Abstract
The brittle to ductile transition (BDT) in nickel free high nitrogen austenitic stainless steel was investigated. Falling weight impact tests at 176, 273 and 336 K revealed that Fe-25Cr-1·1N (wt-%) austenitic steel exhibits a sharp BDT in spite of being a face centred cubic alloy. The plastic deformation observed following the impact tests indicated that the BDT is induced by poor ductility at low temperatures, as is the case with ferritic steels. To measure the activation energy for the BDT, the strain rate dependence of the BDT temperature was examined using four-point bending tests. The BDT temperature was found to be weakly dependent on strain rate. Arrhenius plots of the BDT temperature against strain rate showed that the activation energy for the BDT of Fe-25Cr-1·1N steel is much higher than that of low carbon ferritic steels. The origins of this distinctive BDT and the large value for its activation energy in this high nitrogen steel are discussed in terms of the reduction in dislocation mobility at low temperatures because of the interactions between the glide dislocations and the solute nitrogen atoms.
| Original language | English |
|---|---|
| Pages (from-to) | 99-102 |
| Number of pages | 4 |
| Journal | International Heat Treatment and Surface Engineering |
| Volume | 6 |
| Issue number | 3 |
| DOIs | |
| Publication status | Published - Sep 1 2012 |
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All Science Journal Classification (ASJC) codes
- Materials Science(all)
Cite this
Brittle to ductile transition in nickel free high nitrogen austenitic stainless steels. / Tanaka, Masaki; Onomoto, T.; Tsuchiyma, Toshihiro; Higashida, K.
In: International Heat Treatment and Surface Engineering, Vol. 6, No. 3, 01.09.2012, p. 99-102.Research output: Contribution to journal › Article
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TY - JOUR
T1 - Brittle to ductile transition in nickel free high nitrogen austenitic stainless steels
AU - Tanaka, Masaki
AU - Onomoto, T.
AU - Tsuchiyma, Toshihiro
AU - Higashida, K.
PY - 2012/9/1
Y1 - 2012/9/1
N2 - The brittle to ductile transition (BDT) in nickel free high nitrogen austenitic stainless steel was investigated. Falling weight impact tests at 176, 273 and 336 K revealed that Fe-25Cr-1·1N (wt-%) austenitic steel exhibits a sharp BDT in spite of being a face centred cubic alloy. The plastic deformation observed following the impact tests indicated that the BDT is induced by poor ductility at low temperatures, as is the case with ferritic steels. To measure the activation energy for the BDT, the strain rate dependence of the BDT temperature was examined using four-point bending tests. The BDT temperature was found to be weakly dependent on strain rate. Arrhenius plots of the BDT temperature against strain rate showed that the activation energy for the BDT of Fe-25Cr-1·1N steel is much higher than that of low carbon ferritic steels. The origins of this distinctive BDT and the large value for its activation energy in this high nitrogen steel are discussed in terms of the reduction in dislocation mobility at low temperatures because of the interactions between the glide dislocations and the solute nitrogen atoms.
AB - The brittle to ductile transition (BDT) in nickel free high nitrogen austenitic stainless steel was investigated. Falling weight impact tests at 176, 273 and 336 K revealed that Fe-25Cr-1·1N (wt-%) austenitic steel exhibits a sharp BDT in spite of being a face centred cubic alloy. The plastic deformation observed following the impact tests indicated that the BDT is induced by poor ductility at low temperatures, as is the case with ferritic steels. To measure the activation energy for the BDT, the strain rate dependence of the BDT temperature was examined using four-point bending tests. The BDT temperature was found to be weakly dependent on strain rate. Arrhenius plots of the BDT temperature against strain rate showed that the activation energy for the BDT of Fe-25Cr-1·1N steel is much higher than that of low carbon ferritic steels. The origins of this distinctive BDT and the large value for its activation energy in this high nitrogen steel are discussed in terms of the reduction in dislocation mobility at low temperatures because of the interactions between the glide dislocations and the solute nitrogen atoms.
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U2 - 10.1179/1749514812Z.00000000029
DO - 10.1179/1749514812Z.00000000029
M3 - Article
VL - 6
SP - 99
EP - 102
JO - International Heat Treatment and Surface Engineering
JF - International Heat Treatment and Surface Engineering
SN - 1749-5148
IS - 3
ER -