Microstructure and texture evolution in dual-phase steels: Competition between recovery, recrystallization, and phase transformation

2010 ◽  
Vol 527 (16-17) ◽  
pp. 4161-4168 ◽  
Author(s):  
N. Peranio ◽  
Y.J. Li ◽  
F. Roters ◽  
D. Raabe
Keyword(s):  
Phase Transformation ◽  
Texture Evolution ◽  
Dual Phase ◽  
Dual Phase Steels

Texture Evolution during Cold Rolling and Annealing in Dual Phase Steels

2011 ◽  
Vol 702-703 ◽  
pp. 778-781 ◽  
Author(s):  
Jai Gautam ◽  
Alexis G. Miroux ◽  
Jaap Moerman ◽  
Carla Barbatti ◽  
Leo Kestens
Keyword(s):  
Phase Transformation ◽  
Cold Rolling ◽  
Texture Evolution ◽  
Rolling Texture ◽  
Recovery Process ◽  
Second Phase ◽  
Dual Phase ◽  
Dual Phase Steels ◽  
Initial Stage ◽  
Cold Rolling And Annealing

This paper investigates the bulk texture evolution during cold rolling and annealing of Dual Phase steels for different processing conditions, i.e. cold reduction within the reduction range of 45 to 73% and annealing at temperatures between 650 and 850°C, which includes the recovery, recrystallisation and partial phase transformation domains. Textures have been measured by X-ray diffraction. The results reveal that the rolling texture is strengthened during the recovery process or initial stage of recrystallisation while during recrystallisation a weak RD-ND type of texture appears. During subsequent phase transformation the RD-ND type of texture further weakens and later randomises as the second phase fraction increases beyond 75%.

EBSD Study of Substructure and Texture Formation in Dual-Phase Steel Sheets for Semi-Finished Products

2010 ◽  
Vol 160 ◽  
pp. 251-256 ◽  
Author(s):  
M. Masimov ◽  
N. Peranio ◽  
B. Springub ◽  
Franz Roters ◽  
Dierk Raabe
Keyword(s):  
Cold Rolling ◽  
Annealing Temperature ◽  
Texture Evolution ◽  
Industrial Process ◽  
Dual Phase ◽  
Technological Parameters ◽  
Dual Phase Steels ◽  
Final Annealing ◽  
Steel Sheets ◽  
Different Temperatures

Using SEM/EBSD the substructure and texture evolution in dual phase steels in the first steps of the process chain, i.e. hot rolling, cold rolling, and following annealing were characterized. In order to obtain dual phase steels with high ductility and high tensile strength an industrial process was reproduced by cold rolling of industrially hot rolled steel sheets of a thickness of 3.75 mm with ferrite and pearlite morphology down to a thickness of 1.75 mm and finally annealing at different temperatures. Such technique allows a compilation of ferrite and martensite morphology typical for dual phase steels. Due to the competition between recovery, recrystallization and phase trans-formation during annealing a variety of ferrite martensite morphologies was produced by promoting one of the mechanisms through the variation of technological parameters such as heating rate, intercritical annealing temperature, annealing time, cooling rate and the final annealing temperature. Annealing induced changes of the mechanical properties were determined by hardness measurements and are discussed on the basis of the results of the substructure investigations.

Texture evolution of high-strength deep-drawing dual-phase steels

2015 ◽  
Vol 19 (sup5) ◽  
pp. S5-631-S5-634
Author(s):  
G. Hai-rong ◽  
Z. Zheng-zhi ◽  
Y. Jie-yun ◽  
W. Zhi-gang ◽  
Z. Ai-min
Keyword(s):  
Deep Drawing ◽  
Texture Evolution ◽  
High Strength ◽  
Dual Phase ◽  
Dual Phase Steels

The Effects of Si and Deformation on the Phase Transformation in Dual Phase Steels

2007 ◽  
Vol 124-126 ◽  
pp. 1617-1620 ◽  
Author(s):  
Sang Hwan Lee ◽  
Jong Min Choi ◽  
Yeol Rae Cho ◽  
Kyung Jong Lee
Keyword(s):  
Phase Transformation ◽  
Lower Bainite ◽  
Dual Phase ◽  
Dual Phase Steels ◽  
Austenite Grain Size ◽  
Temperature Range ◽  
Intermediate Temperature Range ◽  
Ferrite Transformation ◽  
Untransformed Austenite ◽  
Cct Diagrams

The effect of Si on phase transformation was well known in dual phase steels. Si promoted the ferrite transformation and the enriched C in untransformed austenite prohibited the transformation at intermediate temperature range resulting in the formation of lower bainite and martensite at low temperature range. In addition, during continuous cooling with fast cooling rate, it was very hard to differentiate one phase from the others. In order to clarify the effects of Si on the austenite-to-ferrite transformation quantitatively, the start temperatures of bainite(BS) and martensite(MS) as well as ferrite(Ae3) and pearlite(Ae1) were calculated by thermodynamic analysis. LVDT measured by dilatometer and 1st differentiation peaks of LVDT were examined with microstructures, which gives a possibility of the phase separation. In CCT diagrams, it was also found that large austenite grain size(AGS) widened the gap between the transformation start(Ts) and end(Tf) when Si was added.

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