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Study on Carbothermal Reduction of Titania in Molten Iron

  • Yong Deng EMAIL logo , Jianliang Zhang and Kexin Jiao
Published/Copyright: August 29, 2018
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

In order to improve the reduction rate of titania in molten iron, various iron powders containing C, Si, Mn and S were melted. The experiments were carried out on the reduction of titania through a high-temperature tube furnace at 1,723–1,823 K. The quantitative effects of C, Si, Mn, S and temperature on the reduction of titania were investigated in the current study. The results demonstrated that when the carbon content, the manganese content and the temperature increased by 1 %, 0.1 % and 100 K, the reduction rate increased by 0.008 %/h, 0.001125 %/h and 0.0235 %/h, respectively; when the sulfur content increased by 0.01 %, the reduction rate decreased by 0.004875 %/h; the reduction rate was irregular with the change of silicon content in molten iron. The phase at the reaction interface after the experiment was confirmed to be the Fe2Ti3O9 which was considered to be the combination product between iron oxide and titania; the lower titanium oxides were unstable and hard to be observed. The reduction was affected by the concentration of various elements in molten iron and the activity interaction coefficients between various elements. The rate constants for reduction were calculated at 1,723 K, 1,773 K and 1,823 K; the apparent activation energy was calculated as 209 kJ/mol through the rate constants and temperatures according to the Arrhenius equation.

Keywords: blast furnace; molten iron; titania; carbothermal reduction; reduction rate
PACS: 2010; 81.05.Bx

Introduction

In recent years, increased utilization of blast furnace (BF) has been highly desirable for ironmaking [1, 2]. Many companies have sustained a series of BF hearth incidents, such as the abnormal temperature increase of the hearth sidewall and the hearth sidewall breakout [3, 4]. Currently, the formation of a stable solidified layer, rapidly on the hot face of carbon bricks, is the key to solve the problems of the hearth, where the ore containing titania charged in BF is the most effective way to form a protective layer [5, 6]. Therefore, the titania reduction and the titanium behavior in molten iron have attracted an increasing attention.

Certain studies were executed to describe the reduction of titania. Licko et al. [7] analyzed the reduction of titania by carbon into lower titanium oxides beginning at 1,443 K. The sequence of reduction was observed: TiO2-TinO2n-1 (n>10)–TinO2n–1 (4<n<10)–Ti3O5–(Ti2O3)–Ti(CxOy)–TiC(vacuum), whereas the Ti2O3 would be reduced and carburized to Ti(CxOy) rather than TiO [8]. Wei et  al. [9] investigated that the titanium content in molten iron increased with the increase of titania in BF, binary basicity of slag, temperature, and reaction time. Zhao et al. [10] found that the titanium content in molten iron was mainly affected by the temperature. The reduction rate of titania in molten iron was strongly dependent on the carbon content and temperature [11]. Shigeno et al. [12] concluded that the reduction rate of titania would decline as sulfur adsorption at the interface decreased the contact area, when sulfur existed in molten iron. In contrast, the effect of sulfur was not apparently observed in the research of Bandyopadhyay [13]. The behavior of titanium in molten iron was investigated in other papers. Manabu et al. [14] reported that the swelling and drooping phenomena were observed when carbon saturated molten iron containing titanium. The effects of titanium content on viscosity, melting temperature and fluidity of molten iron were investigated by He et al. [15]. Wen [16] measured the viscosity of molten iron, observing that the effect of titanium was the most remarkable. In a number of studies, the reduction of titania was investigated; however, the effect of element content on the reduction is empirical summary, and few have carried out experiments to explore the quantitative effect of the elements on the reduction. Moreover, significant effort is required to analyze the reaction process through thermodynamic analysis and kinetics parameter calculation.

In this paper, the quantitative effect of the elements as well as the corresponding interaction on the reduction of titania in molten iron was investigated, and thermodynamic analysis and kinetics parameter calculation were analyzed to improve the reduction rate of titania to guide ironmaking practice.

Experimental procedure

Sample

In the present series of experiments, the titania powder (≥98 %), the iron powder (≥ 98 %), the graphite powder (≥ 99.85 %), the silica fume (≥ 99 %), the manganese powder (≥ 99.9 %) and the FeS (≥ 99 %) were utilized as the experimental raw materials.

