Martensitic Transformation During Compressive Deformation of a Non-conventional Stainless Steel and Its Quantitative Assessment
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Diffusionless transformation
Austenitic stainless steel
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Isothermal process
Carbon fibers
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The reverse transformation mechanism of martensite to austenite in 00Cr15Ni7Mo2WCu2 super martensitic stainless steel has been studied. The experimental results indicated that the volume fraction of reversed austenite in 00Cr15Ni7Mo2WCu2 super martensitic stainless steel increased first and then decreased with increasing tempering temperature over a range of 550–750 °C after quenching at 1050 °C. The reversed austenite formed along the martensite lath boundaries. When the tempering temperature was below 700 °C, the reversed austenite grew with a Ni‐enrichment; when the temperature was above 700 °C, the reversed austenite re‐dissolved and transformed to martensite and a part of the reversed austenite divided the original wider martensitic laths into a number of thinner ones. The basic mechanism for formation of the reversed austenite is diffusion in 00Cr15Ni7Mo2WCu2 super martensitic stainless steel.
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The aim of the present study was to study the changes of micro-structural behavior of medium manganese steel during intercritical annealing. During the process, it was observed that the microstructure gradually evolved from austenite structure into martensite. The retained austenite volume fraction reached the maximum value of 35% at 650 o C annealing temperature. From SEM and TEM results, it was found that reversed austenite partly changed into fresh martensite during quenching while the remained part was retained as retained austenite. The final structure consisted of ferrite, retained austenite and fresh martensite.
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In this paper we investigated the microstructure and phase transition of atomized Fe-(1.3, 7.9, 11.7 wt.%) Mn alloy powders. The results show that the main phases of Fe-1.3Mn, Fe-7.9Mn and Fe-11.7Mn powders are ferrite, α’-martensite+austenite, α’-martensite+ε-martensite+austenite, respectively. The δ-ferrite in the Fe-1.3Mn powder is the high-temperature δ-ferrite directly formed from liquid, companying by a small number of nanometer sized austenite particles precipitated from the ferrite matrix. In the Fe-11.7Mn powder, the γ-austenite, ε-martensite and α’-martensite are found in the same region and have the K-S orientation relationship, suggesting phase transitions of γ-austenite → ε-martensite → α’-martensite and γ → α’-martensite.
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The stabilization of austenite during isothermal holding above Ms has been investigated using 1%-carbon, 5%-nickel steel. The stabilization increases with the amount of martensite present, but it is established that the martensite is not an important factor in stabilization. It has been found that actually the presence of martensite is not even necessary for the stabilization to occur. Hence stabilization is possible without prior decomposition of austenite either into bainite or martensite and seems to reflect some internal rearrangement occuring in the parent phase during retarded cooling or isothermal holding.
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A series of quenching temperatures (QT) were applied to investigate the interaction of bainite and martensite transformations in intercritical quenching and partitioning steels with multiple-stage martensite transformation. It reveals that the fractions of initial martensite, bainite, whole retained austenite and austenite respectively retained by bainite or martensite showed obvious three-stage variations, coincided with first stage, stagnant stage and second stage of martensite transformation. In the case of high QT that near Ms., the retained austenite was mainly ascribed to bainite carbon enrichment. As quenched to relatively low QT in stage-1 region or lower, the austenite retained by martensite carbon partitioning occupied the majority and the decrease of RA was mainly ascribed to inter-lath austenite and packet boundary austenite. In addition, an identical partitioning end was achieved with mean austenite carbon contents between T0 line and paraequilibrium condition, irrespective of initial martensite and bainite fractions. The heterogeneous carbon distribution in parent austenite deriving from ferrite formation significantly influenced the subsequent martensite transformation and corresponding martensite structure. The martensite block in high carbon region possessed much smaller size, while the corresponding packet size was still larger. Moreover, the significant martensite variant absence and variant combination were also observed.
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두 種類의 martensite合金, 즉 Fe-C基 martensite鋼(Fe-1.7%C)과 Fe-Ni基 martensite合金(Fe-27% Ni-0.14%C)을 마련해서, 이 두 martensite 조직 중에 含有된 잔류 austenite의 tempering 擧動을 X-線的으로 調査하여 다음과 같은 結論을 얻었다.
1. Fe-1.7%C martensite 鋼의 잔류 austenite는 約 150℃×1hr tempering에서 分解하기 시작하였으며 280℃×1hr tempering에서는 거의 大部分 分解하였다.
2. Fe-1.7%C martensite 鋼中의 殘留 austenite의 (111)γ 回折線의 積分幅은 tempering 溫度와 더불어 增加하였다.
3. Fe-27% Ni-0.14%C martensite 鋼은 430℃까지 tempering하여도 殘留 austenite가 分解하지 않았다.
4. Fe-27% Ni-0.14%C martensite 鋼에 있어서 austenite의 積分幅은 360℃ tempering 까지는 거의 一定한 값을 나타내다가 그 以上 溫度가 增加함에 따라 減少하였다.
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