Influence of Strain Rate on Hot Ductility of a V‐Microalloyed Steel Slab

Großeiber, Simon; Ilie, Sergiu; Poletti, María Cecilia; Harrer, Bernhard; Degischer, H. P.

doi:10.1002/srin.201100335

Cited by 21 publications

(18 citation statements)

References 15 publications

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“…[8][9][10] Furthermore, the method XCT has been successfully used to characterize samples from continuous casting regarding ductility, damage initiation, and fracture mechanism. [11][12][13] In general though, the evaluation of XCT-data of Fe-based materials can be rather difficult if the conditions mentioned above are not completely fulfilled. Therefore, XCT-data concerning steel samples have to be usually inspected in a manual way by individually examining the XCT-slices.…”

Section: X-ray-computed Tomographymentioning

confidence: 97%

Detection of Non-Metallic Inclusions in Quenched and Tempered Steel Bars by XCT and after Fatigue Life Testing

Gusenbauer

Reiter

Kastner

et al. 2015

steel research int.

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Non-metallic inclusions (NMIs) determine to a high degree the quality and cleanness of steel and are often the reason for functional failure, especially in dynamic-stressed components. Therefore, it is important to have accurate, fast, and reliable characterization methods for these unwanted material inhomogeneities. In this paper, two different methods for the detection of NMIs are compared: X-ray-computed tomography (XCT) and fatigue life testing. XCT allows the detection and analysis of material inhomogeneities and their positions in a 3D volume. The evaluation of XCT-data of Fe-based materials can be rather difficult, since the results are usually prone to image noise, offer poor contrast, and the interpretation is affected by artifacts. Suitable evaluation strategies for detection and classification are presented. The degradation of steel samples by dynamic fatigue testing is a destructive way of determining the existence of harmful NMIs. If there is an NMI of critical size in the sample, a functional failure may occur. The fracture surface is investigated by scanning electron microscopy (SEM), equipped with an energy dispersive X-ray (EDX) spectroscopy unit in order to identify shape, type, and chemical composition of the harmful NMI.

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Section: X-ray-computed Tomographymentioning

confidence: 97%

Detection of Non-Metallic Inclusions in Quenched and Tempered Steel Bars by XCT and after Fatigue Life Testing

Gusenbauer

Reiter

Kastner

et al. 2015

steel research int.

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show abstract

“…The reasons for the decrease of hot ductility have been studied by many scholars. [3][4][5][6][7][8][9][10][11][12][13][14][15][38][39][40][41][42] Zhang et al indicated that hot ductility trough resulted from the formation of pro-eutectoid ferrite films along prior austenite grain boundaries. [38,39] The distribution of the impurities [40] or precipitation [39,41] containing Ti, Nb, B, etc.…”

Section: A Factors Influencing the Hot Ductilitymentioning

confidence: 99%

“…[14] By decreasing the strain rate, strain-induced precipitation takes place, and the formation of nitrides and carbides is increased. [15] The numerical simulation of CC was constrained due to the lack of high-temperature mechanical property data of the novel steels. These data can be obtained using specific process parameters corresponding to the actual production-line parameters.…”

Section: Introductionmentioning

confidence: 99%

Hot Ductility and Compression Deformation Behavior of TRIP980 at Elevated Temperatures

Zhang

Gan

et al. 2017

Metall Mater Trans B

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The hot ductility tests of a kind of 980 MPa class Fe-0.31C (wt pct) TRIP steel (TRIP980) with the addition of Ti/V/Nb were conducted on a Gleeble-3500 thermomechanical simulator in the temperatures ranging from 873 K to 1573 K (600°C to 1300°C) at a constant strain rate of 0.001 s À1 . It is found that the hot ductility trough ranges from 873 K to 1123 K (600°C to 850°C). The recommended straightening temperatures are from 1173 K to 1523 K (900°C to 1250°C). The isothermal hot compression deformation behavior was also studied by means of Gleeble-3500 in the temperatures ranging from 1173 K to 1373 K (900°C to 1100°C) at strain rates ranging from 0.01 s À1 to 10 s À1 . The results show that the peak stress decreases with the increasing temperature and the decreasing strain rate. The deformation activation energy of the test steel is 436.7 kJ/mol. The hot deformation equation of the steel has been established, and the processing maps have been developed on the basis of experimental data and the principle of dynamic materials model (DMM). By analyzing the processing maps of strains of 0.5, 0.7, and 0.9, it is found that dynamic recrystallization occurs in the peak power dissipation efficiency domain, which is the optimal area of hot working. Finally, the factors influencing hot ductility and thermal activation energy of the test steel were investigated by means of microscopic analysis. It indicates that the additional microalloying elements play important roles both in the loss of hot ductility and in the enormous increase of deformation activation energy for the TRIP980 steel.

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“…The occurrence of cracking is strongly associated with the ductility of steel in the temperature range of the straightening stage of continuous casting (ranging from 700 to 1000 C), [1][2][3] besides casting parameters, such as casting speed and secondary cooling pattern. Boron-containing steels are very susceptible to slab corner cracking because of poor hot ductility.…”

Section: Introductionmentioning

confidence: 99%

Effect of Boron on the Hot Ductility of Low-Carbon Nb-Ti-Microalloyed Steel

Shi

Liu

et al. 2016

Mater. Trans.

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Hot tensile tests were performed to examine the effect of boron on the hot ductility of Nb-Ti-microalloyed steels. The equilibrium precipitation in the steel was predicted by Thermo-Calc calculation. The microstructure, fracture surface and precipitates in the deformed steel were examined. The results show that boron addition is favorable to improving the hot ductility of Nb-Ti-microalloyed steel. This bene cial effect is caused by the soluble boron instead of coarse BN in the steel. The hot ductility of the steel decreases less from 1000 C with increasing boron addition. The hot ductility trough shifts toward lower temperatures because ferrite formation was restrained with increasing boron content of the steel. The formation of NbC, TiN and thin lm-like ferrite along austenite grain boundaries lead to the decrease in the hot ductility of the steel. Boron addition has negligible in uence on the precipitation temperature and amount of TiN and NbC precipitates in Nb-Ti-microalloyed steel. The amount of NbC precipitates is largest in the steel, followed by TiN and BN. The precipitation temperature of BN increases considerably with further increasing the boron content. The fracture mode of Nb-Ti-microalloyed steel tends to be more ductile with the increase in the boron content of the steel.

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Influence of Strain Rate on Hot Ductility of a V‐Microalloyed Steel Slab

Cited by 21 publications

References 15 publications

Detection of Non-Metallic Inclusions in Quenched and Tempered Steel Bars by XCT and after Fatigue Life Testing

Detection of Non-Metallic Inclusions in Quenched and Tempered Steel Bars by XCT and after Fatigue Life Testing

Hot Ductility and Compression Deformation Behavior of TRIP980 at Elevated Temperatures

Effect of Boron on the Hot Ductility of Low-Carbon Nb-Ti-Microalloyed Steel

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