The titania powder was ground to low-sized particles with an automatic grinding machine, in order to obtain a chemical uniform tablet. The size distribution and specific surface area of titania particles were measured with a laser particle size analyzer (LMS-30), as presented in Table 1. Consequently, the pure titania powder (10 g in weight) was pressed into a tablet (retained 3 min under 300 MPa of pressure) of 10 mm in thickness and 25 mm in diameter. Subsequently, the titania sample was placed in a drying oven at 378 K for 2 h. Following this, the sample was pre-sintered in a high-temperature tube furnace at 1,823 K for 2 h, to increase the strength. The sintered titania sample was 8 mm in thickness and 20 mm in diameter (as presented in Figure 1), and the volume of sintered titania sample was reduced due to crystal transition.

Figure 1: Titania sample prior to and following sintering.
Figure 1:

Titania sample prior to and following sintering.

Table 1:

Geometry parameters of titania particles.

ParticleAverage particle size (μm)Specific surface area (m2/cm3)
Titania1.2496.615

Fine-grained reduced iron powder was the main experimental material utilized to melt into molten iron. In order to simulate the composition of molten iron in the actual BF, graphite powder, silica fume, manganese powder, and FeS (sulfur is volatile during heating) were mixed with the iron powder. The mixture was ground thoroughly with a mortal, in order to increase the contact between the particles, in order for the mixture to be completely melted when the temperature exceeds the corresponding liquidus temperature.

Reactor

A high-temperature tube furnace was employed for the heating of the materials to the desired temperature. The high-temperature tube furnace mainly consisted of two parts: the furnace body and the control cabinet. The schematic diagram of the furnace body is presented in Figure 2(a). The U-shaped MoSi2 rod was utilized as the heating element. A Pt-6 %Rh/Pt-30 %Rh thermocouple was placed under the protection crucible. Prior to the experiment initiation, a standard thermocouple was utilized to measure the constant-temperature zone and calibrate the temperature of the thermocouple inside the furnace. The constant-temperature zone was approximately 8 cm in length, whereas the highest accuracy area (± 1 ℃) was located at 3 cm above the crucible supporter, in order for the temperature measurement by the Pt-6 %Rh/Pt-30 %Rh thermocouple to match the actual temperature of molten iron.

Figure 2: Schematic diagram of experimental apparatus.
Figure 2:

Schematic diagram of experimental apparatus.

Experimental procedure

Approximately 160 g of the iron powder mixture was placed in an alumina crucible (36 mm I.D. and height 73 mm) or a graphite crucible (40 mm I.D. and height 80 mm). Consequently, the alumina crucible or the graphite crucible was placed into the protective crucible (67 mm I.D. and height 93 mm). The components of molten iron and experimental conditions of each experiment are presented in Table 2. The assemble was placed into the tube at room temperature and heated from room temperature to the desired temperature at a rate of 5 ℃/min. When the experiment started, high-purity argon gas (99.999 %) was introduced into the tube at a flow rate of 2 L/min, to protect the molten iron from potential reactions. When the temperature reached the desired value, the molten iron was stirred with a glass rod and the temperature was maintained for 30 min, to obtain a uniform composition of molten iron. Following this, the sintered titania sample was placed on the surface of molten iron through a thin iron wire (Figure2(b)). The reaction started and lasted for 120 min. Samples of molten iron were withdrawn with a glass tube (4 mm I.D.) every 30 min and quenched quickly in water for chemical analysis.

Table 2:

Chemical composition of molten iron and experimental conditions of each experiment.

NumberFe, Wt PctC, Wt PctSi, Wt PctMn, Wt PctS, Wt PctCrucibleTemperature, K
A-197.182.50.20.10.02Alumina1,773
A-296.183.50.20.10.02Alumina1,773
A-395.184.50.20.10.02Alumina1,773
A-494.68Saturated0.20.10.02Graphite1,773
B-1(A-3)95.184.50.20.10.02Alumina1,773
B-295.164.50.20.10.04Alumina1,773
B-395.144.50.20.10.06Alumina1,773
C-1(A-3)95.184.50.20.10.02Alumina1,773
C-294.984.50.40.10.02Alumina1,773
C-394.784.50.60.10.02Alumina1,773
D-1(A-3)95.184.50.20.10.02Alumina1,773
D-294.984.50.20.30.02Alumina1,773
D-394.784.50.20.50.02Alumina1,773
E-194.68Saturated0.20.10.02Graphite1,723
E-2(A-4)94.68Saturated0.20.10.02Graphite1,773
E-394.68Saturated0.20.10.02Graphite1,823

