The influence of strain rate on the microstructure transition of 304 stainless steel

Chen, A. Y.; Ruan, Haihui; Wang, J.; Chan, Ho Lam; Wang, Q.; Li, Quan; J, Lu

doi:10.1016/j.actamat.2011.03.005

Cited by 274 publications

(122 citation statements)

References 44 publications

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“…10 shows the indexed SADP, comprised of γ, T, and ε, with the zone axis of [110] γ //[011] T //[1120] ε . The orientation relationship of the newly nucleated ε-martensite with the γ and twin, observed here, agreed with the measurements on stainless steel deformed by SMAT (Chen et al, 2011), and fatigued at low temperature (Kruml et al, 2000), which is known as the S-N (ShojiNichiyama) relationship between fcc and hcp lattices. is imaged by the diffraction spots as marked in Fig.…”

Section: Microstructural Evolution In the Absp Specimensupporting

confidence: 78%

“…18A. Formation of ε-martensite is usually observed in deformed austenitic stainless steel with low SFE (Lee & Lin, 2000;Nakada et al, 2010;Chen et al, 2011), and that may suggest a path for the formation of the α'-martensite, namely, γεα' instead of γα' directly (Xue et al, 2007;Chen et al, 2011). At shallower depths the SB begin to form (state 5 of Fig.…”

Section: Microstructural Refinement Mechanismmentioning

confidence: 99%

“…peened and severely deformed stainless steel (Lee & Lin, 2000;Nakada et al, 2010;Chen et al, 2011). However, XRD shows no evidence of the ε-martensite transformation in the shot peened specimens, which is ascribed to the low volume of the ε-martensite.…”

Section: Fig 2 Andmentioning

confidence: 99%

“…This is related to the introduction of low angle grain boundaries, increase of grain misorientation, turning to high angle grain boundaries with random misorientation, followed by sub-division of the original coarse grain into an even smaller one (Liu & Lu, 2000;Zhang et al, 2003). Chen et al (2011) reported the nucleation of the strain induced ε-and α'-martensite transformation as well as a deformation mechanism of the γDT, γε, and γα' depending on the calculated strain rate. An interesting deformation microstructure was the formation of a third-directional DT which cut the two-directional DT-DT intersections.…”

Section: Introductionmentioning

confidence: 99%

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Microstructural Characterization of SS304 upon Various Shot Peening Treatments

Cho

et al. 2015

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Plastic deformation was introduced to the austenitic (γ) stainless steel of SS304 by air blast shot peening, ultrasonic shot peening, and ultrasonic nanocrystalline surface modification. Various deformation structures were formed. The hardness, the deformation structure and the underlying grain refinement mechanism were investigated. In the deformed region, planar dislocation arrays and deformation twin (DT), the DT-DT intersection and ε-martensite structures, and α'-martensite were formed in the respective regions of low, medium, and high strain. The grain refinement mechanism is found to be closely related to the 1) sub-division of coarse grains by DT, shear bands and their intersection, and 2) formation of nano-sized α'-martensite due to the high plastic deformation.

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Section: Microstructural Evolution In the Absp Specimensupporting

confidence: 78%

Section: Microstructural Refinement Mechanismmentioning

confidence: 99%

Section: Fig 2 Andmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Microstructural Characterization of SS304 upon Various Shot Peening Treatments

Cho

et al. 2015

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“…Thus, conventional dislocation glide and the formation of dislocation cells are only observed on glide systems, where the trailing partial experiences a higher force than the leading partial. [19,20] Plastic deformation proceeds mainly in narrowly spaced deformation bands, which consist of SFs, dislocations, or twins of nanometer size. [21] Because of a high density of SFs in the deformation bands of the austenite, hexagonal areas are formed, which appear as hcp phase (e-martensite) in X-ray diffraction experiments or in TEM and EBSD investigations.…”

Section: Introductionmentioning

confidence: 99%

Deformation Mechanisms in Austenitic TRIP/TWIP Steel as a Function of Temperature

Martin

Wolf

Martin

et al. 2014

Metall Mater Trans A

243

106

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A high-alloy austenitic CrMnNi steel was deformed at temperatures between 213 K and 473 K (À60°C and 200°C) and the resulting microstructures were investigated. At low temperatures, the deformation was mainly accompanied by the direct martensitic transformation of c-austenite to a¢-martensite (fcc fi bcc), whereas at ambient temperatures, the transformation via emartensite (fcc fi hcp fi bcc) was observed in deformation bands. Deformation twinning of the austenite became the dominant deformation mechanism at 373 K (100°C), whereas the conventional dislocation glide represented the prevailing deformation mode at 473 K (200°C). The change of the deformation mechanisms was attributed to the temperature dependence of both the driving force of the martensitic c fi a¢ transformation and the stacking fault energy of the austenite. The continuous transition between the e-martensite formation and the twinning could be explained by different stacking fault arrangements on every second and on each successive {111} austenite lattice plane, respectively, when the stacking fault energy increased. A continuous transition between the transformation-induced plasticity effect and the twinninginduced plasticity effect was observed with increasing deformation temperature. Whereas the formation of a¢-martensite was mainly responsible for increased work hardening, the stacking fault configurations forming e-martensite and twins induced additional elongation during tensile testing.

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