Abstract:Instead of hot rolling and cold rolling followed by annealing, strip casting is a more economic and environmentally friendly way to produce transformation-induced plasticity (TRIP) steels. According to industrial practice of strip casting, rapid cooling in this work was achieved using a dip tester, and a Gleeble 3500 thermo-mechanical simulator was used to carry out the processing route. A typical microstructure of TRIP steels, which included ~0.55 fraction of polygonal ferrite with bainite, retained austenite… Show more
“…The optimal annealing hold temperature of thermo-mechanically processed 42SiMn steel would therefore be in the interval of 350-425 • C, depending wheatear higher strength or higher total elongation is desired. The highest formability (RmxA product) was obtained for the hold at 425 • C. This finding corresponds to a previous work on a low carbon 0.17C-1.5Si-1.6Mn TRIP steel, which confirmed the bainitic hold temperature of 400 • C as an optimal choice for both, heat and thermo-mechanical treatment [34]. It should be however noted that unlike the case of low carbon steel, where thermo-mechanical treatment improved mechanical properties of the steel, thermo-mechanical treatment of 42SiMn steel resulted in the formation of a significant amount of pearlite, which deteriorated the mechanical properties in comparison to those that were obtained by heat treatment.…”
Section: Effect Of Bainitic Hold Temperaturesupporting
Medium-carbon steel 42SiMn (0.4C-0.6Mn-2Si-0.03Nb) was used for a two-step heat treatment consisting of a soaking hold and an annealing hold at bainite transformation temperature. Various heating temperatures, cooling rates, and bainitic hold temperatures were applied to the steel to obtain microstructures typical for TRIP (Transformation Induced Plasticity) steels. TRIP steels utilize the positive effects of a multiphase microstructure with retained austenite, creating a good combination of strength and total elongation and an excellent deep-drawing ability. Typical microstructures consist of ferrite, bainite, and 10-15% of retained austenite. In this work, tensile strengths in the region of 887-1063 MPa were achieved with total elongation A 5mm of 26-47%, and the final microstructures contained 4-16% of retained austenite. The most suitable microstructure and the best combination of high strength and total elongation were achieved for the processing with intercritical heating temperature of 850 • C and cooling at 30 • C/s to the bainitic hold of 400 • C. Very fine pearlite persisted in the microstructures, even after applying a cooling rate of 50 • C/s, however these small areas with extremely fine laths did not prevent the retention of up to 16% of retained austenite, and high total elongation A 5mm above 40% was still reached for these microstructures.
“…The optimal annealing hold temperature of thermo-mechanically processed 42SiMn steel would therefore be in the interval of 350-425 • C, depending wheatear higher strength or higher total elongation is desired. The highest formability (RmxA product) was obtained for the hold at 425 • C. This finding corresponds to a previous work on a low carbon 0.17C-1.5Si-1.6Mn TRIP steel, which confirmed the bainitic hold temperature of 400 • C as an optimal choice for both, heat and thermo-mechanical treatment [34]. It should be however noted that unlike the case of low carbon steel, where thermo-mechanical treatment improved mechanical properties of the steel, thermo-mechanical treatment of 42SiMn steel resulted in the formation of a significant amount of pearlite, which deteriorated the mechanical properties in comparison to those that were obtained by heat treatment.…”
Section: Effect Of Bainitic Hold Temperaturesupporting
Medium-carbon steel 42SiMn (0.4C-0.6Mn-2Si-0.03Nb) was used for a two-step heat treatment consisting of a soaking hold and an annealing hold at bainite transformation temperature. Various heating temperatures, cooling rates, and bainitic hold temperatures were applied to the steel to obtain microstructures typical for TRIP (Transformation Induced Plasticity) steels. TRIP steels utilize the positive effects of a multiphase microstructure with retained austenite, creating a good combination of strength and total elongation and an excellent deep-drawing ability. Typical microstructures consist of ferrite, bainite, and 10-15% of retained austenite. In this work, tensile strengths in the region of 887-1063 MPa were achieved with total elongation A 5mm of 26-47%, and the final microstructures contained 4-16% of retained austenite. The most suitable microstructure and the best combination of high strength and total elongation were achieved for the processing with intercritical heating temperature of 850 • C and cooling at 30 • C/s to the bainitic hold of 400 • C. Very fine pearlite persisted in the microstructures, even after applying a cooling rate of 50 • C/s, however these small areas with extremely fine laths did not prevent the retention of up to 16% of retained austenite, and high total elongation A 5mm above 40% was still reached for these microstructures.
