Observations of {212} 〈110〉 slip system in face centered cubic austenitic stainless steel

1976 ◽  
Vol 10 (1) ◽  
pp. 19-24 ◽  
Author(s):  
R.T. Bhatr ◽  
P.A. Thrower ◽  
W.R. Bitler
Keyword(s):  
Stainless Steel ◽  
Austenitic Stainless Steel ◽  
Slip System ◽  
Face Centered Cubic ◽  
Face Centered

Critical factors that determine face-centered cubic to body-centered cubic phase transformation in sputter-deposited austenitic stainless steel films

2004 ◽  
Vol 19 (6) ◽  
pp. 1696-1702 ◽  
Author(s):  
X. Zhang ◽  
A. Misra ◽  
R.K. Schulze ◽  
C.J. Wetteland ◽  
H. Wang ◽  
...  
Keyword(s):  
Thin Films ◽  
Stainless Steel ◽  
Austenitic Stainless Steel ◽  
Phase Stability ◽  
Cubic Phase ◽  
Face Centered Cubic ◽  
Body Centered Cubic ◽  
Bcc Structure ◽  
Face Centered ◽  
Sputter Deposited

Bulk austenitic stainless steels (SS) have a face-centered cubic (fcc) structure. However, sputter deposited films synthesized using austenitic stainless steel targets usually exhibit body-centered cubic (bcc) structure or a mixture of fcc and bcc phases. This paper presents studies on the effect of processing parameters on the phase stability of 304 and 330 SS thin films. The 304 SS thin films with in-plane, biaxial residual stresses in the range of approximately 1 GPa (tensile) to approximately 300 MPa (compressive) exhibited only bcc structure. The retention of bcc 304 SS after high-temperature annealing followed by slow furnace cooling indicates depletion of Ni in as-sputtered 304 SS films. The 330 SS films sputtered at room temperature possess pure fcc phase. The Ni content and the substrate temperature during deposition are crucial factors in determining the phase stability in sputter deposited austenitic SS films.

Stacking Faults in a High Nitrogen Face-Centered-Cubic Phase Formed on Nitrogen-Modified Austenitic Stainless Steel

2008 ◽  
Vol 373-374 ◽  
pp. 318-321
Author(s):  
J. Liang ◽  
M.K. Lei
Keyword(s):  
Stainless Steel ◽  
Plasma Source ◽  
Peak Shift ◽  
Cubic Phase ◽  
Face Centered Cubic ◽  
X Ray Diffraction ◽  
High Nitrogen ◽  
X Ray ◽  
Peak Asymmetry ◽  
Face Centered

Effects of stacking faults in a high nitrogen face-centered-cubic phase (γΝ) formed on plasma source ion nitrided 1Cr18Ni9Ti (18-8 type) austenitic stainless steel on peak shift and peak asymmetry of x-ray diffraction were investigated based on Warren’s theory and Wagner’s method, respectively. The peak shift from peak position of the γΝ phase is ascribed to the deformation faults density α, while the peak asymmetry of the γΝ phase is characterized by deviation of the center of gravity of a peak from the peak maximum (Δ C.G.) due to the twin faults density β. The calculated peak positions of x-ray diffraction patterns are consistent with that measured for plasma source ion nitrided 1Cr18Ni9Ti stainless steel.

Stress Corrosion and Hydrogen Cracking off 17-7 Stainless Steel

CORROSION ◽  
1966 ◽  
Vol 22 (1) ◽  
pp. 23-27 ◽  
Author(s):  
I. MATSUSHIMA ◽  
D. DEEGAN ◽  
H. H. UHLIG
Keyword(s):  
Stainless Steel ◽  
Stress Corrosion ◽  
Stress Corrosion Cracking ◽  
Corrosion Cracking ◽  
Face Centered Cubic ◽  
Hydrogen Cracking ◽  
Pure Phase ◽  
Face Centered ◽  
As Stress ◽  
Mgcl2 Solution

Abstract Whether a stainless steel fails by stress corrosion cracking or by hydrogen cracking depends on its structure. A pure ferritic 18–8, body-centered cubic as quenched, fails by hydrogen cracking when cathodically polarized in dilute sulfuric acid containing arsenic trioxide. However, it is resistant to stress corrosion cracking in MgCl2 solution boiling at 154 C (310 F). A similar composition austenitic 18–8, face-centered cubic as quenched and tested similarly is resistant to hydrogen cracking but fails by stress corrosion cracking. Type 301 austenitic 17–7 stainless steel, which transforms in part to ferrite on cold rolling, is resistant, therefore, to hydrogen cracking as annealed-quenched or slightly cold reduced. It fails within 10–30 minutes when cold reduced more than 20 percent even though it transforms only partially to ferrite. In MgCl2 solution, both the annealed-quenched and the cold-reduced alloy fail, cracking times being prolonged by cathodic polarization, characterizing the failures as stress corrosion cracking. Contrary to reactions observed in pure phase alloys, stainless steels containing mixtures of austenite and ferrite may fail either by hydrogen cracking or by stress corrosion cracking, depending on the environment.

EBSD-AFM Hybrid Analysis of Crack Initiation in Stainless Steel under Fatigue Loading

2007 ◽  
Vol 340-341 ◽  
pp. 531-536 ◽  
Author(s):  
Yun Wang ◽  
Hidehiko Kimura ◽  
Yoshiaki Akiniwa ◽  
Keisuke Tanaka
Keyword(s):  
Stainless Steel ◽  
Crack Initiation ◽  
Fatigue Crack Initiation ◽  
Fatigue Loading ◽  
Face Centered Cubic ◽  
Slip Planes ◽  
Schmid Factor ◽  
Slip Displacement ◽  
Face Centered ◽  
Active Slip

Both EBSD and AFM methods were used to investigate the active slip systems and fatigue crack initiation behavior in face-centered cubic polycrystalline metal, austenitic stainless steel, SUS316NG, under cyclic torsional loading. Most active slip planes are the primary slip planes having the largest Schmid factor. Grains with slip band cracks or transcrystalline cracks have larger Taylor's factors. On the basis of EBSD and AFM observations, h, the depth of intrusion vertical to the surface, S, and the component of the slip displacement perpendicular to the surface trace, SB, showed a sharp increase at the onset of crack initiation. The critical value of SB at crack initiation was 170 nm.

Bulk nanocrystalline stainless steel fabricated by equal channel angular pressing

2006 ◽  
Vol 21 (7) ◽  
pp. 1687-1692 ◽  
Author(s):  
C.X. Huang ◽  
Y.L. Gao ◽  
G. Yang ◽  
S.D. Wu ◽  
G.Y. Li ◽  
...  
Keyword(s):  
Stainless Steel ◽  
Equal Channel Angular Pressing ◽  
Face Centered Cubic ◽  
Angular Pressing ◽  
Grain Structures ◽  
Strain Induced Martensite ◽  
High Resolution Tem ◽  
Cubic Structure ◽  
Face Centered ◽  
Bulk Nanocrystalline

Bulk fully nanocrystalline grain structures were successfully obtained in ultralow carbon stainless steel by means of equal channel angular pressing at room temperature. Transmission electron microscopy (TEM) and high-resolution TEM investigations indicated that two types of nanostructures were formed: nanocrystalline strain-induced martensite (body-centered cubic structure) with a mean grain size of 74 nm and nanocrystalline austenite (face-centered cubic structure) with a size of 31 nm characterized by dense deformation twins. The results about the formation of fully nanocrystalline grain structures in stainless steel suggested that a low stacking fault energy is exceptionally profitable for producing nanocrystalline materials by equal channel angular pressing.

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