Results and discussion

Experimental results

Effect of element content in molten iron

Effects of different element contents in molten iron on the reduction of titania were investigated at 1,773 K. According to Figure 3, the titanium content in molten iron increased rapidly as the carbon content increased in the initial molten iron. The slope of each line corresponded to the reduction rate of titania. Therefore, it could be concluded that the reduction rate of titania increased along the higher carbon content. Figure 4 presents the reduction rate decreased along the increasing sulfur content. In a previous study [17], the surface tension of molten iron containing sulfur was measured, whereas the adsorption of sulfur was observed. The adsorption phenomenon of sulfur was considered to reduce the contact area between molten iron and solid titania inhibiting the reduction of titania.

Figure 3: Effect of carbon content.
Figure 3:

Effect of carbon content.

Figure 4: Effect of sulfur content.
Figure 4:

Effect of sulfur content.

Effect of silicon is presented in Figure 5. The reduction rate was irregular with the change of silicon content in molten iron, the reduction rate was high when the silicon content was 0.2 %, the reduction rate was maintained at a low level when the silicon content was 0.4 % or 0.6 %. The reduction rate increased along with the higher manganese content in molten iron, as presented in Figure 6, which demonstrated that manganese was a promoter of the reduction. This occurred mainly because the manganese decreased the viscosity of molten iron and promoted the diffusion of carbon in the molten iron.

Figure 5: Effect of silicon content.
Figure 5:

Effect of silicon content.

Figure 6: Effect of manganese content.
Figure 6:

Effect of manganese content.

Effect of temperature

Effect of temperature on the reduction of titania was investigated under the condition of saturated carbon content at 1,723 K, 1,773 K and 1,823 K (as presented in Figure 7). According to the results, the reduction rate of titania increased rapidly along with the higher temperature. Firstly, the solubility of carbon in molten iron increased with the higher temperature and the activity of carbon increased in molten iron. Secondly, the viscosity of molten iron decreased with the increasing temperature, and the kinetic condition of mass transfer in molten iron was improved. Hence, the temperature had the highest effect on the reduction of titania in the molten iron.

Figure 7: Effect of temperature.
Figure 7:

Effect of temperature.

As d[Ti]/dt indicated the reduction rate of titania, the reduction rate under different element content and temperature can be calculated as presented in Table 3. According to Table 3, when the carbon content increased by 1 %, the reduction rate increased by 0.008 %/h; when the sulfur content increased by 0.01 %, the reduction rate decreased by 0.004875 %/h; when the manganese content increased by 0.1 %, the reduction rate increased by 0.001125 %/h; when the temperature increased by 100 K, the reduction rate increased by 0.0235 %/h.

Table 3:

The reduction rate under different element contents and temperatures.

CThe element content, %2.53.54.5△[C]=1
The reduction rate, %/h0.0140.020.03△rate=0.008
SThe element content, %0.020.040.06△[S]=0.01
The reduction rate, %/h0.030.01250.0105△rate=0.004875
MnThe element content, %0.10.30.5△[Mn]=0.1
The reduction rate, %/h0.030.03250.0345△rate=0.001125
TemperatureTemperature, K1,7231,7731,823△T=100
The reduction rate, %/h0.02350.03350.047△rate=0.0235

Analysis and discussion

Thermodynamic analysis

The overall reaction of the reduction of titania in molten iron can be expressed as follows:

(1)(TiO2)+2[C]=[Ti]+2COΔGΘ=632210−302.09T(J/mol)

The carbothermal reduction of titania in molten iron was carried out step by step, where the reduction process was as follows: TiO2–Ti3O5–Ti2O3–TiO–Ti. When the titania was completely reduced and a surplus of carbon still existed, the following reaction occurred:

(2)[Ti]+[C]=TiC(s)ΔGΘ=−176,934+100.11T(J/mol)

The remaining titania was observed subsequently to each experiment which proved that the titania was not been completely reduced. Therefore, reaction (2) could not occur and no TiC was found in the molten iron or the tablet.

