Concurrence of Phase Transition and Grain Growth in Nanocrystalline Metallic Materials

doi:10.11900/0412.1961.2018.00318

Acta Metall Sin

2018, Vol. 54

Issue (11): 1525-1536 DOI: 10.11900/0412.1961.2018.00318

Microstructures

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Concurrence of Phase Transition and Grain Growth in Nanocrystalline Metallic Materials

Feng LIU(

), Linke HUANG, Yuzeng CHEN

State Key Laboratory of Solidification Processing, Northwestern Polytechnical University, Xi'an 710072, China

Cite this article:

Feng LIU, Linke HUANG, Yuzeng CHEN. Concurrence of Phase Transition and Grain Growth in Nanocrystalline Metallic Materials. Acta Metall Sin, 2018, 54(11): 1525-1536.

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Abstract

The concurrence of solid-state phase transition and grain growth is ubiquitous in thermal processing of metallic materials; understanding the concurrence is significant for manipulation of microstructure and design of structured materials with high strength and good ductility. This work will briefly review the recent progresses on the concurrence in nanocrystalline metallic materials, with particular attention to the physical origin, typical examples, underlying mechanisms, as well as microstructures, of the concurrence. On this basis, perspectives on scientific understanding of the occurrence in nanocrystalline materials are addressed.

Key words: phase transition grain growth nanocrystalline metallic material concurrence

Received: 09 July 2018

ZTFLH:

TG113

Fund: Supported by National Key Research and Development Program of China (Nos.2017YFB0305100 and 2017YFB0703001), National Natural Science Foundation of China (Nos.51431008 and 51790481), Fundamental Research Funds for the Central Universities (No.3102017jc01002) and Research Fund of State Key Laboratory of Solidification Processing of Northwestern Polytechnical University (No.117-TZ-2015)

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	Feng LIU
	Linke HUANG
	Yuzeng CHEN

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00318 OR https://www.ams.org.cn/EN/Y2018/V54/I11/1525

Fig.1 Concurrence of recrystallization and ferrite to austenite transformation upon heating the cold-rolled Fe-0.15C-1.48Mn-0.013Si steel^[47]
(a) volume fraction (F_v) of austenite, recrystallized and deformed ferrite as a function of time
(b) electron backscatter diffraction (EBSD) map of microstructure obtained by the concurrence (Red, green and blue correspond to martensite (austenite), deformed ferrite and recrystallized ferrite, respectively)

Fig.2 The microstructure by concurrence of precipitation and recrystallization in the Al-Mn alloy. Mn-rich precipitates disperse into the well-defined matrix^[53] (ND—normal direction, RD—rolling direction)

Fig.3 Concurrence of phase boundary (PB) and grain boundary (GB) migrations characterized by in situ high-resolution transmission electron microscopy (HRTEM) in the nanocrystalline Fe₉₁Ni₈Zr₁alloy^[17] (A series of in situ HRTEM images show the concurrence of GB (highlighted in red) and PB (highlighted in yellow) migrations with time at 600 ℃. Two PB segments are indexed as PB1 and PB2, respectively. The initial time of interest is set as t=0 s. 0~7 s: the region of interest is ferrite and only GB migration is observed; 26~74 s: both GB and PB migrations occur; 92~123 s: the region of interest is totally transformed into austenite and thus austenite growth is observed)

Fig.4 Interaction between PB and GB migrations^[17]
(a) the new phase forms at GB (b) PB is propagating toward GB
(c) PB is intersecting with GB (d) PB has crossed over GB

Fig.5 Effect of GB on the PB migration and the corresponding migration direction^[17]. The velocity of PB migration is retarded (a) and the corresponding migration direction varies markedly (b) once the PB crosses over the GB-affected zone

Fig.6 APT analysis of the nanocrystalline Fe₉₁Ni₈Zr₁ alloy with single ferrite phase^[18]
(a) Ni and C segregate at GBs; two GB segments (i.e. GB1 and GB2) are indicated by black arrows. Zr-O-based clusters are observed to almost homogeneously distribute through the whole detected volume
(b) top: isoconcentration surfaces plotted at 7% ZrO (atomic fraction) revealing the dispersion of Zr-O-based nanoclusters. Bottom: quantitative chemical analysis of Ni and C across the GB1 and GB2 shown in Fig.6a

Fig.7 Bright-field images captured from the in situ TEM heating experiment revealing the austenite growth behavior in the nanocrystalline Fe₉₁Ni₈Zr₁ alloy^[18]
(a) three ferrite grains are labeled as G1, G2 and G3; two GB segments (i.e. G1/G2, G2/G3) are highlighted by purple arrows
(b~f, h) formation and sluggish growth of the austenite phase
(g) diffraction pattern showing the coexistence of ferrite and austenite phase
(i) PB displacement as a function of temperature (Inset shows the evolution of PB position during the trajectory that normal to the GB segment)

Fig.8 APT analysis of nanocrystalline Fe₉₁Ni₈Zr₁ alloy with dual-phase bimodal nanostructure^[18]
(a) the detected volume is separated by a clear PB: Ni (green dots) and C (red dots) enriched and depleted regions can be identified as the austenite and ferrite phase, respectively. Zr-O-based clusters are observed to homogeneously distribute through the austenite and ferrite phase
(b) top: isoconcentration surfaces plotted at 9% Ni (green) and 7% ZrO (purple) revealing the PB and the dispersion of Zr-O-based nanoclusters, respectively. Bottom: proximity histogram for the indicated isoconcentration surfaces at 9% Ni showing quantitative compositional partitioning in the ferrite and austenite phase

Fig.9 Dual-phase bimodal nanostructure of nanocrystalline Fe₉₁Ni₈Zr₁ alloy^[18] (Left: nano-/ultrafine austenite is embedded inside the nano-matrix of ferrite, dividing the nanocrystalline system into a series of constrained transformation cells. Right: interface map showing the PBs and GBs)

Table 1 Examples of precipitates in nanocrystalline metallic materials^{[22,23,24,25,26,27,28,29,30,31,32,33,34,35,36]}

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