Home Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
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Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3

  • Yi-ci Wang , Wen-bin Xin EMAIL logo , Xiao-geng Huo , Guo-ping Luo and Fang Zhang
Published/Copyright: July 29, 2019
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

In this study, the blast furnace slag of the Baotou Steel and Iron Company was used as the main raw material to prepare glass ceramics with diopside as the main crystal phase. The composition of the parent glass was designed by thermodynamic calculations with FactSage software. Small amounts of the nucleation agent Cr2O3 were then added to the parent glass to induce crystallization. Differential thermal analysis was used to determine the nucleation and crystallization temperatures of the glasses, and scanning electron microscopy and X-ray diffraction were adopted to determine the microstructures and phase compositions of the glasses after heat treatment, respectively. The results showed that glass ceramics of the diopside phase can be prepared with up to 73 wt% blast furnace slag when 1.44–1.91 wt% Cr2O3 is added, and the ceramics have uniform compact grains and a high bending strength of about 84.6–101.7 MPa. In addition, the mechanical properties are better than those of natural marble and granite. These results provide basic information and a scientific basis for industrial production of diopside glass ceramics using molten blast furnace slag as the main raw material.

Keywords: glass ceramics;; blast furnace slag;; nucleation agents;; Cr2O3

Introduction

The blast furnace (BF) slag is the highest quantity metallurgical slag in the iron and steel industry, which has been used as the main raw material to produce cement. Although its utilization ratio has reached 78% in China, its additional value is rather low [1, 2]. In recent years, investigation of glass ceramics prepared from solid waste, such as BF slag, tailings, and fly ash, has gradually become an important issue [3, 4]. It is important to prepare glass ceramics using molten BF slag to improve utilization and the added value of iron smelting slag, reduce energy consumption, increase the economic benefit, and alleviate environmental pollution. In BF slag, the mass percentage of CaO, SiO2, Al2O3 and MgO is about 90%, which is the ideal raw material for preparing glass ceramics. Glass ceramics with diopside or wollastonite as the main crystal phase have high strength and good chemical resistance. Therefore, they are widely used as building decoration materials [5, 6]. Because of the low crystallization capacity of the glass [7], it is necessary to add a small amount of nucleating agents to promote precipitation of diopside and wollastonite. Omara et al. [8] suggested that addition of Cr2O3 as a nucleating agent can promote precipitation of diopside or wollastonite from the CaO–Al2O3–SiO2–MgO glass system. However, Erkmen et al. [9] showed that the crystalline phases only exist on the surface of the sample, and akermanite (2CaO·MgO·2SiO2) and gehlenite (2CaO·Al2O3·SiO2) are the main crystallization phases when glass ceramics produced from BF slag are added with 5 wt% TiO2, 10 wt%TiO2, and 5 wt% TiO2 + 5 wt% Cr2O3. Yang et al. [10] found that when a high proportion of BF slag is introduced, scum is generated in the liquid glass surface layer during the melting process and both phase separation and crystallization of the glass are difficult. Similar problems have also been encountered in many other studies. Therefore, the mass ratio of BF slag should be limited to less than 50%, which leads to lower utilization efficiencies for the slag and its latent heat. Thus, it will lead to high cost and energy consumption for industrial production of glass ceramics when molten blast BF slag is used as the main raw material. To overcome the above problems, in this study, preparation and the properties of BF slag glass ceramics containing Cr2O3 were investigated for mixtures containing of more high proportion of molten slag. The results will provide a scientific basis for industrial production of diopside glass ceramics using molten BF slag as the main raw material.

Materials and methods

Raw materials

The main raw materials for preparation of the parent glass were BF slag, quartz sand, and small amounts of the analytical reagents CaO, MgO, and Al2O3. Table 1 presents the chemical composition of BF slag used. CaO and Al2O3 powder were provided by the third chemical reagent plant (Tianjin, China), MgO powder was provided by Yongda chemical reagent company (Tianjin, China). First, the particles of each raw material were ground to sizes smaller than 0.074 mm. The raw materials were then completely mixed with addition of a small amount of Cr2O3 as a nucleating agent to promote crystallization of the glass. The added amount of Cr2O3 in each sample is shown in Table 2.

