Stress corrosion cracking of austenitic stainless steels
Juang, Hsun-Kai
This item is only available for download by members of the University of Illinois community. Students, faculty, and staff at the U of I may log in with your NetID and password to view the item. If you are trying to access an Illinois-restricted dissertation or thesis, you can request a copy through your library's Inter-Library Loan office or purchase a copy directly from ProQuest.
Permalink
https://hdl.handle.net/2142/20139
Description
Title
Stress corrosion cracking of austenitic stainless steels
Author(s)
Juang, Hsun-Kai
Issue Date
1989
Doctoral Committee Chair(s)
Altstetter, Carl J.
Department of Study
Materials Science and Engineering
Discipline
Materials Engineering
Degree Granting Institution
University of Illinois at Urbana-Champaign
Degree Name
Ph.D.
Degree Level
Dissertation
Keyword(s)
Engineering, Mechanical
Engineering, Metallurgy
Engineering, Materials Science
Language
eng
Abstract
In order to understand the stress corrosion cracking behavior of metastable and stable austenitic stainless steels, constant elongation rate tests (CERT) and sub-critical crack growth (SCG) tests were used to measure the susceptibility and cracking rate. The tests were performed in H$\sb2$SO$\sb4$/NaCl solutions in the pH ranges from 0 to 7 and at temperatures from 25 to 75$\sp\circ$C. The AISI 301 (metastable) and AISI 310S (stable) alloys were used for these tests. In CERT, the 301 alloy showed susceptible to SCC while 310S did not. In SCG tests, SCG behavior was analysed with respect to applied potential zones on the polarization curve, i.e. cathodic, active (zone 1), active/passive (zone 2) and passive/transpassive (zone 3). It was found that hydrogen embrittlement (HE) was the main cracking process in zone 1 and cathodic zone for annealed specimens. For deformed specimens, HE was operative in the cathodic zone, but in zone 1 the behavior was not clearly HE. Film rupture and active path corrosion were found to proceed in zone 3. In zone 2, SCC seemed to proceed by a mixture of models. The HE characteristics in 301 alloy was believed to be related to the rate of accumulation of hydrogen at the crack tip. Since stain-induced $\alpha\sp\prime$ phase was verified on the fracture surface, $\alpha\sp\prime$ was considered to play an important role in the HE process. The fast diffusion rate of hydrogen in $\alpha\sp\prime$ phase and low escape rate of hydrogen in the surrounding $\gamma$ phase were believed to be the cause of HE. At potentials more noble than zone 1, the smaller hydrogen charging rate (HCR) was believed to be the cause of immunity to HE, resulting in predominance of dissolution or active path corrosion (APC). The HE process was found to be strengthened by hydrogen recombination poison (NaAsO$\sb2$) in zone 1 and cathodic zone, although it was a corrosion inhibitor. For 310S alloy, 3-stage SCG behavior was observed in pH $$ 4N. A ductile failure morphology was identified for 310S alloy tested in the above solution. The resistance of 310S to SCC was thought to be related to its extremely rapid repassivation rate and high SFE.
Use this login method if you
don't
have an
@illinois.edu
email address.
(Oops, I do have one)
IDEALS migrated to a new platform on June 23, 2022. If you created
your account prior to this date, you will have to reset your password
using the forgot-password link below.
