Phase equilibria of the Al2O3–CaO–SiO2-(0%, 5%, 10%) MgO slag system for non-metallic inclusions control
Introduction
Supreme wear resistance and fatigue strength properties are notably preferred for hardened spring steel working with high-frequency dynamics stresses, making it possible for applications in automobile production, serving as valve, clutch, suspensions and plate springs [[1], [2], [3], [4]]. However, these properties could be severely impaired by stress concentration gradient and small voids surrounding inclusions related to thermal expansion coefficients differences and detachment between inclusions and surrounding matrix [[5], [6], [7]]. Owing to the unfeasibility of thorough removal of non-metallic inside molten steel, inclusions with excellent deformability and low liquidus temperatures were generally favoured [8,9]. To enhance overall steel cleanliness levels, ladle furnace (LF) refining and aluminium deoxidation process was commonly employed, the unstable operations of which could result into severe inclusion contamination caused by slag entrapment and spinel generation [[10], [11], [12]]. To further promote steel cleanliness levels and inclusions compositions optimization, reliable thermodynamic properties of liquidus temperature and equilibrated phases of Al2O3–CaO–SiO2–MgO system related to refining slag should be investigated in detail [13,14]. Numerous preceding research had been conducted concerning the Al2O3–CaO–SiO2–MgO system. Mao et al. [15] optimized cordierite and sapphirine ternary compounds for the Al2O3–MgO–SiO2 system and illustrated the liquid phases utilizing the ionic two-sublattice model. Fabrichnaya et al. [16] established the thermodynamic properties consistent with calorimetric measurements and phase equilibria for the liquid phase in the system CaSiO3–CaAl2Si2O7–Ca2Al2SiO7 utilizing molecular regular solution models. Gran et al. [17] confirmed the glassy phases in the regions of high basicity for the Al2O3–CaO–MgO–SiO2 system at 1500 and 1600°C utilizing quenching methods and subsequent EPMA microanalysis. Heulens et al. [18] confirmed the wollastonite crystal growth for CaO–Al2O3–SiO2 melt from 1320 °C to 1370 °C utilizing high-temperature confocal scanning laser microscope. Valdez et al. [19] studied dissolution of alumina in ternary slags with high SiO2 contents, a high silica quaternary slag and a low silica ternary slag close to ladle slag composition within the temperature range 1470 and 1530°C with CSLM. The liquidus temperature and phase equilibrium of CaO–Al2O3–SiO2–MgO system had been explored within previous research [[20], [21], [22]]. Kim et al. [23] found viscosities of CaO–SiO2-20 wt%Al2O3–MgO slags (CaO/SiO2 = 1.0–1.2) decreased with increased MgO contents. Shi et al. [24] constructed liquidus lines and phase diagram for the CaO–SiO2-5wt%MgO-20wt%Al2O3–TiO2 phase diagram system between 1300 °C and 1400°C. Shi et al. [25] also established the 1400 °C and 1450 °C isotherms and phase relations for CaO–SiO2-5wt%MgO-30 wt%Al2O3–TiO2 system relevant to high Al2O3 Ti-bearing slag system. Wang et al. [26] confirmed initial crystallization temperature of CaO–SiO2–MgO–Al2O3 slag system decreased with increasing Al2O3/SiO2 ratio. Shen et al. [27] found the viscosity of CaO–MgO–SiO2–Al2O3–FeO slag system increased with increased ratios of (Al2O3)/(Al2O3+FeO). Sun et al. [28] found minimum viscosity of CaO–SiO2-10mass% MgO–Al2O3 slags was achieved at 16 mass%, which improved the amphiprotic properties of Al2O3. Nevertheless, the experimental isotherm intervals of 100 K in part of these research could not provide precise thermodynamic data concerning liquidus and equilibrated phases related to refining slag compositions. Furthermore, the dashed lines in predicted phase diagrams indicated the isotherm distribution inaccuracy. Meanwhile, owing to the obvious incompatability of analyzed solid compositions with X-ray examination and EMPA techniques, dependable thermodynamic properties of CaO–Al2O3–SiO2–MgO quaternary system are indispensable for industrial operations [29,30].
