Deformation Mechanism and Microstructure Evolution of T92/S30432 Dissimilar Welded Joint During Creep

Xu, Lianyong; Wang, Yongfa; Jing, Hongyang; Zhao, Lei; Han, Yongdian

doi:10.1007/s11665-016-2254-6

Cited by 19 publications

(5 citation statements)

References 32 publications

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“…HR3C-weld's maximum principal stress distribution trend is basically the same as T92-weld's, but the working time near the surface weld maximum principal stress does not appear to fluctuate in value, which is the reason for the stronger creep resistance [10][11] .…”

Section: Maximum Principal Stress Simulation Analysismentioning

confidence: 88%

Analysis of the Creep Failure of P92/HR3C Dissimilar Steel Welded Joint

Li,

Liu,

et al. 2023

J. Phys.: Conf. Ser.

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Harsh service environments, such as high temperature and pressure, cause many unforeseen premature failures, especially for welded joint structures, whose heat-affected zones have been in service. Cases of pressure vessel damage caused by premature cracking in the process often occur. In this paper, the finite element model of dissimilar welded joints of P92/HR3C steel was established to simulate the actual service process, and the variation law of maximum principal stress, equivalent stress, and stress triaxiality on the inner and outer surfaces of the joint and both sides of the welding were analyzed. The results show that in the long-term use of welded joints, the stress concentration occurs in the weld fusion zone; with the increase in service time, the creep strength of the HR3C weld interface is much higher than the P92 weld interface, the structural shape changes and the stress concentration is transferred from the HR3C-weld to the P92-weld.

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Section: Maximum Principal Stress Simulation Analysismentioning

confidence: 88%

Analysis of the Creep Failure of P92/HR3C Dissimilar Steel Welded Joint

Li,

Liu,

et al. 2023

J. Phys.: Conf. Ser.

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“…As shown in Figure 4, the HAZ and BM hardness decreased considerably after PWHT at 788 • C as a result of sufficient tempering at high temperature (much higher than tempering temperature of the BM). Therefore, PWHT at 788 • C decreases the creep strength of 10% Cr steel, and the fracture mechanism of the ductile failure controlled by plastic deformation is expected to be applied as same as that creep failure under higher applied stress [15,[34][35][36].…”

Section: Creep and Rupture Behavior For Various Pwht Conditionsmentioning

confidence: 99%

Effect of Postweld Heat Treatments on Type IV Creep Failure in the Intercritical Heat-Affected Zone of 10% Cr Martensitic Steel Welded with Haynes 282 Filler

Kim

Kang

Bang

et al. 2021

Metals

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This study investigated the effect of postweld heat treatment (PWHT) conditions on Type IV failure behavior of 10% Cr martensitic steel welds using Haynes 282 filler. The welded joints were subjected to PWHT at temperatures of 688, 738, and 788 °C for 4 and 8 h. Creep tests were carried out at 600 °C under a stress of 200 MPa. The as-welded joint without PWHT showed Type IV cracking due to growth of voids around Laves phase by localized creep deformation in the intercritical heat-affected zone (ICHAZ). The creep properties of the PWHTed joints at 688 °C were similar to those of the as-welded joints without PWHT. On the other hand, the PWHTed joints at 738 °C exhibited a significantly longer creep life by a lower amount of Laves phase in the ICHAZ than those at 688 °C; this could be a result of the homogenization of ICHAZ microstructure during PWHT at 738 °C. However, the PWHT at 688 and 738 °C showed the same Type IV creep failure mode. Meanwhile, the PWHTed joints at 788 °C exhibited the shortest creep life in this study. The failure location was shifted to the base metal away from the HAZ, and severe plastic deformation occurred due to the softened matrix by excessive tempering.

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“…It has been shown that the most critical zone of the weldment after thermal aging is the interfacial region T92 BM/Ni WM [14]. There are many studies on the creep behavior of martensitic/austenitic dissimilar weld joints between T92 steel and austenitic heat resistant steels (e.g., AISI 304 or 347 grades) [7,[54][55][56]. It has been frequently observed that the final fracture location after creep exposure was located mainly at the T92 weld part within its fine grained heat-affected zone [7,[54][55][56].…”

Section: Fracture Behaviormentioning

confidence: 99%

“…There are many studies on the creep behavior of martensitic/austenitic dissimilar weld joints between T92 steel and austenitic heat resistant steels (e.g., AISI 304 or 347 grades) [7,[54][55][56]. It has been frequently observed that the final fracture location after creep exposure was located mainly at the T92 weld part within its fine grained heat-affected zone [7,[54][55][56]. As it was observed by Falat et al [11][12][13], the quenching-and-tempering post weld treatment (QT PWHT) of the investigated T92/TP316H dissimilar weldments led to microstructural homogenization of welded base materials.…”

Section: Fracture Behaviormentioning

confidence: 99%

The Effects of Electrochemical Hydrogen Charging on Room-Temperature Tensile Properties of T92/TP316H Dissimilar Weldments in Quenched-and-Tempered and Thermally-Aged Conditions

Ševc

Falat

Čiripová

et al. 2019

Metals

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The influence of isothermal aging at 620 °C in combination with subsequent electrochemical hydrogen charging at room-temperature was studied on quenched-and-tempered T92/TP316H martensitic/austenitic weldments in terms of their room-temperature tensile properties and fracture behavior. Hydrogen charging of the weldments did not significantly affect their strength properties; however, it resulted in considerable deterioration of their plastic properties along with significant impact on their fracture characteristics and failure localization. The hydrogen embrittlement plays a dominant role in degradation of the plastic properties of the weldments already in their initial material state, i.e., before thermal aging. After thermal aging and subsequent hydrogen charging, mutual superposition of thermal and hydrogen embrittlement phenomena had led to clearly observable effects on the welds deformation and fracture processes. The measure of hydrogen embrittlement was clearly lowered for thermally aged material state, since the contribution of thermal embrittlement to overall degradation of the weldments has dominated. The majority of failures of the weldments after hydrogen charging occurred in the vicinity of T92 BM/Ni weld metal (WM) fusion zone; mostly along the Type-II boundary in Ni-based weld metal. Thus, regardless of aging exposure, the most critical failure regions of the investigated weldments after hydrogen charging and tensile straining at room temperature are the T92 BM/Ni WM fusion boundary and Type-II boundary acting like preferential microstructural sites for hydrogen embrittling effects accumulation.

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Deformation Mechanism and Microstructure Evolution of T92/S30432 Dissimilar Welded Joint During Creep

Cited by 19 publications

References 32 publications

Analysis of the Creep Failure of P92/HR3C Dissimilar Steel Welded Joint

Analysis of the Creep Failure of P92/HR3C Dissimilar Steel Welded Joint

Effect of Postweld Heat Treatments on Type IV Creep Failure in the Intercritical Heat-Affected Zone of 10% Cr Martensitic Steel Welded with Haynes 282 Filler

The Effects of Electrochemical Hydrogen Charging on Room-Temperature Tensile Properties of T92/TP316H Dissimilar Weldments in Quenched-and-Tempered and Thermally-Aged Conditions

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