Fatigue characteristics of a type 304 austenitic stainless steel in hydrogen gas environment

Aoki, Yuta; Kawamoto, Kyohei; Oda, Yasuji; Noguchi, Hiroshi; Higashida, Kenji

doi:10.1007/s10704-005-4942-3

Cited by 38 publications

(21 citation statements)

References 11 publications

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“…It is well known that the more stable the γ phase, the less the material is sensitive to hydrogen in the static tensile mode. On the other hand, there are some reports on the fatigue characteristics of austenitic stainless steels in a hydrogen environment including our reports (14), (15), (19), (20) . They reported the findings concerning fatigue crack growth (FCG) acceleration, the effects of the stability of the γ phase on the degree of the acceleration, increasing of a brittle faceted area and so on.…”

Section: Introductionmentioning

confidence: 73%

“…The testing apparatus used in this study is a system in which the fatigue test can be performed in a gas environment including a hydrogen gas environment (20) . This system consists of three parts; a testing machine for plain bending fatigue, an environmental chamber and an optical microscope for in-situ observation.…”

Section: Testing Systemmentioning

confidence: 99%

“…Figure 3 shows that the FCG diagram in the total strain range ∆ε t =0.49%. ∆ε t =0.49% was chosen as a representative value for the relatively high FCG rate (20) . One test in hydrogen was carried out using a specimen, which was exposed to the hydrogen gas (pressure; 1.0MPa, temperature; 393K, time; 100hours) before the fatigue test.…”

Section: Effects Of Hydrogen Environment On Fatigue Crack Growth Ratementioning

confidence: 99%

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Effects of a Hydrogen Gas Environment on Fatigue Crack Growth of a Stable Austenitic Stainless Steel

Kawamoto

Oda

Nishikawa

et al. 2007

JMMP

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In order to clarify the effects of a hydrogen gas environment on the fatigue crack growth characteristics of stable austenitic stainless steels, bending fatigue tests were carried out in a hydrogen gas, in a nitrogen gas at 1.0 MPa and in air on a SUS316L using the Japanese Industrial Standards (type 316L). Also, in order to discuss the difference in the hydrogen sensitivity between austenitic stainless steels, the fatigue tests were also carried out on a SUS304 using the Japanese Industrial Standards (type 304) metastable austenitic stainless steel as a material for comparison. The main results obtained are as follows. Hydrogen gas accelerates the fatigue crack growth rate of type 316L. The degree of the fatigue crack growth acceleration is low compared to that in type 304. The fracture surfaces of both the materials practically consist of two parts; the faceted area seemed to be brittle and the remaining area occupying a greater part of the fracture surface and seemed to be ductile. The faceted area does not significantly contribute to the fatigue crack growth rate in both austenitic stainless steels. The slip-off mechanism seems to be valid not only in air and in nitrogen, but also in hydrogen. Also, the main cause of the fatigue crack growth acceleration of both materials occurs by variation of the slip behaviour. The difference in the degree of the acceleration, which in type 316L is lower than in type 304, seems to be caused by the difference in the stability of the γ phase.

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Section: Introductionmentioning

confidence: 73%

Section: Testing Systemmentioning

confidence: 99%

Section: Effects Of Hydrogen Environment On Fatigue Crack Growth Ratementioning

confidence: 99%

See 1 more Smart Citation

Effects of a Hydrogen Gas Environment on Fatigue Crack Growth of a Stable Austenitic Stainless Steel

Kawamoto

Oda

Nishikawa

et al. 2007

JMMP

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“…With the testing apparatus used in this study, the fatigue test can be performed in a gas environment (2) . This apparatus mainly consists of three parts; a testing machine for plane bending fatigue, an environmental chamber and an optical microscope for in-situ observation.…”

Section: Fatigue Testing Apparatusmentioning

confidence: 99%

Investigation of Local Hydrogen Distribution Around Fatigue Crack Tip of a Type 304 Stainless Steel with Secondary Ion Mass Spectrometry and Hydrogen Micro-Print Technique

Kawamoto

Oda

Noguchi

et al. 2009

JMMP

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In order to establish an appropriate method for measuring the local hydrogen content distribution around a fatigue crack tip in austenitic stainless steels, secondary ion mass spectrometry (SIMS) and the hydrogen micro-print technique (HMPT) were applied to a fatigue crack in a type 304 stainless steel fatigued in a hydrogen gas environment. The main results in this study are as follows. In the SIMS method, it is visualized that a high content of hydrogen exists in the plastic zone at a fatigue crack tip propagated in hydrogen gas, compared to that on a smooth area fatigued in hydrogen, though there is a measurement error based on false detection due to the edge effect regarding hydrogen in water vapor on the fatigue crack surface. On the other hand, hydrogen in the plastic zone is difficult to detect by HMPT. This is attributed to the difficulty for hydrogen atoms to be emitted from the sample in this case. To detect hydrogen, it is necessary to sputter the atoms forcibly. In addition, it is considered that to analyze the local hydrogen distribution around a fatigue crack tip with SIMS not only qualitatively but also quantitatively, reduction of the false detection due to the edge effect is necessary.

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“…The dislocation cells and wall-channels are observed near the crack tip of fatigued 316 stainless steels. [9][10][11][12] The formation of dislocation structure plays an important role in the accumulation of plastic strain during cyclic loading. When dislocation tangles are saturated, dislocations would make planar slip which could prompt the initiation and growth of fatigue crack.…”

Section: Introductionmentioning

confidence: 99%

Corrosion Fatigue Behavior of Cold-Worked 304L Stainless Steel in a Simulated BWR Coolant Environment

2009

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Fatigue crack growth tests were performed to evaluate the effect of cold work on the fatigue behavior of 304L stainless steel in the ambient air at room temperature and 300 C and in a simulated BWR coolant environment, respectively. The fatigue crack growth rates (FCGRs) for the as-received (AR) and cold-rolled specimens at room temperature were in the same range and the FCGRs obtained at 300 C in air were higher than those at room temperature. In addition, the FCGRs for the AR specimens were higher at 300 C in air compared with those for the coldrolled. The specimens tested in the water environment at 300 C showed higher corrosion fatigue crack growth rates (CFCGRs) relative to those measured in air at room temperature and 300 C. Local quasi-cleavages could account for the observation that the FCGRs in air at 300 C were faster than at room temperature. The dominant fracture features of quasi-cleavages, along with corrosion products, were observed with all the 304L specimens tested in the simulated BWR water environment, which could be related to the higher crack growth rates in the corrosive environment.

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Fatigue characteristics of a type 304 austenitic stainless steel in hydrogen gas environment

Cited by 38 publications

References 11 publications

Effects of a Hydrogen Gas Environment on Fatigue Crack Growth of a Stable Austenitic Stainless Steel

Effects of a Hydrogen Gas Environment on Fatigue Crack Growth of a Stable Austenitic Stainless Steel

Investigation of Local Hydrogen Distribution Around Fatigue Crack Tip of a Type 304 Stainless Steel with Secondary Ion Mass Spectrometry and Hydrogen Micro-Print Technique

Corrosion Fatigue Behavior of Cold-Worked 304L Stainless Steel in a Simulated BWR Coolant Environment

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