As clarified in our precedent investigation of Al2O3-containing inclusions in spring steel deoxidized by aluminium, the Al2O3–CaO–SiO2-(MgO) inclusions inside Al-killed spring steel primarily originated from entrapped high-basicity slags, the SiO2 of which was reduced by dissolved [Al] [31]. Meanwhile, according to our previous research of pseudo-ternary diagram of CaO–Al2O3–SiO2–MgO quaternary slag related to Al2O3–SiO2–CaO inclusions originating fromcollision between Al2O3–SiO2 and CaO–SiO2 inclusions in Si-deoxidized spring steel, significant incompatibility of liquidus temperature and equilibrated phases distribution between FactSage calculations, previous experimental results and our results were determined [32]. The Al2O3–CaO–SiO2–MgO pseudo-ternary system with basicity of 1.1, 1.3, and 1.5 have been determined in the proceeding research [30,33,34]. Fig. 1 illustrated the comparison results of preceding experimental results from Ma et al. [30], Cavalier et al. [35] and predictions of FactSage 7.3. Apparent differences of liquidus temperatures and equilibrated phases for system of CaO–Al2O3–SiO2–5%MgO between previous and current experimental results were confirmed by Ma et al. [24], Cavalier et al. [35] and FactSage predictions, especially when CaO contents were between 35wt% and 55wt%. For example, based on experimental data of Cavalier et al. [35], the liquidus temperatures of points with CaO contents around 45% and SiO2 contents almost 35% were near 1400 °C, much higher than that determined by FactSage prediction being almost 1470 °C.
During the refining process of Al-deoxidized spring steel, high-basicity slag was generally utilized for the sake of inclusions removal and control, but inaccurate thermodynamic data of predetermined phase diagram of Al2O3–CaO–SiO2–MgO system related to high-basicity slag is still a problem. In this study, the principal phases and liquidus temperatures of Al2O3–CaO–SiO2–MgO system with magnesium oxide mass percent being 0, 5 and 10 predicted by FactSage 7.3 were compared with experimental analysis results both from previous publications [30,33,34] and present authors.
Section snippets
Selection of pseudo-binaries system
To enhance the modification and control of Al2O3–CaO inclusions, the appropriate selection of pseudo-binaries sections in the Al2O3–CaO–SiO2–MgO system is essential. Based on our precending study, high-basicity slag entrapment reduced by dissolved [Al] resulted in Al2O3–CaO inclusions [31]. Therefore, two compositions were proposed based on compositions of deoxidation products and refining slag, which were pure Al2O3 and had mass ratio of XCaOXSiO2 = 6 respectively, indicated as the black
Explanation of the pseudo-binary portions
Almost 60 equilibria experiments of the (Al2O3)-(CaO + SiO2)–MgO system were carried out for current study, temperature ranges of which varies from 1623 K to 1833 K (1350°C and 1560°C). Experimental results would be thoroughly evaluated and then depicted on the pseudo-binary phase equilibrium diagrams, as illustrated in the subsequent parts. The typical quenched slag morphologies gained by back-scattered examination of the glassy phases dominant phase equilibrium are shown in Fig. 4 (a)-(g),
Conclusions
To obtain accurate thermodynamic properties concerning formation mechanism of Al2O3–CaO-(MgO–SiO2) inclusions, the phase equilibria and liquidus temperatures of Al2O3–CaO–MgO–SiO2 with CaO/SiO2 ratios of 6.0 with fixed MgO contents have been experimentally explored between 1623 K and 1833 K (1350 °C and 1560 °C). Some significant conclusions were summarized as follows.
- (1)
The increased Al2O3 contents gradually transformed coexisting equilibria solids phases from Ca2SiO4 and Ca3SiO5, into CaAl2O4,
Declaration of competing interest
The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
Acknowledgments
Baosteel Australia Research and Development Centre and Australian Research Council supported this research financially. Dr Sha Lyu was supported by the scholarships from China Scholarship Council and The University of Queensland International Research Tuition. The Australian Microscopy & Microanalysis Research Facility is deeply acknowledged for EPMA operations. Ms Ying Yu and Mr Ron Rasch from the Centre for Microscopy and Microanalysis at the University of Queensland are gratefully
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