The XRD (X-ray diffraction) analysis was conducted on the reaction interface of the sintered titania prior to and following the experiments. The results are presented in Figure 8. From Figure 8, the phase at the reaction interface after the experiment was confirmed to be the Fe2Ti3O9(Fe2O3·3TiO2), which was considered to be the combination product between iron oxide and titania. The lower titanium oxides were not observed in the reaction, and this phenomenon was in agreement with the results reported by certain studies [18, 19] because the lower titanium oxides were unstable. Also, certain peaks were confirmed as graphite carbon. It could be inferred that a transition layer might exist at the interface during the experiments.

Figure 8: XRD pattern analysis prior to and following experimentation.
Figure 8:

XRD pattern analysis prior to and following experimentation.

Effect of elements interaction on reduction

The equilibrium constant of reaction (1) can be expressed by:

(3)K=a[Ti](Pco/PΘ)2a[TiO2]a[C]2

where K is the equilibrium constant of the chemical reaction; a[Ti] is the activity of titanium in molten iron; Pco is the partial pressure of CO; P is the normal atmospheric pressure; a[TiO2] is the activity of solid titania which is usually considered to be 1 and a[C] is the activity of carbon in molten iron.

When the overall reaction reaches equilibrium, the standard Gibbs-free energy of reaction (1) can also be expressed as:

(4)ΔGΘ=−RTlnK=−2.303RTlgK

For the equilibrium constant of reaction (1):

(5)lgK=lg[%Ti]+lgfTi+2lg(Pco/PΘ)−2lg[%C]−2lgfc

The titanium content in molten iron can be expressed by eq. (6) from eqs. (1), (4), and (5):

(6)lg[%Ti]=−33018.50T+15.78−lgfTi−2lg(Pco/PΘ)+2lg[%C]+2lgfC

It is known from eq. (6) that the temperature had the highest effect on the titanium content in molten iron. The experimental results agreed with the calculation. In addition, the viscosity of molten iron decreased as the temperature increased, described as [20]:

(7)μ=0.3699×10−3e41.4×103R(T+273)

where R is the gas constant.

Therefore, the kinetic condition of the mass transfer in molten iron was improved. Secondly, the wettability between solid titania and molten iron also improved, which could increase the contact area. Furthermore, the carbon content in molten iron was also temperature dependent, increasing along with the higher temperature. Consequently, the higher amount of titanium could be obtained with the higher temperature.

The activity coefficient in eq. (6) can be calculated by eq. (8), according to the Wagner model [21]:

(8)lgfTi=eTiTi[%Ti]+eTiC[%C]+eTiSi[%Si]+eTiMn[%Mn]+eTiS[%S]

It was apparent from eqs. (6) and (8) that the titanium content in molten iron was affected by the concentration of various elements in the molten iron and the activity interaction coefficients among the various elements. The activity interaction coefficients among various elements at 1,873 K are presented in Table 4.

Table 4:

Activity interaction coefficients among various elements at 1,873 K.

eijeTiTieTiCeTiSieTiMneTiSeCCeCSieCMneCS
Numerical value0.013−0.1650.050.0043−0.110.140.08−0.0120.016

The activity coefficient of titanium decreased with the increasing carbon content (activity interaction coefficient is negative), so the reduction rate increased. The carbon content had a higher effect relatively to the other elements, as it had the highest activity interaction coefficient. The activity coefficient of titanium increased along with the higher manganese content, so the reduction rate should have decreased, while the reduction rate increased along with the higher manganese content; this occurred mainly because the manganese decreased the viscosity of molten iron and promoted the diffusion of carbon in the molten iron. The activity coefficient of titanium decreased along with the higher sulfur content (activity interaction coefficient is negative), so the reduction rate should have increased, while the reduction rate decreased along with the higher sulfur content; the adsorption phenomenon of sulfur was considered to reduce the contact area between molten iron and solid titania inhibiting the reduction of titania.

Kinetics parameter calculation

The activity of carbon in molten iron can be written as eq. (9), and the activity coefficient can be calculated through eq. (10):

(9)a[C]=[%C]∗fC
(10)lgfC=eCC[%C]+eCSi[%Si]+eCMn[%Mn]+eCS[%S]

The activity interaction coefficients at different temperatures can be calculated through the activity interaction coefficients at 1,873 K:

(11)e(T)=e×1,873T

The activity of carbon under different carbon content at 1,773 K can be calculated, and d[Ti]/dt was linearly plotted against the activity of carbon in Figure 9. d[Ti]/dt indicated the reduction mass of titanium at unit time, that was the reduction rate of titania. Therefore, the reduction rate was linearly plotted against the activity of carbon.

