. Sin. 56 1313 Google Scholar
[25]	Li W, Li L, Wei C, Zhao J C, Feng Q 2021 J. Mater. Sci. Technol. 80 139 Google Scholar
[26]	王清, 查钱锋, 刘恩雪, 董闯, 王学军, 谭朝鑫, 冀春俊 2012 金属学报 48 1201 Google Scholar Wang Q, Zha Q F, Liu E X, Dong C, Wang X J, Tan C X, Ji C J 2012 Acta. Metall. Sin. 48 1201 Google Scholar
[27]	马仁涛, 郝传璞, 王清, 任明法, 王英敏, 董闯 2010 金属学报 46 1034 Google Scholar Ma R T, Hao C P, Wang Q, Ren M F, Wang Y M, Dong C 2010 Acta. Metall. Sin. 46 1034 Google Scholar
[28]	Zhang Y, Wang Q, Dong H G, Dong C, Zhang H Y, Sun X F 2018 Acta Metall. Sin. -Engl. Lett. 31 127 Google Scholar
[29]	Chen C, Wang Q, Dong C, Zhang Y, Dong H 2020 Sci. Rep. 10 1 Google Scholar
[30]	Makineni S K, Samanta A, Rojhirunsakool T, Alam T, Nithin B, Singh A K, Banerjee R, Chattopadhyay K 2015 Acta Mater. 97 29 Google Scholar
[31]	Zhang J, Huang T, Cao K, Chen J, Zong H, Wang D, Zhang J, Zhang J, Liu L 2021 J. Mater. Sci. Technol. 75 68 Google Scholar
[32]	Yang T, Zhao Y L, Tong Y, Jiao Z B, Wei J, Cai J X, Han X D, Chen D, Hu A, Liu C T 2018 Science 362 933 Google Scholar
[33]	Kim K, Voorhees P W 2018 Acta Materi. 152 327 Google Scholar
[34]	Orthacker A, Haberfehlner G, Taendl J, Poletti M C, Sonderegger B, Kothleitner G 2018 Nat. Mater. 17 1101 Google Scholar
[35]	Sims C T, S Stoloff N S, Hagel W C 1987 Superalloy II (New York: John Wiley & Sons Inc) p1
[36]	Nithin B, Samanta A, Makineni S K, Alam T, Pandey P, Singh A K, Banerjee R, Chattopadhyay K 2017 J. Mater. Sci. 52 11036 Google Scholar
[37]	Wang Q, Li Z, Pang S, Li X, Dong C, Liaw P K 2018 Entropy 20 878 Google Scholar
[38]	Yoo Y S, Yoon D Y, Henry M F 1995 Met. Mater. 1 47 Google Scholar
[39]	Zenk C H, Neumeier S, Stone H J, Göken M 2014 Intermetallics 55 28 Google Scholar
[40]	Philippe T, Voorhees P W 2013 Acta Mater. 61 4237 Google Scholar
[41]	Zhou H J, Xue F, Chang H, Feng Q 2018 J. Mater. Sci. Technol. 34 799 Google Scholar

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Design of cuboidal γ/γ′ coherent microstructure and its stability in low-density Co-Ni-Al-Mo-Cr-Ti/ Nb/Ta superalloys

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Corresponding author: Wang Qing, wangq@dlut.edu.cn

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Design of cuboidal γ/γ′ coherent microstructure and its stability in low-density Co-Ni-Al-Mo-Cr-Ti/ Nb/Ta superalloys

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Corresponding author: Wang Qing, wangq@dlut.edu.cn

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