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Acta Metall Sin  2020, Vol. 56 Issue (9): 1217-1226    DOI: 10.11900/0412.1961.2020.00005
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Influence of Solution Temperature on γε Transformation and Damping Capacity of Fe-19Mn Alloy
WANG Shihong, LI Jian(), CHAI Feng, LUO Xiaobing, YANG Caifu, SU Hang
Department of Structure Steels, Central Iron and Steel Research Institute, Beijing 100081, China
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Due to the high damping capacity and excellent mechanical properties, Fe-Mn alloy is considered to be a promising high damping alloy, and suitable for constructional and vehicle metal parts application, which can enhance the fatigue property of structures and metal parts, and also improve the working and living environment. It's generally accepted at present that damping capacity of Fe-Mn alloy is influenced by the stacking fault boundaries in γ-austenite and ε-martensite, γ/ε phase boundaries and ε/ε variant boundaries; another view is that boundaries of the above damping sources are made up of partial dislocations, so the damping capacity of Fe-Mn alloy is caused by the motion of partial dislocations, and interpreted by G-L dislocation pinning model and stacking fault probabilities calculation. But there is no distinction between the probabilities of different type stacking faults. Both deformation stacking fault and growth stacking fault can be formed in γ-austenite and ε-martensite, and the change of process parameters has different influence on them, which will lead to different changes of deformation and growth stacking fault probabilities. So it's necessary to analyze whether boundaries of different stacking fault types will have different effects on damping capacity of Fe-Mn alloy. Based on that, a hot-rolled Fe-19Mn alloy is prepared and then solution treated between 950~1100 ℃. Damping capacity is measured by dynamic mechanical analyzer (DMA). The microstructure evolution is observed by OM and TEM, and XRD is used to analyze phase constitution and to measure stacking fault probabilities. The results reveal that Fe-19Mn alloy shows amplitude-dependent damping capacity which almost linearly increases with amplitude, and frequency-independent damping capacity. From G-L plot, the variation of damping capacity below the critical amplitude A' (A'≈30 μm) is interpreted by G-L model, while it's associated with micro-plastic deformation when above A'. As the increase of solution treatment temperature, the damping capacity of Fe-19Mn decreases, and possesses the best performance at 950 ℃; furthermore, it shows different characteristics in different amplitude ranges: when the amplitude is lower than 170 μm, damping capacity decreases in exponential form, which changes similarily with deformation stacking fault probability in ε-martensite, so it can be considered the boundaries of deformation stacking fault as the main damping source; when the amplitude is higher than 170 μm, damping capacity decreases linearly, which changes similarily with the relative length of γ/ε phase boundary, so it can be considered γ/ε phase boundary as the main damping source. Based on TEM observation of stacking faults in γ-austenite, it can be inferred that stacking fault boundaries in γ-austenite have no obvious contribution to the change of damping capacity of Fe-19Mn with amplitude.

Key words:  Fe-Mn alloy      damping capacity      γε transformation      stacking fault probability      γ/ε interface     
Received:  02 January 2020     
ZTFLH:  TG135.7  
Corresponding Authors:  LI Jian     E-mail:

Cite this article: 

WANG Shihong, LI Jian, CHAI Feng, LUO Xiaobing, YANG Caifu, SU Hang. Influence of Solution Temperature on γε Transformation and Damping Capacity of Fe-19Mn Alloy. Acta Metall Sin, 2020, 56(9): 1217-1226.

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Fig.1  Influence of amplitude (a) and frequency (b) on damping capacity of Fe-19Mn alloy (A—amplitude, f—frequency, δ—phase lag angle, tanδ—damping value)
Fig.2  The influence of solution temperature on damping capacity of Fe-19Mn alloy in different A ranges (f=50 Hz)
Fig.3  OM images of microstructures of Fe-19Mn alloy under different solution temperatures
Fig.4  The influence of solution temperature on ε-mar-tensite plate size (a) and relative length of γ/ε interface (b)
Fig.5  Variations of austenite grain size and Msγε with solution temperature (Msγε—starting temperature of γε transformation)
Fig.6  Bright-field TEM image of γ-austenite and ε-martensite (a), dark-field images of γ-austenite (b) and ε-martensite (c) of 1100 ℃ solution treated sample, and corresponding selected area electron diffraction (SAED) patterns for areas A~C in Fig.6a (d~f)
Fig.7  Bright-field (a, d) and dark-field (b, e) TEM images of stacking faults in γ-austenite of 950 ℃ (a, b) and 1050 ℃ (d, e) solution treated sample under two-beam condition, and corresponding SAED patterns for circle areas A (c) and B (f) in Figs.7a and d, respectively
Fig.8  Bright-field TEM images of stacking faults in ε-martensite with different plate thickness under two-beam condition (a~c), and corresponding SAED patterns for ε-martensite in Fig.7a (d), and for ε-martensite in Figs.7b and c (e),respectively
Fig.9  XRD spectra (a) and phase fractions (b) of samples treated in different solution temperatures
Fig.10  The influence of solution temperature on stacking fault probabilities in γ-austenite (a) and ε-martensite (b) (α—deformation fault probab-ility, β—growth fault probability)
Fig.11  The influence of austenite grain size (Dγ) on stacking fault energy (Γ) of γ-austenite (a) and driving force (ΔGγε) (b)
Fig.12  G-L plot of Fe-19Mn alloy (δH—damping, A'—critical amplitude )
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