“…Previous works [56,84,85] have used high temperature tensile tests to simulate and understand the formation of solidification cracks during the casting process. Scheller et al [86] schematically (Figure 4) presented the temperature range where the material will show a propensity for cracking due to low-ductility during the casting process.…”
Section: Cracking Problems In Cast Steel In Temperature Zone Higher T...mentioning
confidence: 99%
“…The parameter, ΔT O (= T NF – T NZ ) [86,87] is known as the brittle temperature range [46] and is used as a physical quantity to describe the tendency of hot-crack formation during the continuous casting process [84,86]. Moreover, the temperature range of ΔT O is equivalent to the temperature range of the low-ductility zone (T > 1200°C) as shown in Figure 5. Figure 4. Schematic representation of reduction of area (RA) and maximum force as function of temperature (taken from Scheller et al [86]). Figure 5. Schematic representation of different temperature zones of reduced hot-ductility of steel for different embrittling mechanisms (taken from Fedosov et al [85]). Ψ % in y-axis is reduction of area (RA (%)).…”
Section: Cracking Problems In Cast Steel In Temperature Zone Higher T...mentioning
There is a growing drive within the steel industry to increase scrap usage in the Blast Furnace (BF)-Basic Oxygen Furnace (BOF) integrated route and extend the scrap-based Electric Arc Furnace (EAF) route for steel production due to the resultant reduced energy costs and CO 2 emissions and the abundant steel scrap supply in the UK. In general, steel scrap may contain high levels of undesirable residual elements, which may have pronounced effects on the casting process of steel production. This article critically reviews current metallurgical understanding about the behaviour of various residual elements, individually and synergistically at high (>1200°C) and low (<1200°C) temperatures during the casting process, with a focus on local enrichment and cracking caused by the residual elements. This review article aims to help the steel community to increase the utilisation of steel scrap for steel production by identifying the current constraints and opportunities.
“…Previous works [56,84,85] have used high temperature tensile tests to simulate and understand the formation of solidification cracks during the casting process. Scheller et al [86] schematically (Figure 4) presented the temperature range where the material will show a propensity for cracking due to low-ductility during the casting process.…”
Section: Cracking Problems In Cast Steel In Temperature Zone Higher T...mentioning
confidence: 99%
“…The parameter, ΔT O (= T NF – T NZ ) [86,87] is known as the brittle temperature range [46] and is used as a physical quantity to describe the tendency of hot-crack formation during the continuous casting process [84,86]. Moreover, the temperature range of ΔT O is equivalent to the temperature range of the low-ductility zone (T > 1200°C) as shown in Figure 5. Figure 4. Schematic representation of reduction of area (RA) and maximum force as function of temperature (taken from Scheller et al [86]). Figure 5. Schematic representation of different temperature zones of reduced hot-ductility of steel for different embrittling mechanisms (taken from Fedosov et al [85]). Ψ % in y-axis is reduction of area (RA (%)).…”
Section: Cracking Problems In Cast Steel In Temperature Zone Higher T...mentioning
There is a growing drive within the steel industry to increase scrap usage in the Blast Furnace (BF)-Basic Oxygen Furnace (BOF) integrated route and extend the scrap-based Electric Arc Furnace (EAF) route for steel production due to the resultant reduced energy costs and CO 2 emissions and the abundant steel scrap supply in the UK. In general, steel scrap may contain high levels of undesirable residual elements, which may have pronounced effects on the casting process of steel production. This article critically reviews current metallurgical understanding about the behaviour of various residual elements, individually and synergistically at high (>1200°C) and low (<1200°C) temperatures during the casting process, with a focus on local enrichment and cracking caused by the residual elements. This review article aims to help the steel community to increase the utilisation of steel scrap for steel production by identifying the current constraints and opportunities.
“…There are many types of surface cracks in hot-rolled thick plates, which can be classified according to their morphology and the location of appearance: transverse crack, longitudinal crack, corner crack, star crack, etc. [2][3][4][5][6] The formation causes of the cracks with different morphologies are different. Most types of hot-rolled plate cracks are associated with the surface defects of the continuous casting slab.…”
Mountain‐like surface cracks often appear on the thick plates of high‐strength low‐alloy (HSLA) steel after hot rolling, which have a serious impact on production efficiency. Herein, the formation cause of mountain‐like cracks is discussed using methods such as acid pickling and observations of microstructure and inclusions. The deformation behavior of microcracks is obtained by analyzing the rolling process of slab. The inclusions in the top of the crack are Type‐I inclusions with high elemental contents of K and P and Type‐II inclusions with high elemental contents of C. The inclusions in the sides of the crack are Al2O3. It is concluded that mountain‐like cracks are caused by surface microcracks containing Type‐I inclusions in the continuous casting slab. During rolling, the rapid deforming of side‐1 stretches the crack so that the unusual microstructure appears. The cracks extended in the rolling direction have Al2O3 inclusions. The mountain‐like crack with Type‐I inclusions in the top and Al2O3 in the sides eventually form. A single microcrack forms a single mountain‐like crack and multiple clustered microcracks form a continuous mountain‐like crack. To reduce mountain‐like cracks, reducing Type‐I inclusions to reduce surface defects of the slab is an effective means.
“…When the temperature drops to the temperature of austenite transformation completion (Tγ), the austenite begins to grow rapidly and finally forms coarse austenite grains with sizes above 1 mm during the solidification of peritectic steel, which are usually called 'blown grains' (BG) [1,2]. BG will decrease the ductility of the slab surface and promote crack propagation, which is an important reason for the formation of transverse corner cracks during the straightening process of slabs [3][4][5][6][7][8]. Therefore, eliminating BG during the solidification of peritectic steel has become the key factor in controlling the transverse corner crack.…”
Refinement of solidification austenite grains is an important way to control the transverse corner cracks. In the present work, the effect of Ti-Nb carbonitride on the refinement of solidification austenite grains is studied by laboratory experiments. Then, the precipitation temperature of Nb-Ti carbonitride is analysed by establishing a thermodynamic model. The results show that the austenite diameter decreases slowly from 1.45 to 1.16 mm (without Ti addition) and significantly decreases from 0.84 to 0.21 mm (with 0.02 wt-% Ti addition) with the Nb content varying from 0.03 to 0.09 wt-%. The pinning pressure provided by composite precipitation greatly increases with 0.02 wt-% Ti addition. The thermodynamic model of Nb-Ti carbonitride shows that the precipitation temperature of (Nb, Ti)(C, N) increases by approximately 20°C compared to Nb(C, N), which is the main reason for the increase in the pinning pressure.
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