Microstructures and Corrosion Behaviors of an Austenitic Stainless Steel Strengthened by Nanotwinned Austenitic Grains

2015 ◽  
Vol 18 (4) ◽  
pp. 650-656 ◽  
Author(s):  
Fengkai Yan ◽  
Nairong Tao ◽  
Chen Pan ◽  
Li Liu
Keyword(s):  
Stainless Steel ◽  
Austenitic Stainless Steel ◽  
Corrosion Behaviors

scholarly journals Corrosion Behaviors of Super Austenitic Stainless Steel Weld Joints in the As-Welded and Post Weld Heat Treated States

2021 ◽  
Vol 59 (6) ◽  
pp. 374-383
Author(s):  
Dong min Cho ◽  
Jin-seong Park ◽  
Won Ki Jeong ◽  
Seung Gab Hong ◽  
Sung Jin Kim
Keyword(s):  
Heat Treatment ◽  
Stainless Steel ◽  
Austenitic Stainless Steel ◽  
Pitting Corrosion ◽  
Arc Welding ◽  
Sigma Phase ◽  
Inconel 625 ◽  
Gas Tungsten Arc ◽  
Corrosion Behaviors ◽  
Super Austenitic Stainless Steel

The corrosion behaviors of a combined weld (plasma, gas tungsten arc) joint in a super austenitic stainless steel pipe were investigated using a range of experimental and analytical methods. To ensure superior corrosion resistance, a Ni-based super alloy (Inconel 625) was employed as the welding material only in the gas tungsten arc welding (GTAW). Nevertheless, pitting corrosion occurred preferentially around the sigma phase which had been precipitated in the interdendritic region of the GTAW. This indicated that the Inconel 625, which has a higher pitting resistance equivalent number (PREN), became even more susceptible to pitting corrosion than the base metal (BM). The higher Fe content in the Inconel 625 due to the dilution of Fe, supplied by the leading plasma arc welding, may increase the driving force for the precipitation of sigma phase. It was also revealed that the post weld heat treatment conducted at 1050~1150 oC effectively reduced the fraction of sigma phase precipitated in the weld. Even after such heat treatment, however, pitting corrosion occurred unexpectedly in the center region of the BM. This may be due to additional precipitation of the sigma phase in the BM, caused by inadequate control of the cooling rate during heat treatment at the industrial site.

Corrosion Behavior of Austenitic and Ferritic/martensitic Steels Exposed in Supercritical Water with Dissolved Oxygen

2011 ◽  
Vol 71-78 ◽  
pp. 2916-2919 ◽  
Author(s):  
Nai Qiang Zhang ◽  
Yang Bai ◽  
Xiao Na Yuan ◽  
Bao Rang Li ◽  
Hong Xu
Keyword(s):  
Stainless Steel ◽  
Corrosion Resistance ◽  
Austenitic Stainless Steel ◽  
Dissolved Oxygen ◽  
Supercritical Water ◽  
Martensitic Steel ◽  
Martensitic Steels ◽  
Varying Thickness ◽  
Corrosion Behaviors ◽  
Xrd Studies

The corrosion behaviors of ferritic/martensitic steel P92, austenitic stainless steel TP347HFG and HR3C have been investigated in supercritical water (SCW) at 550°C under 25MPa with 2ppm dissolved oxygen. After 600h exposue, all the samples formed a stable oxide layer, but of varying thickness and microstructure. A typical dual-layered oxide film on P92 and a single-layered structure on TP347HFG and HR3C were observed by SEM and EDS. Further XRD studies indicated the compositions of oxide layers weren’t independent to the type of the used steel. In comparison with ferritic/martensitic steel, austenitic steel showed a higher corrosion resistance.

Some aspects of the defect structure in an austenitic stainless steel

1978 ◽  
Vol 36 (1) ◽  
pp. 314-315
Author(s):  
R. Gonzalez ◽  
L. Bru
Keyword(s):  
Stainless Steel ◽  
Austenitic Stainless Steel ◽  
Cellular Structures ◽  
Total Strain Amplitude ◽  
Total Deformation ◽  
Density Of Dislocations ◽  
Planar Arrays ◽  
Stacking Fault Tetrahedra ◽  
Distribution Of Dislocations ◽  
Very High

The analysis of stacking fault tetrahedra (SFT) in fatigued metals (1,2) is somewhat complicated, due partly to their relatively low density, but principally to the presence of a very high density of dislocations which hides them. In order to overcome this second difficulty, we have used in this work an austenitic stainless steel that deforms in a planar mode and, as expected, examination of the substructure revealed planar arrays of dislocation dipoles rather than the cellular structures which appear both in single and polycrystals of cyclically deformed copper and silver. This more uniform distribution of dislocations allows a better identification of the SFT.The samples were fatigue deformed at the constant total strain amplitude Δε = 0.025 for 5 cycles at three temperatures: 85, 293 and 773 K. One of the samples was tensile strained with a total deformation of 3.5%.

A TEM microscopical investigation of the magnetic domain structure of a metastable austenitic stainless steel

1994 ◽  
Vol 52 ◽  
pp. 696-697
Author(s):  
G. Fourlaris ◽  
T. Gladman
Keyword(s):  
Tensile Strength ◽  
Stainless Steel ◽  
Austenitic Stainless Steel ◽  
Cold Rolling ◽  
Solution Treatment ◽  
Magnetic Domain ◽  
High Strength ◽  
Medium Carbon Steel ◽  
Magnetic Characteristics ◽  
Metastable Austenitic Stainless Steel

Stainless steels have widespread applications due to their good corrosion resistance, but for certain types of large naval constructions, other requirements are imposed such as high strength and toughness , and modified magnetic characteristics.The magnetic characteristics of a 302 type metastable austenitic stainless steel has been assessed after various cold rolling treatments designed to increase strength by strain inducement of martensite. A grade 817M40 low alloy medium carbon steel was used as a reference material.The metastable austenitic stainless steel after solution treatment possesses a fully austenitic microstructure. However its tensile strength , in the solution treated condition , is low.Cold rolling results in the strain induced transformation to α’- martensite in austenitic matrix and enhances the tensile strength. However , α’-martensite is ferromagnetic , and its introduction to an otherwise fully paramagnetic matrix alters the magnetic response of the material. An example of the mixed martensitic-retained austenitic microstructure obtained after the cold rolling experiment is provided in the SEM micrograph of Figure 1.

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