Morphology of Solidification Structure and MnS Inclusion in High Carbon Steel Continuously Cast Bloom

Luo, Shaohua; Wang, Bingyu; Wang, Zhaohui; Jiang, Donghua; Wang, Weiling; Zhu, Miaoyong

doi:10.2355/isijinternational.isijint-2017-294

Cited by 34 publications

(17 citation statements)

References 35 publications

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“…As shown in Table 4, it can be seen that the Lever-rule model is obtained based on the assumption that solute elements are completely diffused in both liquid and γ-Fe phases; however, the Scheil model neglects such diffusion in the γ-Fe phase, which means the solute elements are completely diffused in liquid and have no diffusion in the γ-Fe phase. Due to the fact that the diffusion coefficient of N is much larger than that of Ti in the γ-Fe phase, as comparison of Equations (18) and (19) indicates [18,21], and more obviously supported by Figure 2, so, it is reasonable to assume that solute element N is completely diffused in the γ-Fe phase and the diffusion in the γ-Fe phase for Ti is neglected. That is to say, the Lever-rule model is applied for the N and Scheil model for Ti.…”

Section: Usage Of the Lrsm Modelmentioning

confidence: 98%

“…where w [i] and w 0 [i] denote the instantaneous and initial concentration of solute elements (N and Ti) in the liquid phase zone during the solidification process, respectively; k i is the equilibrium distribution coefficient between liquid and γ-Fe phase, herein k C = 0.34, k N = 0.48, and k Ti = 0.30 [18][19][20]; g represents the solid fraction; φ (in the range of 0-1) denotes the inverse diffusion coefficient and α is the Fourier parameter.…”

Section: Models Equation Conditions Nomentioning

confidence: 99%

“…The above analytical results ( Figure 3) were obtained based on the assumption that N is completely diffused and Ti has no diffusion in the γ-Fe phase. In fact, both N and Ti would diffuse to some extent in the γ-Fe phase, as shown in Equations (18) and (19), respectively. and 3 lg Q (calculated by LRSM model) are depicted in Figure 3, from which it can be easily seen that TiN will only precipitate at the very late stage of the solidification process, with a solid fraction bigger than 0.9966.…”

Section: Usage Of Ohnaka Model On Considering the Effect Of Carbon Onmentioning

confidence: 99%

Section: Usage Of Ohnaka Model On Considering the Effect Of Carbon Onmentioning

confidence: 99%

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Understanding TiN Precipitation Behavior during Solidification of SWRH 92A Tire Cord Steel by Selected Thermodynamic Models

et al. 2019

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Tire cord steel is widely used in the tire production process of the vehicle manufacturing industry due to its excellent strength and toughness. Titanium nitride (TiN) inclusion, existing in tire rod, has a seriously detrimental effect on the fatigue and drawing performances of the tire steel. In order to control its amount and morphology, the precipitation behavior of TiN during solidification in SWRH 92A tire cord steel was analyzed by selected thermodynamic models. The calculated results showed that TiN cannot precipitate in the liquid phase region regardless of the selected models. However, the precipitation of TiN in the mushy zone would occur at the final stage during the solidification process (at solid fractions greater than 0.98) if the LRSM (Lever-rule model was applied for the N and Scheil model for Ti) or Ohnaka models (without considering the effect of carbon on secondary dendrite arm spacing (SDAS)) were adopted. For the Ohnaka model, in the case when the effect of carbon on SDAS was considered, TiN would probably precipitate in the solid phase zone rather than precipitate in the liquid phase region or mushy zone.

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Section: Usage Of the Lrsm Modelmentioning

confidence: 98%

Section: Models Equation Conditions Nomentioning

confidence: 99%

Section: Usage Of Ohnaka Model On Considering the Effect Of Carbon Onmentioning

confidence: 99%

Section: Usage Of Ohnaka Model On Considering the Effect Of Carbon Onmentioning

confidence: 99%

See 2 more Smart Citations

Understanding TiN Precipitation Behavior during Solidification of SWRH 92A Tire Cord Steel by Selected Thermodynamic Models

et al. 2019

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“…where C Mn L and C S L represent the concentration of Mn and S at the solidification front, respectively; C Mn 0 and C S 0 denote the initial concentration of Mn, S in the molten steel, respectively; f s is the solid fraction; k Mn and k S are the equilibrium distribution coefficients of Mn and S, respectively; k Mn = 0.78 and k S = 0.035 [32].…”

Section: Mechanism On the Formation Of Mgal 2 O 4 -Mns Inclusionmentioning

confidence: 99%

Thermodynamics and Agglomeration Behavior on Spinel Inclusion in Al-Deoxidized Steel Coupling with Mg Treatment

Lei

Wang

Yuan

et al. 2019

Metals

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There are many types of non-metallic MgAl2O4 inclusions observed in Al-deoxidized steel coupling with Mg treatment, including single-particle MgAl2O4, agglomerated MgAl2O4, and MgAl2O4-MnS. Thermodynamic calculation shows that MgAl2O4 precipitates in the liquid phase. The phase transformation follows liquid + Al2O3 + MgAl2O4 → liquid + MgAl2O4 → liquid + MgO + MgAl2O4 → liquid + MgO with the Mg content increasing when the Al content is a constant in molten steel, and it is in agreement with the experimental results for the formation of MgAl2O4 in molten steel. The calculation results of various attractive forces between two particles show that the cavity bridge force plays a dominant role in the agglomeration process and results in the agglomerated MgAl2O4. The lattice mismatch calculation result shows that MgAl2O4 can provide effective sites for MnS nucleating in steel.

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Detection and Numerical Simulation of Non‐Metallic Inclusions in Continuous Casting Slab

Liu

et al. 2019

steel research int.

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A high-efficiency fast-detection platform (FDP) is set up to detect the spacial distribution of non-metallic inclusions in slab. The spacial distribution of inclusion in the slab is asymmetrical and non-uniform. In the vertical part of the caster, more inclusions are found in the loose side; while in the bending part, more inclusions are found in the fixed side. Two main sources of inclusions are revealed through SEM þ EDS method: slag entrapment and oxidation of molten steel. The reason for these large inclusions is because of the high super heat and excessive rate of water cooling, since the micro structure is proven to be Widmanstatten. Then, a large eddy simulation (LES) model coupled with solidification is developed to study the inclusion transport and entrapment in the mold. Results show that the velocity near the fixed side is larger than that in the loose side, leading to the fact that more inclusions are removed from the top surface at the fixed side. Smaller inclusions are easier taken deep into the bending part of the caster, and are dragged by the curvature of fixed side, leading to the fact that inclusions in the fixed side are more than that in the loose side.

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Morphology of Solidification Structure and MnS Inclusion in High Carbon Steel Continuously Cast Bloom

Cited by 34 publications

References 35 publications

Understanding TiN Precipitation Behavior during Solidification of SWRH 92A Tire Cord Steel by Selected Thermodynamic Models

Understanding TiN Precipitation Behavior during Solidification of SWRH 92A Tire Cord Steel by Selected Thermodynamic Models

Thermodynamics and Agglomeration Behavior on Spinel Inclusion in Al-Deoxidized Steel Coupling with Mg Treatment

Detection and Numerical Simulation of Non‐Metallic Inclusions in Continuous Casting Slab

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