Table 1:

Chemical composition of the BF slag provided by the iron plant of the Baotou iron and steel company (wt%).

SiO2CaOMgOAl2O3FeONa2OK2OFTiO2Others
34.0637.799.6713.081.650.340.310.270.931.90
Table 2:

Mass percentage of raw material for the six samples containing Cr2O3 and the prepared glass composition (wt%).

Mass percentage of raw materialChemical composition of the prepared glass
No.BF slagQuartz sandCaOAl2O3MgOCr2O3CaOSiO2Al2O3MgOCr2O3FeONa2OK2OOthers
172.9622.781.840.891.530.0029.4147.6310.438.590.001.200.250.232.26
272.9722.541.680.841.490.4829.2647.3910.388.550.481.200.250.232.26
372.9922.301.530.781.440.9629.1147.1610.338.500.961.200.250.232.26
472.9822.071.380.731.401.4428.9646.9310.288.461.441.200.250.232.26
573.0021.831.240.671.351.9128.8346.6910.228.411.911.200.250.232.26
672.9621.591.140.621.312.3728.7146.4410.168.372.371.200.250.232.26

Preparation of the parent glass

Mixtures were prepared according to the ratios in Table 2. The mixtures were then completely mixed, placed in corundum crucibles, and melted in a furnace at 1450°C for 3 h using Si–Mo rods as heaters. The furnace was heated from room temperature to 200°C at a heating rate of 10°C/min, from 200 to 1000°C at a heating rate of 8°C/min, and from 1000 to 1450°C at a heating rate of 4°C/min. The melts were then poured into steel molds. The molds containing the cooled melts were placed in another furnace and held at 600°C for 2 h. The glasses were obtained after the annealing process.

Detection and analysis methods

Differential thermal analysis

Differential thermal analysis (DTA) was performed to determine the nucleation and crystallization temperatures of the glasses. The thermal variations of the phase transformations were analyzed using about 10–15 mg powdered glass samples. The α-Al2O3 powder was used as a reference material in the temperature range from room temperature to 1250°C in an argon atmosphere at a heating rate of 10°C/min.

X-ray diffraction

An X-ray diffractometer (D8 ADVANCE, Germany) was used to identify the crystalline phases present in the glass samples after heat treatment. The particle sizes of the samples were ground to sizes less than 200 mesh and the experimental conditions were a copper target, a working voltage of 40 kV, a working current of 80 mA, a scanning angle range of 20°–80°, and a scanning angular velocity of 3°/min.

Scanning electron microscopy

Scanning electron microscopy (SEM) was performed with an S-3400 scanning electron microscopy (Japan) to observe the microstructures of the glass samples after heat treatment. The polished surfaces of the samples were corroded by hydrofluoric acid (4 vol%) for 40 s and then observed after gold sputtering treatment.

Determination of the flexural strength

The flexural strengths of the samples after heat treatment were determined using an electronic universal testing machine (CSS-88000) by the three-point bending method. The sizes of the samples were 40 mm (length) × 4 mm (width) × 3 mm (height). The reported flexural strengths are the average of measurements for 3–6 samples.

Results and discussion

Thermodynamic prediction of the crystallization mineral composition of the parent glass

FactSage software contains a thermodynamic database with rich information and it has a powerful calculating function under the Windows operating system [11]. First, the Equilib module of the software was used to calculate the amounts of the crystallization minerals if the parent glass sample was heat treated in the temperature range 1000–1100°C. The calculated results are given in Table 3.

Table 3:

Mass percentages of the crystallization minerals for the parent glass calculated by Factsage (wt%).

