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Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process

  • Guo Jing EMAIL logo , Cheng Shu-Sen and Guo Hanjie
Published/Copyright: October 13, 2019
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

Thermodynamic analysis was performed to obtain the relation between the carbon content at the BOF endpoint and the dissolved oxygen content in liquid steel and the (FeO + MnO) content in the slag with the help of thermodynamic calculation software FactSage. It finds that both the [O] and (FeO + MnO) content increase with decreasing the carbon content at the BOF endpoint and the increasing rate is larger when the carbon content is lower. In addition, in the case of the higher temperature at the BOF endpoint the [O] in liquid steel increase and the (FeO + MnO) in the slag increase as well. The consumption of O2 for decarbonization at the BOF endpoint is much more than that in RH degasser since the majority of the blowing O2 at the BOF endpoint will produce FeO into the slag, thus it increase the metal loss and deteriorate the steel cleanness during the consequent refining process. As a result, the carbon content at the BOF endpoint should be properly increased within the RH decarbonization ability. At last, industrial trials were carried out and confirmed that total oxygen consumption decrease obviously and the (FeO + MnO) of final BOF slag decline as well with increasing carbon content at BOF endpoint from 0.042% to 0.081%. In addition, it almost does not slow down the RH process and the carbon content in final steel all met the demand of the ultra-low carbon steel. In addition, mechanical properties of IF steel with higher carbon content at the endpoint of BOF are almost all more superior to those of heat with lower carbon content at BOF endpoint.

Keywords: BOF endpoint; decarbonization; C–O equilibrium; ultra-low carbon IF steel

Introduction

There are generally two major problems with regard to production of ultra-low carbon IF steel currently: one is the surface quality problems, the other is the continuous casting (CC) nozzle clogging [1, 2, 3, 4] . Both of the problems have a great relationship with the cleanliness of molten steel, i. e. the amount, size and composition of inclusions in steel. (FeO + MnO) in the final slag of the converter is the main reason for the high oxidizability of the refining slag in RH. Many works [5, 6] have proved that reducing the content of (FeO + MnO) in the refining can effectively decrease the total oxygen content in the steel, improve the castability and reduce IF steel surface quality problems. On the one hand, it is necessary to strictly control the amount of slag during converter tapping to the next refining process; on the other hand, it also needs to reduce the content of1 (FeO + MnO) content in the BOF final slag. Therefore, the determination of the optimized carbon content at the BOF endpoint by reasonable allocation decarburization amount in converter and in RH is if high significance to improve subsequent liquid steel cleaness.

At present, the usual operation principle of producing ultra-low carbon IF steel is to lower the carbon content in the converter as much as possible to increase the free oxygen in the molten steel so as to reduce the decarburization tasks in RH refining. For example, Baosteel [7, 8] considered that the optimum carbon and dissolved oxygen contents before RH treatment were (300–400) × 10–6 and (500–650) × 10–6, respectively; Kawasaki Steel Company [9], the United States Inland Iron and Steel Company [10] controlled the carbon content in the molten steel between 0.03% and 0.04% and

the oxygen content between 0.050% and 0.065% at the end of converter; and Thyssen Steel [11] considered the optimal carbon content of the molten steel at the end of BOF is 0.03%, and the optimal oxygen content is 0.06%. However, the removal of carbon at the BOF endpoint in the steel is at the expense of a large amount of oxygen blowing, a substantial increase of oxygen in the steel, and an increase of (FeO + MnO) in the slag. This will not only increase the oxygen consumption and the iron loss, but also increase the difficulty of slag modification during subsequent refining process and lower the cleanliness of molten steel. Due to the rate of RH vacuumizing increases and the ultimate vacuum degree steady decreases in recent years, decarburization ability of RH has been greatly strengthened, which provides the conditions for more decarburization tasks in RH. In this paper, the thermodynamic software FactSage was used to analyze the influence of carbon content at the BOF endpoint theoretically. The theoretical calculations and industrial trials both verify that increasing the carbon content at the BOF endpoint in a proper extent is beneficial for steel cleanness improvement as well as many other aspects.

