Evolution Behavior of Complex Precipitation Phases in Highly Alloyed GH4151 Superalloy

doi:10.11900/0412.1961.2021.00375

Acta Metall Sin

2023, Vol. 59

Issue (6): 787-796 DOI: 10.11900/0412.1961.2021.00375

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Evolution Behavior of Complex Precipitation Phases in Highly Alloyed GH4151 Superalloy

WANG Fa, JIANG He(

), DONG Jianxin

School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing 100083, China

Cite this article:

WANG Fa, JIANG He, DONG Jianxin. Evolution Behavior of Complex Precipitation Phases in Highly Alloyed GH4151 Superalloy. Acta Metall Sin, 2023, 59(6): 787-796.

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Abstract

Designing high-performance aeroengine is important for development in the aviation industry. One of the key components is turbine disk material that can operate at 800^oC. Among various methods for strengthening alloys, increasing the alloying degree is important, and GH4151 is one of the typical alloys with a high alloying degree. It comprises a large number of refractory metal elements and γ'-forming elements. OM, SEM, and JMatPro software were used to study the sensitivity of GH4151 microstructure evolution during heat treatment processes. The results show that a high alloying degree produces a complex microstructure with low-melting phases, such as Laves, γ/γ′ eutectic, and η phases. Due to the difference in incipient melting temperature of each precipitated phase, a three-stage heat treatment was developed to effectively eliminate the harmful phases in the alloy. The contents of segregation elements Nb and Ti in the as-cast GH4151 alloy have an obvious influence on the incipient melting temperature, whereas the effect of Mo content is relatively slight, and that of W content is not obvious. Decreasing Ti content while increasing Nb and Mo contents could reduce the incipient melting temperature of the η phase. Furthermore, increasing Ti and Mo contents while decreasing Nb content could reduce the incipient melting temperature of Laves phase. A large amount of γ'-forming elements contributes to the cooling rate sensitivity of γ′ phase evolution. 15^oC/min is the critical value for the irregular growth of the γ' phase in the GH4151 alloy. When compared to alloys with low γ′-forming elements content, the γ′ phase in GH4151 alloy has a larger size when the cooling rate is > 15^oC/min, and exhibits an irregular shape when the cooling rate is < 15^oC/min. Thus, a high alloying degree contributes to the complex and sensitive microstructure evolution behavior of GH4151 alloy.

Key words: GH4151 superalloy heat treatment temperature cooling rate microstructure evolution

Received: 03 September 2021

ZTFLH:

TG156.1

Fund: National Key Laboratory of Advanced High-Temperature Materials Open Fund and Fundamental Research Funds for the Central Universities(FRF-TP-19-038A2)

Corresponding Authors: JIANG He, associate professor, Tel:13811910685, E-mail: jianghe@ustb.edu.cn

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https://www.ams.org.cn/EN/10.11900/0412.1961.2021.00375 OR https://www.ams.org.cn/EN/Y2023/V59/I6/787

Fig.1 Thermodynamic calculation results of element distribution behavior during solidification (a) and solidification process (b) of GH4151 superalloy

Fig.2 OM image of dendritic morphology (a), SEM image of γ′ phase at dendritic region (b), SEM images of precipitations at interdendritic region (c-f) in as-cast GH4151 superalloy

Table 1 Chemical compositions of precipitations at interdendritic region in Figs.2d-f of as-cast GH4151 superalloy

Fig.3 SEM images of GH4151 superalloy after heat treated at 1150^oC (a, b), 1160^oC (c, d), 1170^oC (e), 1180^oC (f), and 1190^oC (g) for 10 min and then water quenching

Fig.4 SEM images of GH4151 superalloy after heat treatment at 1140^oC, 10 h (a), 1140^oC, 20 h (b), 1140^oC, 20 h + 1170^oC, 10 h (c), 1140^oC, 20 h + 1170^oC, 10 h + 1200^oC, 20 h (d) based on the key temperature ranges (Insets show the locally enlarged views)

Fig.5 Mass fraction of γ' phase of different alloys (a) and the relationship between ΔT and γ' phase content (ΔT—difference between current temperature and γ' phase precipitation temperature) (b) based on calculation by using JMatPro software

Fig.6 SEM images of γ′ phase in GH4151 superalloy after heat treatment at 1140^oC, 20 h + 1170^oC, 10 h + 1200^oC, 20 h and then water quenching (cooling rate v = 7888^oC/min) (a), oil quenching (v = 2663^oC/min) (b), air cooling (v = 220^oC/min) (c), and furnace cooling (v = 15^oC/min) (d) when the cooling rate ≥ furnace cooling

Fig.7 Low (a, c) and high (b, d) magnified SEM images of γ' phase in GH4151 superalloy after heat treatment at 1140^oC, 20 h + 1170^oC, 10 h + 1200^oC, 20 h and then slow cooling (v = 10^oC/min) (a, b), super slow cooling (v = 1^oC/min) (c, d) when the cooling rate < furnace cooling (Oval regions show the γ' phases with irregular morphologies)

Fig.8 Relationship between the average size of γ' phase (d^{) and v}

Fig.9 SEM images and irregularity coefficients (ξ^{) of different superalloys after cooling at 10^oC/min from the super-solvus state}

Fig.10 Influences of the contents of Ti (a), Nb (b), Mo (c), and W (d) on the incipient melting temperature of the low-melting phases

Fig.11 Schematic of relationship between cooling rate sensibility of γ' phase, degree of alloying, and cooling rate (d_cr—critical diameter of γ' phase growing irregularly; d_ssc, d_sc, and d_fc are the diameters of γ' phase under super slow cooling, slow cooling, and fast cooling, respectively)

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