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AN INTERNAL FRICTION PEAK DUE TO STRESS INDUCED α’ MARTENSITE IN A SUS 304 STEEL
N. Igata, H. Chen, K. Miyahara
To cite this version:
N. Igata, H. Chen, K. Miyahara. AN INTERNAL FRICTION PEAK DUE TO STRESS INDUCED
α’ MARTENSITE IN A SUS 304 STEEL. Journal de Physique Colloques, 1982, 43 (C4), pp.C4-547-
C4-550. �10.1051/jphyscol:1982485�. �jpa-00222205�
JOURNAL DE PHYSIQUE
CoZZoque C4, supple'ment au n o 12, Tome 43, de'cembre 1982 page C4-547
AN INTERNAL F R I C T I O N PEAK DUE TO STRESS INDUCED a ' MARTENSITE I N A SUS 304 STEEL
N. Igata, H.B. ChenXand K. Miyahara
Department o f Materia l s Science, Faculty o f Engineering, University o f Tokyo, Hongo, Bunkyo-ku, Tokyo, 11 3, Japan
(Accepted 9 August 1982)
Abstract.- An internal friction peak which is considered to be due to a' martensite phase in a cold worked 304L stain- less steel has been found at 360K at the measurement fre- quency of about 500Hz by the present authors. This peak is different from the peaks which have been reported by Baraz et al. and Mezzetti et al. in cold worked 18-8 stainless steels. The present work has revealed that the 360K peak height increases with the concentration of solute carbon and nitrogen atoms. The 6 value, which is discussed in Nowick et al's papers is larger than 2.5 for the 360K peak.
Accordingly, this peak is not a single relaxation peak such as a Snoek peak of solute carbon atom. The 360K peak is con- sidered to be a cold work peak which is caused by the inter- action between high density dislocations and solute carbon and nitrogen atoms in martensite phase.
Introduction.- Internal friction peaks which are considered to be due to a phase or a' martensite phase in 18-8 stainless steels have been reported by Baraz et al.(l), Mezzetti et a1.(2) and the present authors
(3). Baraz et al.(l) and Mezzetti et a1.(2) have found 370 to 500K peaks and 590K peak at 1 Hz in cold worked 18-8 stainless steels, re- spectively. On the other hand, the present authors have observed 360K peak at the measurement frequency of about 500Hz in a 304L stainless steel deformed at 77K. Recently, Yoshida has observed a peak which occurs at about 310K at the measurement frequency of 1 Hz in a cold worked 301ML steel(4). The temperature of this peak is higher by about ZOK than the result of the present work, considering the measurement frequency. Yoshida says this 310K peak is neither stable nor affected by the concentration of nitrogen. In the present work, however, it has been found that the 360K peak height is affected by the solute carbon and nitrogen concentration. The objective of this work is to clarify some characteristics of the behaviors of this 360K peak and to discuss the origin of this peak.
Experimental procedure.- Chemical compositions of materials used in this work are given in Table 1. Material A is a received material of a SUS 304L stainless steel. Materials B and C are obtained by dry-hydro- gen treatments at 1620K for 3.6x103s and at 1670K for 1.8x104s on the material A, respectively. Specimens are cut from t h ~ sheets of mate- rials A, B and C. They are heated at 1370K for 9x10 s, quenched in water, anddeformed by 20 to 50% by tensile deformation and rolling at temperatures of 77 and 398K. The conditions of the cold work are sum- marized in Table 2. The size of the specimen for internal friction measurement is about 0.5x10.0x100mm. Internal friction is measured by the transverse vibration method at temperature range 130 to 440K and at a heating rate of 2 . 1 ~ 1 0 - ~ ~ / s . Measurement frequency is about 500Hz.
"permanent Address : Department of Materials Science and Engineering, Harbin Institute of Technology, Harbin, China
Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphyscol:1982485
JOURNAL DE PHYSIQUE
Table 1. The chemical composition of materials used (wt%).
Material C Si Mn P S Ni Cr 0 N
A 0.049 0.58 1.70 0.023 0.007 9.20 18.65 0.0066 0.029
*
Si, Mn, P, S, Ni, Cr and 0 in materials B and C are not chemically analyzed but these compositions are considered not to change much.Table 2. The cold work condition of each specimen.
Specimen Cold work temp.(K) Cold work degree(%) Cold work mode
A-1
* *
393 22.0 Tension- -
A-2 7 7 50.0 Rolling
B-1 7 7 50.0 Rolling
C- 1 77 50.0 Rolling
* *
A, B and C mean the kind of materials shown in Table 1.X ray diffraction method is used for the analysis of martensite and austenite phases in the specimens. Fe filter is used for the selective transmission of the Co Ka line.
Experimental results and discussions.- Fig.1 shows clearly two peaks at 320 and 360K in cold worked specimens A-1 and A-2, respectively.