Chemical composition of the parent glassCalculated crystallization minerals
CaOSiO2Al2O3MgODiopsideWollastoniteAkermaniteAnorthite
314911950.3–51.223.7–24.27.0–7.218.1–18.3

If the parent glass containing 31 wt% CaO, 49 wt% SiO2, 11 wt% Al2O3, and 9 wt% MgO in Table 3 completely changes into crystallization minerals, the mass percentages of the different minerals are 50.3–51.2 wt% diopside (CaMg(SiO3)2), 23.7–24.2 wt% wollastonite (CaSiO3), 7.0–7.2 t% akermanite (Ca2Mg(Si2O7)), and 18.1–18.3 wt% anorthite (Al2Ca(SiO4)2) when the parent glass is heat treated at 1000–1100°C, in which the main crystal phases were diopside and wollastonite phase. Chemical composition design of the parent glass can ensure that diopside and wollastonite are the main crystal phases, so the chemical composition in Table 3 was selected to prepare the glass ceramics.

Nucleation and crystallization temperatures of the glasses containing Cr2O3

Precipitation of a new phase (crystal nucleus) from the parent glass is an endothermic process, but transformation of the glass from amorphous to crystalline is an exothermic process [12]. According to the Tammann curves, the endothermic and exothermic peaks in the DTA curve represent nucleation and crystallization of glass, respectively. That is, the crystal nuclei will precipitate close to the temperature corresponding to the endothermic peak and crystals will grow at the temperature corresponding to the exothermic peak. In addition, the sharper the exothermic peak, the higher the crystallization rate.

The DTA curves of the glasses containing different mass percentages of Cr2O3 as a nucleating agent are shown in Figure 1. It can be seen that there is an inconspicuous endothermic peak and obvious clear exothermic peak in each DTA curve. The temperatures corresponding to the inconspicuous endothermic peaks in the DTA curves (765–768°C) are the glass transition reactions. This shows that the added amount of Cr2O3 hardly affects the nucleation temperature of the glass, but it has a clear influence on the crystallization temperature. The significant exothermic peaks at 1113, 1109, 1061, 1068, 1028, and 1008°C for samples 1–6, respectively, are the crystallization temperature, which clearly decreases as the amount of Cr2O3 gradually increases from 0 to 2.37 wt%. When the amount of Cr2O3 is less than 0.48 wt% (samples 1 and 2), the crystallization peak temperatures are higher than 1100°C, the peak areas are small, and the peak shapes are not sharp. Thus, crystallization is difficult when the glass samples are heat treated at their exothermic peak temperatures. However, when the amount of Cr2O3 is 0.96, 1.44, 1.91, or 2.37 wt%, the exothermic peaks are sharper and their peak temperatures are lower than 1100°C. The DTA results show that the nucleating agent Cr2O3 promotes crystallization of the glass. Cr3+ in the glass attracts non-bridged oxygen atoms and makes peripheral cations form an oriented arrangement. Furthermore, it makes heterogeneous nucleation of the Cr-enriched phase easy, which induces crystals to form. Therefore, the crystallization peak temperature decreases [13].

Figure 1: DTA curves of the glass samples containing Cr2O3.
Figure 1:

DTA curves of the glass samples containing Cr2O3.

Mineral composition of the glasses containing Cr2O3 after heat treatment

According to related studies [14, 15, 16], the optimum nucleation temperature is usually 30–70°C higher than the glass transition temperature and the crystallization temperature is close to the exothermic peak temperature in the DTA curve. In this study, the nucleation temperature of the glass is determined to be 60°C higher than its glass transition temperature. The six glass samples (1–6) were heat treated for 1 h at their nucleation temperatures (827°C, 825°C, 827°C, 828°C, 827°C, and 826°C) and crystallization temperatures (1113°C, 1109°C, 1061°C, 1068°C, 1028°C, and 1008°C). The XRD patterns of the glass samples after heat treatment are shown in Figure 2.

Figure 2: XRD patterns of the glass samples containing Cr2O3 after heat treatment.
Figure 2:

XRD patterns of the glass samples containing Cr2O3 after heat treatment.