Figure 9: Relation between d[Ti]/dt and ac at 1,773 K.
Figure 9:

Relation between d[Ti]/dt and ac at 1,773 K.

Consequently, the rate constants for the reduction of titania can be calculated through eq. (12) [11]:

(12)d[Ti]dt=AWk[Ti]a[C]

where [Ti] is the titanium content in molten iron, mass%; t is the reaction duration, h; A is the reaction area, m2; W is the weight of molten iron, kg; k[Ti] is the rate constant, kg m−2 h−1; a[C] is the activity of carbon in molten iron.

A transition layer might exist at the contact surface between the liquid and the solid as presented in Figure 11, whereas the mass transfer process resistance was concentrated in the transition layer. The exchange of substances was in equilibrium in the transition layer. The material flow density of the transport material component was proportional to the concentration difference of the component between the liquid and the transition layer. The fluid in the transition layer was stationary.

Figure 11: Explanatory view of transition layer.
Figure 11:

Explanatory view of transition layer.

The rate constants for the reduction of titania could be calculated at 1,723 K, 1,773 K and 1,823 K through the aforementioned equations. The rate constant increased rapidly as the temperature increased, as presented in Table 5. Simultaneously, the apparent activation energy was calculated as 209 kJ/mol through the linear fitting of lnk[Ti] and T−1, according to the Arrhenius equation (Figure 10).

Figure 10: Linear fitting of lnk[Ti] and T−1.
Figure 10:

Linear fitting of lnk[Ti] and T−1.

Table 5:

Rate constants for reduction of titania at 1,723 K, 1,773 K and 1,823 K.

Temperature, K1,7231,7731,823
The rate constant, kg m−2 h−10.4710.7131.05

Conclusions

In order to improve the reduction rate of titania in molten iron, experiments were carried out on the reduction of titania with a high-temperature tube furnace at 1,723–1,823 K. The following conclusions were obtained:

(1) When the carbon content, the manganese content and the temperature increased by 1 %, 0.1 % and 100 K, the reduction rate increased by 0.008 %/h, 0.001125 %/h and 0.0235 %/h, respectively; when the sulfur content increased by 0.01 %, the reduction rate decreased by 0.004875 %/h; the reduction rate was irregular with the change of silicon content in molten iron. The temperature had the highest effect on the reduction.

(2) The phase at the reaction interface after the experiment was confirmed to be the Fe2Ti3O9 which was considered to be the combination product between iron oxide and titania; the lower titanium oxides were unstable and hard to be observed.

(3) The reduction was affected by the concentration of various elements in molten iron and the activity interaction coefficients between various elements.

(4) The rate constants for the reduction of titania were calculated at 1,723 K, 1,773 K and 1,823 K. The apparent activation energy was calculated as 209 kJ/mol through the rate constants and temperatures according to the Arrhenius equation.

Funding statement: This work was financially supported by the National Science Foundation for Young Scientists of China (51704019), Major Science and Technology Program for Water Pollution Control and Treatment (2017ZX07402001), supported by the Fundamental Research Funds for the Central Universities (FRF-BD-17-010A) and (FRF-TP-17-040A1).

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Received: 2017-09-28
Accepted: 2018-07-30
Published Online: 2018-08-29
Published in Print: 2019-02-25

© 2019 Walter de Gruyter GmbH, Berlin/Boston

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

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  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
https://doi.org/10.1515/htmp-2017-0135
Keywords for this article
blast furnace; molten iron; titania; carbothermal reduction; reduction rate
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Articles in the same Issue

  1. Frontmatter
  2. Review Article
  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
  5. Correlation between Travel Speed, Microstructure, Mechanical Properties and Wear Characteristics of Ni-Based Hardfaced Deposits over 316LN Austenitic Stainless Steel
  6. Factors Influencing Gas Generation Behaviours of Lump Coal Used in COREX Gasifier
  7. Experiment Research on Pulverized Coal Combustion in the Tuyere of Oxygen Blast Furnace
  8. Phosphate Capacities of CaO–FeO–SiO2–Al2O3/Na2O/TiO2 Slags
  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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