From the result of X ray diffraction shown in Fiq.2, the 320K peak and the 360K peak are considered to be closely related with y phase and a' martensite phase, respectively(3,5,6). As for the internal friction peaks due to martensite phase in steels, a number of investigations have been performed. Ward et a1.(7) and Gladman et a1.(8) have reported that an internal friction peak occurs at about 490K at a frequency of 1 Hz in martensitic carbon steels. Baraz et al.(l) and Mezzetti et al.
(2) have found 370 to 500K peaks and 590K peak at 1 Hz in cold worked 18-8 stainless steels, respectively. However, these peaks are different from the 360K peak in the present work. Yoshida has observed an inter- nal friction peak at 310K and at 1 Hz in a cold worked 301ML steel(4).
The peak temperature of this 310K peak seems to be a little higher than that of the 360K peak from the frequency dependence of the peak temper- ature shown in Fig.3. Fig.4 shows internal friction curves and Younq's moduluses of specimens A-2, B-1 and C-1. Fig.5 indicates the sol- ute carbon and nitrogen concentration dependence of net peak height of the 360K peak. The peak height increases with the concentration of solute carbon and nitrogen atoms. The activation energy for the 360K peak is found to be 0.92eV from the frequency dependence of the peak temperature shown in Fig.3. This value is approximately equal to the migration energy of carbon (1.07eV) and nitrogen (0.82eV) in a iron.
However, the value of 0 . 9 2 e ~ cannot be directly related with the mi- gration energy of the carbon or nitrogen atom in the martensite phase in a 18-8 steel because of the uncertainty of the effect of Ni and Cr on the migration energy of C and N in this phase. The B value discussed in Nowick et al!s papers (9,lO) are larger than 2.5 for the 360K peak.
Therefore, this peak is not a single relaxation peak such as the Snoek peak. It is also not reasonable that the 360K peak is consisted of some kinds of solute peak, including the Snoek peaks of C and N, because the Snoek peaks are considered not to appear at the high degree of cold work such as 50%. Therefore, it is considered that the 360K peak can be attributed to a cold work peak which is caused by the interaction between high density dislocations and solute carbon and nitrogen atoms
in the a ' martensite phase.
Fig.1 Temperature dependences Fig.2 X ray diffraction of of internal friction and Young's specimens A-1 and A-2.
modulus of specimens A-1 and A-2.
I . . . . . . . . ]
Oi20 1~ 200 2I.O 280 320 360 LW LLO TEMPERATUREIKI
Fig.3 Relationships between the ~ i g . 4 Temperature dependences measurement frequency and the of internal friction and Young's reciprocal peak temperature modulus of specimens A-2, B-1 of the peaks due to y phase and and C-1.
a' martensite phase.
Fig.5 Solute carbon and nitrogen concentration dependence of the net peak height of the 360K peak.
C4-550 JOURNAL DE PHYSIQUE
Conclusion.- The 360K peak at the measurement frequency of about 500Hz is attributed to the strain induced martensite phase in a 304L steel.
The peak height increases with the concentration of solute carbon and nitrogen atoms. The activation energy of the 360K peak is 0.92eV. This peak is not a single relaxation peak. This peak is considered to be a cold work peak which is caused by the interaction between high density dislocations and solute carbon and nitrogen atoms in the martensite phase.
Acknowledgement.- Authors are very grateful to Dr.S.Satoh of Kawasaki Steels Industry Co. Ltd for the chemical analysis of the materials and Dr.H.Wada of University of Tokyo for the dry hydrogen treatments of the specimens.
References.
(1) Baraz V.R., Grache S.V. and Rolshchikov L.D., Steel in the USSR (1972) 670.
(2) Mezzetti F., Passari L. and Nobili D., Proc. of 5th Intern. Conf.
on Internal Friction and Ultrasonic Attenuation in Crystalline Solids (Aug. 1973, Aachen, West Germany), Edited by Lenz D. and Lucke K . , Vol.1, p.436.
(3) Igata N., Chen H.B. and Miyahara K., to be published in Scripta Met.
(4) Yoshida I., private communication.
(5) Igata N., Chen H.B.,Miyahara K. and Uba T., J. Physique (Proc. of 7th Intern. Conf. on Internal Friction and Ultrasonic Attenuation in Crystalline Solids, July, 1981, Lausanne, Switzerland, Edited by Benoit W. and Gremaud G . ) , C5-193 (1982).
(6) Igata N., Chen H.B. and Miyahara K., Scripta Met., 16 (1982) 169.
(7) Ward R. and Capus J.M., J. Iron and Steel Inst., =(1963) 1038.
(8) Gladman T. and Pickering F.B., ibid.,
204
(1966) 112.(9) Nowick A.S. and Berry B.S., IBM Journal of Res. and Develop.,
5
(1961) 297.
(10) Nowick A.S. and Berry B.S., ibid.,