Thermodynamic analysis

With oxygen blowing in the converter, the following two reactions will take place,

(1)[C]+[O]=CO(g)
(2)ΔG1θ=−22200−38.34T[12]
(3)Fe(1)+[O]=(FeO)(1)
(4)ΔG2θ=−117700+49.83T[12]

where ΔGiθstands for Gibbs energy. As a result, oxygen will not only react with the carbon in the steel, but also react with Fe to form FeO into the slag. Especially a large amount of FeO is generated at the same time as decarburization when the carbon content is low at the BOF endpoint. Therefore, the carbon content at the BOF endpoint is directly related to the oxygen in the steel and the FeO (or MnO) in the slag. Due to strong mixing conditions in the converter, it can be considered that the slag-steel equilibrium is reached so that the relationship among the carbon content, dissolved oxygen content and FeO in slag at the endpoint of BOF, can be obtained with the help of thermodynamic software FactSage. This can avoid the complex calculation of multiphase reactions and get more accurate results.

Figure 1 shows the relationship between the oxygen content, the content of (FeO + MnO) in the slag and the carbon content at the BOF endpoint in a 120-ton converter at 1,973 and 1,923 K, respectively calculated by using FactSage. As the carbon content decreases, the corresponding content of oxygen and of (FeO + MnO) gradually increase, and the increasing rate accelerates. In addition, [O] in steel at 1,973 K is higher than [O] at 1,823 K by 20–30 × 10–6 with the same carbon content, whereas the content of (FeO + MnO) in the slag is lower by about 1.5–2.5 mass%. This is due to the fact that the free energy change of C–O reaction eq. (1) decreases with the increasing of temperature and, thus, the value of [C%][O%] in the steel increases in the case of a constant partial pressure of CO. The Fe–O reaction, as reaction(2), is an exothermic reaction, thus, temperature increase causes the above reaction to proceed leftward and reduces the content of FeO in the slag. Therefore, increasing the temperature at the BOF endpoint is advantageous for smelting ultra-low carbon IF steel. This can not only reduce the oxidability of slag, but also increase the dissolved oxygen in the steel for RH decarbonization.

Figure 1 Relations between the oxygen content, (FeO + MnO) content in the slag and the carbon content at the BOF endpoint.
Figure 1

Relations between the oxygen content, (FeO + MnO) content in the slag and the carbon content at the BOF endpoint.

At the BOF endpoint, the target blowing O2 amount to remove a certain amount of carbon should contain the following three parts as shown in eq. (5),

(5)Oaddtion=Ode−C+ΔOin−equ+Oin−slag

where Ode-c means the required oxygen to generate CO in the process of decarbonization, ΔOin-equ indicates increased oxygen in equilibrium with the carbon in liquid steel; and Oin-slag suggests oxygen into the slag.

For RH degasser, on account of the quiet slag-steel interface, the slag-steel interface reaction is quite weak and the amount of FeO into the slag is much smaller during decarbonization. Furthermore, the content of excess oxygen after decarbonization is almost the same (200–300 × 10–6) to that before decarbonization since the oxygen needed in equilibrium with carbon under vacuum condition in RH is very small. Therefore, the required blowing O2 for removing a certain amount of carbon in RH are nearly the same as the O2 demanded in decarbonization chemical reaction,

(6)O'addtion=Ode−C

Figure 2 shows the volume of the blowing O2 and the required oxygen amount for producing CO during decarbonization (Ode-C) by decreasing the carbon content in steel from 0.1% to different levels at BOF endpoint. The amount of the blowing O2 raises dramatically with the decreasing carbon content, especially, it increases more obviously when the carbon content is lower than 0.04%. In addition, the required blowing O2 content at 1,973 K is less than that at 1,923 K. According to eq. (6), the bottom curve could represent the blowing oxygen content for the same carbon content removal in RH degasser. Apparently, it is far less than the blowing oxygen content for removing the same carbon content at the BOF endpoint. When the carbon content s decreases from 0.04% to 0.03% at the endpoint of BOF, for instance, the oxygen content obtained by C–O reaction (Ode−C) is about 133 × 10–6, the increased amount of [O] for equilibrating the carbon (ΔOin−equ) is about 180 × 10–6 (from 550 to 730 × 10–6), and the increment of (FeO + MnO) in the slag is approximating 6% that corresponds to about 1,200 × 10–6 dissolved oxygen (Oin−slag). Namely, 1,513 × 10–6 [O] are demanded in total. However, only 133 × 10–6 [O] are required in RH process (Ode−C) to remove the same amount of carbon, which is less than a tenth of the former. Majority of the blowing oxygen at the BOF endpoint (80%) turns into FeO into the slag, which increases the difficulty of modifying the top slag in the following second refining process so that it is hard to enhance the steel cleanness. Also, it rises metal loss of converter steelmaking resulting in the smelting cost increase. As a result, the carbon content at the BOF end point should be properly increase and more decarbonization task can be carried out in RH degasser within the RH decarbonization ability.

