Creep Properties and Solute Atomic Segregation of High-W and High-Ta Type Powder Metallurgy Superalloy

doi:10.11900/0412.1961.2023.00138

Acta Metall Sin

2023, Vol. 59

Issue (9): 1230-1242 DOI: 10.11900/0412.1961.2023.00138

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Creep Properties and Solute Atomic Segregation of High-W and High-Ta Type Powder Metallurgy Superalloy

BAI Jiaming¹^,²^,³, LIU Jiantao¹^,², JIA Jian¹^,², ZHANG Yiwen¹^,²(

)

¹High Temperature Material Research Institute, Central Iron and Steel Research Institute, Beijing 100081, China
²Gaona Aero Material Co. Ltd., Beijing 100081, China
³School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China

Cite this article:

BAI Jiaming, LIU Jiantao, JIA Jian, ZHANG Yiwen. Creep Properties and Solute Atomic Segregation of High-W and High-Ta Type Powder Metallurgy Superalloy. Acta Metall Sin, 2023, 59(9): 1230-1242.

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Abstract

Developing superalloys and improving their temperature capability are extremely crucial for the advancement of aero-engines. The powder metallurgy (PM) technology can prevent the macroscopic segregation caused by casting and create a high-alloying aero-engine turbine disk alloy having remarkable microstructural homogeneity and superior thermal capability. PM superalloys have been developed into the 3rd generation alloys for decades, and alloys such as René104 already entered service. The chemical composition of the 4th generation PM superalloy is still being researched with the aim of increasing the temperature capability for disk applications to 815^oC. In this work, the remarkable creep resistance and creep strengthening mechanism of a novel high-W and high-Ta type PM superalloy GNPM01 was examined. The creep deformation mechanism of GNPM01 alloy and the segregation of elements on deformation defects were investigated using advanced spherical aberration-corrected scanning transmission electron microscopy. The results reveal that the creep resistance of GNPM01 alloy is considerably higher than that of the 3rd generation PM superalloy. The temperature capacity of GNPM01 alloy is approximately 40^oC greater than that of FGH4098 alloy under the creep condition of 600 MPa and 1000 h. The creep strength of GNPM01 alloy is approximately 160 MPa higher than that of the FGH4098 alloy at 815^oC. In the experimental conditions, the creep deformation behavior was dominated by deformed microtwins, and the GNPM01 alloy clearly slowed down the widening of extended stacking faults and the thickening of microtwins during the creep deformation. It was discovered that the element enrichment of Co, Cr, and Mo existed in the microtwins, and the phase transformation of the twin-structure in γ' phase was disordered because of the segregation of Co, Cr, and Mo by atomic-level energy dispersive X-ray spectroscopy. The isolated superlattice stacking faults in FGH4098 alloy also occurred in the disordered phase transitions. The disordering of superlattice stacking fault or microtwin structure was due to the segregation of Cr, Co, and Mo, which also resulted in the a / 6<112> Shockley partials shearing γ′ phase without producing high-energy nearest-neighbor Al—Al bonds. The segregation disordered the L1₂ structure resulted in reduced pinning of partials by the ordered γ′ phase, which increased the creep rate of the alloy. During the GNPM01 alloy creeping at 815^oC, solute atoms W, Ta, and Nb segregated at the isolated superlattice extrinsic stacking fault (SESF) had ordered atomic occupancy. The fault-level local phase transformation occurred in isolated SESF, forming the [(Ni, Co)₃(Ti, Nb, Ta, W)] ordered η phase that can effectively inhibit the formation and expansion of microtwins, thus lowering the creep rate of GNPM01 alloy.

Key words: powder metallurgy superalloy W Ta creep mechanism local phase transformation microtwin

Received: 03 April 2023

ZTFLH:

TG123.3

Fund: National Science and Technology Major Project(2017-VI-0008-0078)

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https://www.ams.org.cn/EN/10.11900/0412.1961.2023.00138 OR https://www.ams.org.cn/EN/Y2023/V59/I9/1230

Table 1 Chemical compositions of GNPM01, FGH4098^[24], and FGH4096^[24] alloys

Fig.1 Grain boundaries and γ′ phase morphologies (insets) of GNPM01 (a) and FGH4098 (b) alloys after standard heat treatment (SHT) (Black lines indicate the high-angle grain boundaries, red lines indicate the annealing twin boundaries)

Fig.2 Distributions of misorientation angle (a), concentrations of solute atoms in γ (b) and γ′ (c) phases in GNPM01 and FGH4098 alloys after SHT

Fig.3 Extrapolations of creep rupture strength of FGH4096, FGH4098, and GNPM01 alloys using Larson-Miller relationship

Fig.4 Creep strain and time curves (a, c, e) and creep strain rate and time curves (b, d, f) of GNPM01 and FGH4098 alloys under 650^oC (a, b), 750^oC (c, d), and 815^oC (e, f)

Fig.5 Dislocation substructures of FGH4098 and GNPM01 alloys after creep rupture at 650^oC and 980 MPa
(a) TEM bright field (TEM-BF) image and SAED pattern (inset) of FGH4098 alloy (MT—microtwin, BD—beam direction)
(b) TEM-BF image and SAED pattern (inset) of GNPM01 alloy
(c) high-angle annular dark field (HAADF) image of GNPM01 alloy (left) and geometric phase analysis (right) (Superlattice extrinsic stacking fault (SESF)-like fault (two-layer complex layer faults (CSF)) was thickened by a Shockley to form three-layer microtwins, as indicated by the arrow)
(d) HRTEM image of MTs in FGH4098 alloy
(e) HAADF image of MTs in GNPM01 alloy

Fig.6 STEM low-angle annular dark field (LAADF) image (a), and STEM-HAADF image and corresponding element EDS mapping (b) along MTs in FGH4098 alloy after creep rupture at 650^oC and 980 MPa

Fig.7 STEM-HAADF image and corresponding element EDS maps along microtwins in GNPM01 alloy after creep rupture at 650^oC and 1100 MPa

Fig.8 TEM-BF images of the edge-on view of the deformed microtwin in FGH4098 alloy after creep rupture at 750^oC and 650 MPa (a), and GNPM01 alloy after creep rupture at 750^oC and 700 MPa (b) (Obtained by BD//<011> zone axis. Insets show the TEM-DF images of the microtwins)

Fig.9 STEM-annular bright field (ABF) images of dislocation substructures close to [001] zone axis (a, b) and STEM-HAADF images of dislocation substructures close to [011] zone axis (c, d) in FGH4098 (a, c) and GNPM01 (b, d) alloys after creep rupture at 815^oC and 460 MPa (Inset in Fig.9c shows the thickness of the microtwin in FGH4098 alloy. SSF—superlattice stacking fault)

Fig.10 STEM-HAADF image of isolated superlattice stacking fault in GNPM01 alloy after creep rupture at 815^oC and 460 MPa (a), and corresponding EDS maps (b) and EDS line scaning (c)

Fig.11 HAADF images and high-resolution EDS mappings with atomic occupancy information around the microtwins in FGH4098 (a) and GNPM01 (b) alloys

Fig.12 STEM-HAADF image of isolated SESF in FGH4098 alloy (a), contract intensity line scans (b), and disordered elements segregate at stacking faults and the corresponding atomic-level EDS mapping (c)

Fig.13 STEM-HAADF image of isolated SESF in GNPM01 alloy (a), local enlarged HAADF image in Fig.13a and contract intensity line scans (b), and ordered heavy elements segregate at stacking faults and the corresponding atomic-level EDS mapping (c)

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