Fractography of hydrogen-embrittled stainless steel

Caskey, G.R.

doi:10.1016/0036-9748(77)90311-8

Cited by 39 publications

(20 citation statements)

References 10 publications

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“…Our observation of the straininduced α' martensite on the prior annealed-twin boundary by MFM is consistent with the SEM observation of the traces on a prior annealed-twin boundary by Caskey. 27) IRHE is still observed even at 150 K. SEM images of the fracture surfaces of the H-charged and as-solution-annealed 316-3 specimens are shown in Figs. 8(a) and 8(b), respectively.…”

Section: Resultsmentioning

confidence: 98%

“…6(a). Caskey 27) observed fracture along the prior annealed-twin boundary in thermally hydrogencharged type 304L specimen fractured at 198 K. It was observed by HVEM that α' martensite was located along the fracture surface and in front of the crack tip in type 304 stainless steel 53) and type 316 stainless steel. 54) Recently, Miller et al 59) found that α' martensite formed along the crack tip of type 316L stainless steel in a fatigue crack growth test by MFM.…”

Section: Resultsmentioning

confidence: 99%

“…8,11,[16][17][18][19][20][21] The IRHE of stable austenitic stainless steels, in which no strain-induced α' martensitic transformation occurs during deformation, can be attributed to the low stacking-fault energy of the steels, which inhibits the occurrence of cross slips and induces slip planarity. 22,23) Metastable austenitic stainless steels such as type 301, 304 and 316 stainless steels exhibit IRHE [5][6][7][8][9][10][11][12]15,[24][25][26][27][28][29][30][31][32][33][34][35][36][37][38] as well as HGE 8,9,11,[16][17][18][19][20][21][39][40][41][42][43][44]…”

Section: Introductionmentioning

confidence: 99%

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Internal Reversible Hydrogen Embrittlement of Austenitic Stainless Steels Based on Type 316 at Low Temperatures

Zhang

Imade

et al. 2012

ISIJ Int.

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The internal reversible hydrogen embrittlement (IRHE) of austenitic Fe(10-20)Ni17Cr2Mo alloys based on type 316 stainless steels hydrogen-charged to around 40 mass ppm was investigated by performing tensile tests using the slow strain rate technique at temperatures from 80 to 300 K. The susceptibility to IRHE depended on the Ni content. IRHE occurred below a Ni content of 15% (Ni equivalent of 29%), increased with decreasing temperature, reached a maximum at 200 K and decreased with further decreasing temperature. Hydrogen-induced fracture due to IRHE occurred in brittle transgranular mode associated with the strain-induced α' martensite structure at temperatures from 200 to 300 K and occurred simultaneously with fracture along the prior annealed-twin boundary at 200 and 250 K, then changed to dimple rupture mode due to hydrogen localization at 150 K. IRHE was controlled by the amount of strain-induced α' martensite above 200 K, whereas it was controlled by hydrogen diffusion below 200 K.KEY WORDS: stainless steel; hydrogen embrittlement; nickel; low temperature deformation; slow strain rate technique.

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Section: Resultsmentioning

confidence: 98%

Section: Resultsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Internal Reversible Hydrogen Embrittlement of Austenitic Stainless Steels Based on Type 316 at Low Temperatures

Zhang

Imade

et al. 2012

ISIJ Int.

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“…31,32) It has been reported that for an austenitic AISI 310 type stainless steel, H-charging leads to a reduction of ductility without a change of the appearance of the fracture surface which still appears to be have the characteristic dimpled surface of a ductile fracture mode. This has been explained by the trapping of H by inclusions and microvoids.…”

Section: Discussionmentioning

confidence: 99%

Mechanical Properties of H-charged Fe^|^ndash;18Mn^|^ndash;1.5Al^|^ndash;0.6C TWIP Steel

2012

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The effect of H on the mechanical properties of a high Mn twinning-induced plasticity steel was evaluated by comparing the properties of H-free and H-charged tensile specimens deformed at different temperatures prior to H-charging. The H-charging resulted in a reduction of the total elongation. The fracture surface of the tested samples revealed an inhomogeneous fracture appearance with an intergranular fracture in the range of 10 μ m to 20 μ m below the sample surface. The observations strongly suggest that it is this intergranular fracture in the surface layer which is the cause of the reduction of elongation in Hcharged TWIP steel.

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“…[5,6] Reference 5 reported the following key parameters that control fracture mode for stainless steels: a) Dimpled rupture is reported to be the primary mode of failure due to hydrogen, though the ductility may be low. However, dimple sizes change with a change in the yield stress of the materials.…”

Section: Fracture Modesmentioning

confidence: 99%

Microstructural Features Affecting Properties and Aging of Tritium-Exposed Austentic Stainless Steel

Subramanian¹,

Morgan²

2004

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Fractography of hydrogen-embrittled stainless steel

Cited by 39 publications

References 10 publications

Internal Reversible Hydrogen Embrittlement of Austenitic Stainless Steels Based on Type 316 at Low Temperatures

Internal Reversible Hydrogen Embrittlement of Austenitic Stainless Steels Based on Type 316 at Low Temperatures

Mechanical Properties of H-charged Fe^|^ndash;18Mn^|^ndash;1.5Al^|^ndash;0.6C TWIP Steel

Microstructural Features Affecting Properties and Aging of Tritium-Exposed Austentic Stainless Steel

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