Figure 2 Relation between carbon content at the endpoint of BOF and the volume of blowing oxygen.
Figure 2

Relation between carbon content at the endpoint of BOF and the volume of blowing oxygen.

Industrial trial and results

In order to validate the thermodynamic analysis, a large number of industrial data in a 120 ton converter and 120 ladle to produce ultra-low carbon IF steel were collected, in which carbon content in steel were determined by OES (Optical Emission Spectrometer) and (FeO + MnO) content in slag were measured by X-ray fluorescence. In addition, three heats of IF steel with controlling of different carbon content at the endpoint of BOF, 0.042%(A), 0.051%(B) and 0.081%(C) were carried out in the 120 ton converter and ladle for a more accurate comparison by controlling other parameters in similar levels such as hot metal quality and heat treatments. It should be pointed out that the vacuum power of RH should be increased corresponding in a proper manner in the case of carbon content increase.

Figure 3 shows relationship between the oxidizability of final BOF slag and the content of [C] in the steel in a 120 ton converter. It can be seen that the oxidizability of the slag increases with the reduction of carbon content at both temperatures, which is in great agreement with thermodynamic calculations in Figure 1.

Figure 3 Relation between industrial carbon content in liquid steel and oxidizability in slag at different temperature regions at the BOF endpoint in a 120 ton converter.
Figure 3

Relation between industrial carbon content in liquid steel and oxidizability in slag at different temperature regions at the BOF endpoint in a 120 ton converter.

Figure 4 shows relations between the carbon content at the BOF endpoint and the total oxygen consumption both in 120 ton BOF and RH in the case of ultra-low carbon IF steel with final product carbon content lower than 40 × 10–6. A total of 370 industrial data are displayed in the figure corresponding to that in Figure 3(a). When the

Figure 4 Relationship between C content at BOF endpoint and total oxygen consumption of 120 ton BOF and RH.
Figure 4

Relationship between C content at BOF endpoint and total oxygen consumption of 120 ton BOF and RH.

carbon content at the BOF endpoint decreases, the total oxygen consumption in whole smelting process markedly increases. For example, the carbon content at the BOF endpoint is 0.08% and the required total blowing oxygen amount in BOF and RH are between 6,000 and 7,000m3, while the total oxygen consumption are between 6,500 and 8,000m3 in the case of [C%] = 0.03 at the BOF endpoint 0.03%, namely, the latter is 500–1,000m3 higher than the former. Therefore, higher carbon strategy is applied for decarbonization at the endpoint of converter, and the total oxygen consumption is apparently lower than that with a lower carbon strategy at BOF endpoint.

Figure 5 shows the variation of carbon content in IF steel during BOF-RH-CC process. Although the carbon at BOF endpoint in Heat B and Heat C were more than that in Heat A, the carbon content in the steel after RH was lower than that in Heat A, and they three have all been to a low carbon level (< 40 × 10–6) in the final products meeting the IF steel composition demand. Table 1 lists comparison of oxidability in final BOF slag, total oxygen consumption both in BOF and RH and RH vacuum time for the three heats of IF steel with different carbon at the endpoint of BOF. In comparison that of Heat A, the BOF slag oxidability of Heat B and Heat C decreased by 1.6%

Figure 5 Carbon content evolution of three heats of IF steel during BOF-RH-CC process.
Figure 5

Carbon content evolution of three heats of IF steel during BOF-RH-CC process.

Table 1

Comparison between some typical parameters of three heats of IF steel with different carbon content at BOF endpoint.

HeatHeat AHeat BHeat C
C at BOF endpoint/%0.0420.0510.081
(FeO + MnO) in final BOF slag/%26.925.324.6
Total oxygen consumption/m37,2366,9216,583
RH vacuum time/min303227

and 2.3%, respectively. Correspondingly, total oxygen consumptions of Heate B and C decrease by 315 and 653m3, respectively. What’s more, the total RH vacuum time of Heat B and Heat C are 32 and 27 min, respectively compared to 30 min of Heat A, Table 2 shows some mechanical properties of IF steels after the similar heat treatment and rolling process. They are all meet the needs of IF steel, particularly, mechanical properties of heat C are almost all more superior to those of Heat A for IF steel deformation except. Therefore, all the foregoing results indicate almost no negative effect on the normal productivity of melting process and final product properties after increasing C content of BOF endpoint in a reasonable extent.