“…These values are well above other high strength steels such as Dual Phase (UTS = 900 MPa, UTSxTE = 11.6 GPa%) and Bainitic (UTS = 650MPa, UTSxTE = 8.0 GPa%) and are aligned with TRIP multiphase steels, as shown in the studies by Sugimoto et al 7 In Figures 6 are illustrated the stain hardening exponent results in function of true strain to the 6 conditions tested. The conditions presented typical strain hardening exponent curves of TRIP steels according to Xiong et al 8 , except the condition 6.…”
The effect of the application of constant temperatures (isothermal plateau) and variables (cooling ramp) during the overaging (OA) stage of the continuous annealing cycle in the microstructural characteristics and mechanical properties of a TRIP steel of the class of 780 MPa was investigated. It was simulated six overaging conditions in the equipment Gleeble. The microstructures presented variable fractions of ferrite, bainite, retained austenite and a small martensite portion. All the conditions achieved the minimum strength of 780 MPa it is possible to highlight the conditions for initial OA temperature of 440 °C where presented the best results of mechanical properties and typical TRIP steels behaviors.
“…This technique has been applied in industry for the production of aluminium, lead, carbon steel, silicon steel and stainless steel [2][3][4]. In laboratory the ferrite-martensite dual-phase (DP) steel [5][6][7], multi-phase transformation-induced plasticity (TRIP) steel [8,9] and twinning-induced plasticity steel [10] have also been successfully produced by strip casting. In comparison with a traditional way to produce steels by the sequence of steel-making, continuous casting, hot rolling and cold rolling, the strip casting technology requires a shorter production line, due to the strips being directly manufactured from liquid metals.…”
Section: Introductionmentioning
confidence: 99%
“…Recent studies carried out by the present authors produced low-alloyed ferrite-martensite DP [8] and multi-phase TRIP steels [8] using strip casting simulated in the laboratory. Although tensile properties comparable with industrially hot/cold rolled DP and TRIP steels have been achieved, the microstructure is not uniform through strip thickness, due to the cooling rate gradient [8,9]. To avoid this problem, a furnace was introduced into the processing line of strip casting (Figure 1) for the first time in this work, namely the modified strip casting.…”
Instead of conventional steel making and continuous casting followed by hot and cold rolling, strip casting technology modified with the addition of a continuous annealing stage (namely, modified strip casting) is a promising short-route for producing ferrite-martensite dual-phase (DP) and multi-phase transformation-induced plasticity (TRIP) steels. However, at present, the multi-phase steels are not manufactured by the modified strip casting, due to insufficient knowledge about phase transformations occurring during in-line heat treatment. This study analysed the phase transformations, particularly the formation of ferrite, bainite and martensite and the retention of austenite, in one 0.17C-1.52Si-1.61Mn-0.195Cr (wt. %) steel subjected to the modified strip casting simulated in the laboratory. Through the adjustment of temperature and holding time, the characteristic microstructures for DP and TRIP steels have been obtained. The DP steel showed comparable tensile properties with industrial DP 590 and the TRIP steel had a lower strength but a higher ductility than those industrially produced TRIP steels. The strength could be further enhanced by the application of deformation and/or the addition of alloying elements. This study indicates that the modified strip casting technology is a promising new route to produce steels with multi-phase microstructures in the future.
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