Effect of Cr/Mo/W on the Thermal Stability ofγ/γ′Coherent Microstructure in Ni-Based Superalloys

doi:10.11900/0412.1961.2022.00064

Acta Metall Sin

2024, Vol. 60

Issue (4): 453-463 DOI: 10.11900/0412.1961.2022.00064

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Effect of Cr/Mo/W on the Thermal Stability ofγ/γ′Coherent Microstructure in Ni-Based Superalloys

FAN Lihua, LI Jinlin, SUN Jiudong, LV Mengtian, WANG Qing(

), DONG Chuang

Key Laboratory of Materials Modification by Laser, Ion and Electron Beams (Ministry of Education), School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024, China

Cite this article:

FAN Lihua, LI Jinlin, SUN Jiudong, LV Mengtian, WANG Qing, DONG Chuang. Effect of Cr/Mo/W on the Thermal Stability ofγ/γ′Coherent Microstructure in Ni-Based Superalloys. Acta Metall Sin, 2024, 60(4): 453-463.

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Abstract

In general, Ni-based superalloys exhibit high strength, good oxidation and corrosion resistance, and good creep-resistant properties at high temperatures (HTs) because of the coherent precipitation of cuboidal γ′ nanoparticles into a fcc-γ matrix induced by co-alloying of multiple elements. The present work designed a series of Ni-based superalloys based on the cluster composition formula [Al-Ni₁₂](Al₁(Ti, Nb, Ta)_0.5(Cr, Mo, W)_1.5), with S1-CM (Cr_1.0Mo_0.5), S2-CW (Cr_1.0W_0.5), and S3-CMW (Cr_0.7Mo_0.4W_0.4), in which the amounts of Cr, Mo, and W were changed, whereas the contents of other elements were maintained. In addition, the effect of Cr, Mo, and W variation on the thermal stability of γ /γ′ coherent microstructure at HT in these superalloys was investigated. Alloy ingots were prepared by arc melting under an argon atmosphere, solid solutionized at 1300°C for 15 h, and then aged at 900°C for up to 500 h. Microstructural characterization and mechanical properties of these alloys in different aged states were studied by XRD, SEM, EPMA, TEM, Vickers hardness testing, and compressive testing.Result showed that all these three alloys have a high volume fraction (f > 70%) of γ′ particles uniformly distributed in the fcc-γ matrix. In particular, the γ′ particle shape is ellipsoidal in S1-CM and S2-CW alloys, whereas it is cuboidal in the S3-CMW alloy primarily because the latter has a more negative γ /γ′ lattice misfit (δ = -0.47%) than the former (δ = -0.25% to -0.33%). After aging for 500 h, the morphology of γ′ particles in each alloy has no evident change, and all of the particles have a slow coarsening rate (K = 10-18 nm³/s), in which the S3-CMW alloy exhibits the highest γ /γ′ microstructural stability (the coarsening rate of γ′ particles being K = 10.02 nm³/s). Moreover, the amount of second-phase precipitation near the grain boundaries in the S3-CMW alloy is less than that in the former two alloys. The microhardness test results showed that the microhardness of each alloy remains almost constant with aging time, thereby indicating the thermal stability of the coherent structure. In particular, the microhardness of the S3-CMW alloy is 397-418 HV, and the room-temperature compression yield strength is 818 MPa in the 200-h-aged state.

Key words: Ni-based superalloy coherent microstructure γ′ particle coarsening second phase precipitation

Received: 21 February 2022

ZTFLH:

TG113.12

Fund: National Natural Science Foundation of China(91860108);Key Discipline and Major Project of Dalian Science and Technology Innovation Foundation(2020JJ25CY004)

Corresponding Authors: WANG Qing, professor, Tel: (0411)84708615, E-mail: wangq@dlut.edu.cn

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	FAN Lihua
	LI Jinlin
	SUN Jiudong
	LV Mengtian
	WANG Qing
	DONG Chuang

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00064 OR https://www.ams.org.cn/EN/Y2024/V60/I4/453

Table 1 Related data of the designed series of alloys, including cluster formula, alloy composition, γ′ particle size (r), γ′ volume fraction (f), microhardness (H) after aging at 900^oC for 500 h, and lattice constant (a_γ, a_γ'), lattice misfit (δ) between γ and γ′ phase after aging at 900^oC for 50 h

Fig.1 Equilibrium phase diagrams of the designed alloys calculated by Pandat software (Inset shows the typical peak-separation fitting of (200) plane in S1-CM alloy)
(a) S1-CM (b) S2-CW (c) S3-CMW

Fig.2 OM image of the S3-CMW alloy after aging at 900^oC for 50 h

Fig.3 XRD spectra of designed series of alloys after aging at 900^oC for 50 h (Inset shows the corresponding local plots)

Fig.4 SEM images of designed alloys of S1-CM (a1, b1), S2-CW (a2, b2), and S3-CMW (a3, b3) after solid-solutionized at 1300^oC for 15 h (a1-a3) and aged at 900^oC for 50 h (b1-b3)

Fig.5 TEM dark-field images and selected area electron diffraction (SAED) patterns (insets) of 50 h-aged S1-CM (a) and S3-CMW (b) alloys

Fig.6 Microstructure evolutions of the alloys S1-CM (a1-c1), S2-CW (a2-c2), and S3-CMW (a3-c3) aged at 900^oC for 100 h (a1-a3), 200 h (b1-b3), and 500 h (c1-c3)

Fig.7 Variations of particle size (a) and volume fraction (b) of γ′ precipitates with the aging time at 900^oC in the designed alloys

Fig.8 SEM images of microstructures on the grain boundaries in 500 h-aged alloys at 900^oC
(a) S1-CM (b) S2-CW (c) S3-CMW

Fig.9 TEM bright-field images and the corresponding SAED patterns (insets) of precipitated phases on grain boundaries in 500 h-aged S3-CMW alloy at 900^oC
(a) μ phase (b) fcc phase

Fig.10 Back scattered electrons image (BEI) and corresponding elemental distribution maps on grain boundaries in 500 h-aged S3-CMW alloy at 900^oC

Fig.11 Variations of microhardness of the 900^oC-aged alloys with the aging time (a) and compressive true stress-strain curves of 200 h-aged alloys measured at room temperature (b)

Fig.12 Variations of the average particle size r³ with the aging time at 900^oC in the series of alloys (K—coarsening rate constant, R²—coefficient of determination)

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