Table 2

Mechanical properties for IF steels produced by three heats.

HeatHeat AHeat BHeat C
Average plastic strain ratio rm2.542.422.53
Hardening index n0.240.250.25
Yield strength δs/MPa148136133
Tensile strength δb/MPa293288284
Elongation λ/%45.047.047.5

Conclusion

  1. With the decrease of carbon at BOP endpoint, the oxygen in steel and the (FeO + MnO) in the slag gradually increase. For decarbonization at the endpoint of BOF, majority of oxygen reacts with the metal and then the reaction products FeO and MnO enter the slag which makes it difficult to improve molten steel cleanness during the consequent refining and at the same time increases the iron loss.

  2. Industrial data verify that the oxygen consumption for decarbonization will notably decrease in the whole prices (BOF + RH) when the carbon content at BOF endpoint appropriately increase. When the carbon content at BOF endpoint increase from 0.42% to 0.081%, (FeO + MnO) in the final BOF slag decrease from 26.9% to 24.6%, and total oxygen consumption in 120 ton BOF + RH process decreased from 7,236 to 6,583 m3. Moreover, the total vacuum time of RH do not extend by improving vacuum power of RH in a proper manner.

  3. The carbon content in final steel products of the heats with higher carbon content at the endpoint of BOF are all less than 40 × 10–6 which meet the demand of the composition in ultra-low-carbon IF steel. In addition, their mechanical properties are almost all more superior to those of heat with lower carbon content at the endpoint of BOF.

Acknowledgements

The authors express their thanks to National Science Foundation for Young Scientists of China (51704021), China Postdoctoral Fund (2018M630071), fundamental Research Funds for the Central Universities (FRF-TP-16-079A1) and Joint Funds of National Natural Science Foundation of China (U1560203) for their kind financial support. This study is also supported by Beijing Key Laboratory of Special Melting and Preparation of High-end Metal Materials.

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Received: 2018-08-19
Accepted: 2018-12-09
Published Online: 2019-10-13
Published in Print: 2019-02-25

© 2019 Jing et al, published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 Public License.

