Effect of microstructure of simulated heat‐affected zone on low‐ to high‐cycle fatigue properties of low‐carbon steels

Nishikawa, Hideaki; Furuya, Yasubumi; Igi, Satoshi; Goto, Sota; Briffod, Fabien; Shiraiwa, Takayuki; Enoki, Manabu; Kasuya, Tadashi

doi:10.1111/ffe.13217

Cited by 15 publications

(10 citation statements)

References 35 publications

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“…One alternative is to use thermal simulation for each sub-HAZ to assess individual performance. 18,19 Although thermal simulation methods have been widely used to study the microstructure and mechanical properties of the HAZ, 20,21 reports on the fatigue performance of the HAZ mainly focused on the properties of the overall welded joint, 22,23 and little work has been done to investigate the fatigue properties of each sub-HAZ in an X80 pipeline, especially in terms of fatigue crack growth. 24 In addition, the performance of ICHAZ has been rarely reported.…”

Section: Introductionmentioning

confidence: 99%

Research on the fatigue properties of sub‐heat‐affected zones in X80 pipe

Qiao

Wang

et al. 2020

Fatigue Fract Eng Mat Struct

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Pipeline transmission is an essential means of oil and gas transportation, but its safety is threatened by fatigue fracture that generally occurs in the heat-affected zone (HAZ) adjacent to welded joints of the pipeline. Therefore, it is important to determine the fatigue properties of HAZ. In this work, the microstructure and mechanical properties in the HAZ of a X80 pipe were accurately simulated by thermal simulation. The fatigue life and crack growth rate of typical sub-HAZ were tested. The results showed that fine grain HAZ exhibited the lowest strength and fatigue life. In contrast, coarse grain HAZ had the highest strength, but its fatigue life was lower than that of the intercritical HAZ. The microstructure of each sub-HAZ and the effect of this structure on fatigue properties were analysed and discussed in detail. The results provide insight into the effects of microstructure and mechanical properties on the service safety of pipeline transportation.

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Section: Introductionmentioning

confidence: 99%

Research on the fatigue properties of sub‐heat‐affected zones in X80 pipe

Qiao

Wang

et al. 2020

Fatigue Fract Eng Mat Struct

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“…The same issues were also reported in other studies. [8,10,15,34] Figure 7 shows the crack density as a function of the number of cycles for three different stress amplitudes. The crack density rises in all three cases with increasing number of cycles, indicating an accelerating fatigue damage evolution with increasing N and Δσ/2.…”

Section: Resultsmentioning

confidence: 99%

“…[7][8][9][10][11] The observed slip band formation occurred primarily near and along PAGBs. This result is in good agreement with the studies by Nishikawa et al, Batista et al, and Krupp et al, [10,11,14] which also reported a slip band formation at PAGBs. Apart from PAGBs, block boundaries are also cited as slip band formation sites.…”

Section: Discussionmentioning

confidence: 99%

“…[11][12][13] It seems that those slip bands do not cross microstructural interfaces with a high-angle boundary like packet boundaries or prior austenite grain boundaries (PAGBs). [10,13,14] Hence, the crack initiation and early short crack propagation in martensitic steels seem to occur mainly intergranularly at PAGBs [11,12,14,15] or block boundaries, [11,16] although in some studies, transgranular crack initiation and early short crack propagation were also observed. [9,13] In many studies, the preferential alignment of carbides along microstructural interfaces is cited as a possible reason for intergranular crack initiation and early short crack propagation.…”

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confidence: 99%

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Characterizing the Fatigue Damage in a Martensitic Spring Steel

Wildeis

Christ

Brandt

et al. 2021

steel research int.

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Many technical components are subjected to uniaxial cyclic loading in the high cycle fatigue regime. The resulting fatigue damage evolution is commonly subdivided into four stages, i.e., crack initiation, short crack propagation, long crack propagation, and eventually failure. Especially, the stages of crack initiation and short crack propagation can account for up to 90% of the fatigue life in the high cycle fatigue regime, leading to a particular interest in investigating these stages of fatigue damage evolution. [1] Furthermore, it is extremely important to understand the mechanisms of crack initiation and short crack propagation for lifetime predictions of structures which are not fail safe, as their failure can cause a catastrophic damage.Many studies have shown, that crack initiation often occurs at slip bands (see for example, the studies by Christ, McEvily, Efthymiadis et al., and Hong et al. [1][2][3][4] ) and that short crack propagation is strongly influenced by the local microstructure, leading to an oscillating crack propagation rate (see for example, the studies by Christ, McEvily, Miller, and Yang et al. [1,2,5,6] ). However, until now, just a few studies have investigated the fatigue damage evolution in a martensitic steel and the corresponding impact of the complex martensitic microstructure on the crack initiation and the short crack propagation. The crack initiation in martensitic steels seems to occur often at slip bands, [7][8][9][10][11] which mainly arise at microstructural interfaces and are oriented parallel to martensitic laths. [11][12][13] It seems that those slip bands do not cross microstructural interfaces with a high-angle boundary like packet boundaries or prior austenite grain boundaries (PAGBs). [10,13,14] Hence, the crack initiation and early short crack propagation in martensitic steels seem to occur mainly intergranularly at PAGBs [11,12,14,15] or block boundaries, [11,16] although in some studies, transgranular crack initiation and early short crack propagation were also observed. [9,13] In many studies, the preferential alignment of carbides along microstructural interfaces is cited as a possible reason for intergranular crack initiation and early short crack propagation. [7,14,17,18] In addition, intergranular crack initiation can be explained by the impingement of slip bands on grain boundaries [14,19,20] or the anisotropic elastic and plastic properties of the grains. [11,12,15,[21][22][23] The number of slip bands formed and cracks initiated rises with increasing number of cycles and with increasing stress amplitude. [4,8,9,13,24] The subsequent short crack propagation seems to be strongly influenced by the local microstructure, whereby a short crack propagation parallel to the martensitic laths is often observed. [8,24,25] PAGBs [6,8,14,24,26] and block boundaries [6,7,26] seem to act as obstacles for short crack propagation, leading to an oscillating short crack propagation rate. An often referred explanation for the barrier effect of microstructural interfaces is the...

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“…The performance testing of each sub-HAZ is hindered due to their small areas. Thermal simulation can be used for each sub-HAZ to test their individual performance 18,19 . Although thermal simulation methods have been widely used to study the microstructure and mechanical properties of the HAZ 20,21 , reports on the fatigue performance of the HAZ mainly focused on the overall weld joint 22,23 .…”

Section: Introductionmentioning

confidence: 99%