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Acta Metall Sin  2019, Vol. 55 Issue (8): 997-1007    DOI: 10.11900/0412.1961.2018.00428
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Study on the Evolution of Residual Stress During Ageing Treatment in a GH4169 Alloy Disk
Hailong QIN,Ruiyao ZHANG,Zhongnan BI(),Lee Tung Lik,Hongbiao DONG,Jinhui DU,Ji ZHANG
1. Beijing Key Laboratory of Advanced High Temperature Materials, Central Iron and Steel Research Institute, Beijing 100081, China
2. CISRI-GAONA Co. , Ltd. , Beijing 100081, China
3. Department of Engineering, University of Leicester, Leicester, LE1 7RH, UK
4. ISIS Neutron Source, Rutherford Appleton Laboratory, Harwell Oxford, Didcot, OX11 0QX, UK
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Abstract  

GH4169 alloy, a precipitation-strengthened nickel-iron base superalloy, has been widely used in aerospace and energy industries due to its excellent high-temperature strength which derived from the coherent phases (γ″ and γ'). To form these precipitates, the manufacturing process of GH4169 usually involves solid solution heat treatment followed by rapid cooling and double ageing heat treatment. Significant residual stresses are induced during rapid cooling and then partially relieved during the subsequent ageing treatment. However, the reduced residual stress after ageing are still large enough to affect the final machining operations, resulting in the component exceeding the dimensional tolerances if they are not well considered. Furthermore, residual stresses in the final components may lead to further distortion beyond estimation during service, which could deteriorate the engine performances. In the present study, the evolution of residual stresses at heating, isothermal ageing, and air-cooling stages of ageing heat treatment in a GH4169 alloy disk was characterized by in situ neutron diffraction. Considering the effect of residual stresses on the precipitation behavior of γ″, two different types of stress-free samples were used as the basis for the stress analysis. The results show that significant residual stresses were induced during water quenching, which were found to be 340.62 MPa tensile in hoop/radial directions and 33.34 MPa compressive in axial direction in the center of the disk. Subsequently, an in situ ageing heat treatment was undertaken at 720 ℃ for 8 h. During the heating stage, the yield strength of the material decreases with increasing temperature, leading to residual stress relaxation through plastic deformation from 340.62 MPa to 227.67 MPa in hoop/radial direction in the disk center. At the isothermal ageing stage, residual stresses relieved apparently by about 40 MPa during the first 100 min, later on a slower linear relaxation remained for the rest of the ageing heat treatment. The strength of the alloy increased and the creep rate decreased due to the formation of γ″ and γ′ strengthening phases, indicating that most of stress relaxation occurred as a result of creep deformation at the early stage of isothermal ageing. The magnitude of residual stress was almost invariable in the subsequent air-cooling stage.

Key words:  superalloy      ageing treatment      residual stress      in situ neutron diffraction     
Received:  07 September 2018     
ZTFLH:  TG115.23  
Fund: Supported by National Key Research and Development Program of China((No.2017YFB0702901));National Natural Science Foundation of China((No.U1708253))
Corresponding Authors:  Zhongnan BI     E-mail:  bizhongnan21@aliyun.com

Cite this article: 

Hailong QIN,Ruiyao ZHANG,Zhongnan BI,Lee Tung Lik,Hongbiao DONG,Jinhui DU,Ji ZHANG. Study on the Evolution of Residual Stress During Ageing Treatment in a GH4169 Alloy Disk. Acta Metall Sin, 2019, 55(8): 997-1007.

URL: 

https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00428     OR     https://www.ams.org.cn/EN/Y2019/V55/I8/997

Fig.1  In situ neutron diffraction experiment during ageing treatment(a) heating by ceramic blanket under clad insulation (b) covering by heat-preservation cotton
Fig.2  Schematic of neutron path and location for neutron diffraction
Fig.3  Schematic of stress-free s0 sample
Fig.4  Temperature profile of the disk during in situ heating experiment
Fig.5  OM (a) and SEM (b) images of the microstructures of disk after quenching
Fig.6  TEM bright-field images of s0-1 (a, b), s0-2 (c) and s0-5 (d) samples aged for 0.5 h (a, c) and 8 h (b, d)

Temperature

Direction

a / nmStrain / 10-6Stress / MPa
ValueErrorValueErrorValueError

20

Hoop/Radial0.3607680.00000751251.6820.82340.6210.01
Axial0.3598960.0000072-1168.4219.98-33.349.88

340

Hoop/Radial0.3624510.00000851373.1023.48321.859.28
Axial0.3614860.0000079-1292.9821.83-60.709.04

530

Hoop/Radial0.3634920.00000911315.1125.07289.739.33
Axial0.3625500.0000085-1279.6922.59-65.718.99

720

Hoop/Radial0.3644280.00001011165.9927.75227.6710.38
Axial0.3635020.0000088-1351.9624.18-77.749.94
Table 1  Evolution of lattice parameter (a), strain and corresponding residual stress during the heating process
Fig.7  Profiles of a in the center of disk during isothermal ageing process
Fig.8  Evolution of residual stress in the center of disk during isothermal ageing process on the basis of dynamic non-stress standard sample (a) and static non-stress standard sample (b)
Fig.9  Evolution of residual stress in the center of disk during ageing treatment
Fig.10  Neutron diffraction spectra at the beginning (5 min) and the end (480 min) of creep test in longitudinal direction (a), and the separation of overlapped peak (200) (b)
Fig.11  Evolution of stress fitting error with increasing ageing time
Fig.12  Yield strength of as-quenched materials vs temperature
Fig.13  Evolution of microstructure and mechanical properties of GH4169 alloy during isothermal aging treatment(a) volume fraction of γ″ and γ(b) average diameter of γ″ and γ(c) yield strength at room temperature(d) creep strain of as-quenched GH4169 alloy at 720 ℃
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