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https://doi.org/10.1515/htmp-2019-0054
Keywords for this article
BOF endpoint; decarbonization; C–O equilibrium; ultra-low carbon IF steel
Creative Commons
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  3. Research on the Influence of Furnace Structure on Copper Cooling Stave Life
  4. Influence of High Temperature Oxidation on Hydrogen Absorption and Degradation of Zircaloy-2 and Zr 700 Alloys
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  9. Microstructure and Interface Bonding Strength of WC-10Ni/NiCrBSi Composite Coating by Vacuum Brazing
  10. Refill Friction Stir Spot Welding of Dissimilar 6061/7075 Aluminum Alloy
  11. Solvothermal Synthesis and Magnetic Properties of Monodisperse Ni0.5Zn0.5Fe2O4 Hollow Nanospheres
  12. On the Capability of Logarithmic-Power Model for Prediction of Hot Deformation Behavior of Alloy 800H at High Strain Rates
  13. 3D Heat Conductivity Model of Mold Based on Node Temperature Inheritance
  14. 3D Microstructure and Micromechanical Properties of Minerals in Vanadium-Titanium Sinter
  15. Effect of Martensite Structure and Carbide Precipitates on Mechanical Properties of Cr-Mo Alloy Steel with Different Cooling Rate
  16. The Interaction between Erosion Particle and Gas Stream in High Temperature Gas Burner Rig for Thermal Barrier Coatings
  17. Permittivity Study of a CuCl Residue at 13–450 °C and Elucidation of the Microwave Intensification Mechanism for Its Dechlorination
  18. Study on Carbothermal Reduction of Titania in Molten Iron
  19. The Sequence of the Phase Growth during Diffusion in Ti-Based Systems
  20. Growth Kinetics of CoB–Co2B Layers Using the Powder-Pack Boriding Process Assisted by a Direct Current Field
  21. High-Temperature Flow Behaviour and Constitutive Equations for a TC17 Titanium Alloy
  22. Research on Three-Roll Screw Rolling Process for Ti6Al4V Titanium Alloy Bar
  23. Continuous Cooling Transformation of Undeformed and Deformed High Strength Crack-Arrest Steel Plates for Large Container Ships
  24. Formation Mechanism and Influence Factors of the Sticker between Solidified Shell and Mold in Continuous Casting of Steel
  25. Casting Defects in Transition Layer of Cu/Al Composite Castings Prepared Using Pouring Aluminum Method and Their Formation Mechanism
  26. Effect of Current on Segregation and Inclusions Characteristics of Dual Alloy Ingot Processed by Electroslag Remelting
  27. Investigation of Growth Kinetics of Fe2B Layers on AISI 1518 Steel by the Integral Method
  28. Microstructural Evolution and Phase Transformation on the X-Y Surface of Inconel 718 Ni-Based Alloys Fabricated by Selective Laser Melting under Different Heat Treatment
  29. Characterization of Mn-Doped Co3O4 Thin Films Prepared by Sol Gel-Based Dip-Coating Process
  30. Deposition Characteristics of Multitrack Overlayby Plasma Transferred Arc Welding on SS316Lwith Co-Cr Based Alloy – Influence ofProcess Parameters
  31. Elastic Moduli and Elastic Constants of Alloy AuCuSi With FCC Structure Under Pressure
  32. Effect of Cl on Softening and Melting Behaviors of BF Burden
  33. Effect of MgO Injection on Smelting in a Blast Furnace
  34. Structural Characteristics and Hydration Kinetics of Oxidized Steel Slag in a CaO-FeO-SiO2-MgO System
  35. Optimization of Microwave-Assisted Oxidation Roasting of Oxide–Sulphide Zinc Ore with Addition of Manganese Dioxide Using Response Surface Methodology
  36. Hydraulic Study of Bubble Migration in Liquid Titanium Alloy Melt during Vertical Centrifugal Casting Process
  37. Investigation on Double Wire Metal Inert Gas Welding of A7N01-T4 Aluminum Alloy in High-Speed Welding
  38. Oxidation Behaviour of Welded ASTM-SA210 GrA1 Boiler Tube Steels under Cyclic Conditions at 900°C in Air
  39. Study on the Evolution of Damage Degradation at Different Temperatures and Strain Rates for Ti-6Al-4V Alloy
  40. Pack-Boriding of Pure Iron with Powder Mixtures Containing ZrB2
  41. Evolution of Interfacial Features of MnO-SiO2 Type Inclusions/Steel Matrix during Isothermal Heating at Low Temperatures
  42. Effect of MgO/Al2O3 Ratio on Viscosity of Blast Furnace Primary Slag
  43. The Microstructure and Property of the Heat Affected zone in C-Mn Steel Treated by Rare Earth
  44. Microwave-Assisted Molten-Salt Facile Synthesis of Chromium Carbide (Cr3C2) Coatings on the Diamond Particles
  45. Effects of B on the Hot Ductility of Fe-36Ni Invar Alloy
  46. Impurity Distribution after Solidification of Hypereutectic Al-Si Melts and Eutectic Al-Si Melt
  47. Induced Electro-Deposition of High Melting-Point Phases on MgO–C Refractory in CaO–Al2O3–SiO2 – (MgO) Slag at 1773 K
  48. Microstructure and Mechanical Properties of 14Cr-ODS Steels with Zr Addition
  49. A Review of Boron-Rich Silicon Borides Basedon Thermodynamic Stability and Transport Properties of High-Temperature Thermoelectric Materials
  50. Siliceous Manganese Ore from Eastern India:A Potential Resource for Ferrosilicon-Manganese Production
  51. A Strain-Compensated Constitutive Model for Describing the Hot Compressive Deformation Behaviors of an Aged Inconel 718 Superalloy
  52. Surface Alloys of 0.45 C Carbon Steel Produced by High Current Pulsed Electron Beam
  53. Deformation Behavior and Processing Map during Isothermal Hot Compression of 49MnVS3 Non-Quenched and Tempered Steel
  54. A Constitutive Equation for Predicting Elevated Temperature Flow Behavior of BFe10-1-2 Cupronickel Alloy through Double Multiple Nonlinear Regression
  55. Oxidation Behavior of Ferritic Steel T22 Exposed to Supercritical Water
  56. A Multi Scale Strategy for Simulation of Microstructural Evolutions in Friction Stir Welding of Duplex Titanium Alloy
  57. Partition Behavior of Alloying Elements in Nickel-Based Alloys and Their Activity Interaction Parameters and Infinite Dilution Activity Coefficients
  58. Influence of Heating on Tensile Physical-Mechanical Properties of Granite
  59. Comparison of Al-Zn-Mg Alloy P-MIG Welded Joints Filled with Different Wires
  60. Microstructure and Mechanical Properties of Thick Plate Friction Stir Welds for 6082-T6 Aluminum Alloy
  61. Research Article
  62. Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
  63. Calorimetric study on Bi-Cu-Sn alloys
  64. Mineralogical Phase of Slag and Its Effect on Dephosphorization during Converter Steelmaking Using Slag-Remaining Technology
  65. Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder
  66. Cellular Automaton Modeling of Phase Transformation of U-Nb Alloys during Solidification and Consequent Cooling Process
  67. The effect of MgTiO3Adding on Inclusion Characteristics
  68. Cutting performance of a functionally graded cemented carbide tool prepared by microwave heating and nitriding sintering
  69. Creep behaviour and life assessment of a cast nickel – base superalloy MAR – M247
  70. Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation
  71. Reducing Surface Cracks and Improving Cleanliness of H-Beam Blanks in Continuous Casting — Improving continuous casting of H-beam blanks
  72. Rhodium influence on the microstructure and oxidation behaviour of aluminide coatings deposited on pure nickel and nickel based superalloy
  73. The effect of Nb content on precipitates, microstructure and texture of grain oriented silicon steel
  74. Effect of Arc Power on the Wear and High-temperature Oxidation Resistances of Plasma-Sprayed Fe-based Amorphous Coatings
  75. Short Communication
  76. Novel Combined Feeding Approach to Produce Quality Al6061 Composites for Heat Sinks
  77. Research Article
  78. Micromorphology change and microstructure of Cu-P based amorphous filler during heating process
  79. Controlling residual stress and distortion of friction stir welding joint by external stationary shoulder
  80. Research on the ingot shrinkage in the electroslag remelting withdrawal process for 9Cr3Mo roller
  81. Production of Mo2NiB2 Based Hard Alloys by Self-Propagating High-Temperature Synthesis
  82. The Morphology Analysis of Plasma-Sprayed Cast Iron Splats at Different Substrate Temperatures via Fractal Dimension and Circularity Methods
  83. A Comparative Study on Johnson–Cook, Modified Johnson–Cook, Modified Zerilli–Armstrong and Arrhenius-Type Constitutive Models to Predict Hot Deformation Behavior of TA2
  84. Dynamic absorption efficiency of paracetamol powder in microwave drying
  85. Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
  86. Influence of unburned pulverized coal on gasification reaction of coke in blast furnace
  87. Effect of PWHT Conditions on Toughness and Creep Rupture Strength in Modified 9Cr-1Mo Steel Welds
  88. Role of B2O3 on structure and shear-thinning property in CaO–SiO2–Na2O-based mold fluxes
  89. Effect of Acid Slag Treatment on the Inclusions in GCr15 Bearing Steel
  90. Recovery of Iron and Zinc from Blast Furnace Dust Using Iron-Bath Reduction
  91. Phase Analysis and Microstructural Investigations of Ce2Zr2O7 for High-Temperature Coatings on Ni-Base Superalloy Substrates
  92. Combustion Characteristics and Kinetics Study of Pulverized Coal and Semi-Coke
  93. Mechanical and Electrochemical Characterization of Supersolidus Sintered Austenitic Stainless Steel (316 L)
  94. Synthesis and characterization of Cu doped chromium oxide (Cr2O3) thin films
  95. Ladle Nozzle Clogging during casting of Silicon-Steel
  96. Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process
  97. Research Article
  98. Effect of Boundary Conditions on Residual Stresses and Distortion in 316 Stainless Steel Butt Welded Plate
  99. Numerical Analysis on Effect of Additional Gas Injection on Characteristics around Raceway in Melter Gasifier
  100. Variation on thermal damage rate of granite specimen with thermal cycle treatment
  101. Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag
  102. Effect of Basicity on Precipitation of Spinel Crystals in a CaO-SiO2-MgO-Cr2O3-FeO System
  103. Review Article
  104. Exploitation of Mold Flux for the Ti-bearing Welding Wire Steel ER80-G
  105. Research Article
  106. Furnace heat prediction and control model and its application to large blast furnace
  107. Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment
  108. Study of the Viscosity of a La2O3-SiO2-FeO Slag System
  109. Tensile Deformation and Work Hardening Behaviour of AISI 431 Martensitic Stainless Steel at Elevated Temperatures
  110. The Effectiveness of Reinforcement and Processing on Mechanical Properties, Wear Behavior and Damping Response of Aluminum Matrix Composites
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