From the thermodynamic calculation, when the designed parent glass is heat treated at a temperature of 1000–1100°C, the mineral mass percentages are 50.3–51.2 wt% diopside (CaMg(Si2O6)), 23.7–24.2 wt% wollastonite (CaSiO3), 7.0–7.2 wt% akermanite (Ca2Mg(Si2O7), and 18.1–18.3 wt% anorthite (Al2Ca(SiO4)2). It can be seen that diopside and wollastonite are the main crystal phases. However, the XRD pattern of the sample without Cr2O3 (sample 1) in Figure 2 shows that Ca2Mg(Si2O7) is the main crystal phase that precipitated from the glass sample, and there are also peaks for Ca(Mg,Al)(Si,Al)2O6 and Al2Ca(SiO4)2. Ca(Mg,Al)(Si,Al)2O6 and CaMg(Si2O6) have a similar structure and properties, and they can be regarded as the same type of mineral. Therefore, the detected mineral species are consistent with the calculated results. However, based on the estimation of XRD peak intensity, the amounts of the Ca(Mg,Al)(Si,Al)2O6 phase ranges from 74.5 to 80.0 wt%, different from its thermodynamic calculated value of 50.3–51.2 wt%.

The glass includes the four chemical components CaO, SiO2, Al2O3, and MgO, with 73 wt% of the chemical components coming from BF slag. According to many studies [17, 18], most of the chemical components exist as Ca2Mg(Si2O7) complex oxides in the slag. Although 27% of these chemical components are introduced as free oxides, they hardly affect precipitation of Ca2Mg(Si2O7) from the glass. Therefore, the main crystal phase of the glass samples after heat treatment is Ca2Mg(Si2O7) rather than CaMg(Si2O6).

When the mass percentage of Cr2O3 is in the range 0.48–1.91 wt% (samples 2–5), Ca(Mg,Al)(Si,Al)2O6 becomes the main crystal phase, which can be regarded as CaMgSi2O6, but the Ca2Mg(Si2O7) phase are not detected revealed by the XRD patterns in Figure 2. Thus, the nucleating agent affects the mineral composition of the glass after heat treatment. When the mass percentage of Cr2O3 is 2.37 wt%, from the XRD pattern of sample 6, the diffraction peaks of Ca(Mg,Al)(Si,Al)2O6 become weaker, but those of Ca2Mg(Si2O7) appear again. Therefore, Cr2O3 can promote generation of heterogeneous nucleating positions and improve nucleation of glass, which can promote precipitation of Ca(Mg,Al)(Si,Al)2O6 crystals. However, the mass percentage of Cr2O3 should be controlled in the range 0.48–1.91 wt% to obtain the expected main crystal phase.

Microstructures of the glass ceramics containing Cr2O3

SEM images of the glass ceramic samples containing 0, 1.44, 1.91, and 2.37 wt% Cr2O3 (samples 1, 4, 5, and 6) are shown in Figure 3. For sample 1 without any nucleating agent, there are many microcracks and a few unevenly distributed large crystal grains. This is because of the higher crystallization temperature and weaker crystallization ability of the glass. The irregular grains of samples 4 and 5 are dense and uniform and the grain size is about 2–3 μm. Because it contains more nucleating agent, the grains of sample 5 are more compact than those of sample 4. However, precipitation of grains is unfavorable if the glass contains a large amount of Cr2O3. For sample 6 containing 2.37 wt% Cr2O3, neither the distribution of the grains nor their sizes are uniform, because a large amount of Cr2O3 makes the molten glass glutinous, which inhibits precipitation of crystals [19]. Therefore, the mass percentage of Cr2O3 should be controlled in the range 1.44–1.91 wt% to obtain a green glass ceramic with an ideal microstructure. According to the above analysis, the high field strength chromium ions (Cr3+) obtained from Cr2O3 in an oxidizing atmosphere make the ambient ions order. In addition, the solubility of Cr2O3 is very low and most of the Cr2O3 will exist as solid particles in the molten glass and form many tiny crystal nuclei [20]. Therefore, Cr2O3 promotes precipitation of diopside crystals when its mass percentage is lower than 1.91 wt%.

Figure 3: SEM images of the samples after heat treatment: (a) sample 1, (b) sample 4, (c) sample 5, and (d) sample 6.
Figure 3:

SEM images of the samples after heat treatment: (a) sample 1, (b) sample 4, (c) sample 5, and (d) sample 6.

Flexural strengths of the glass ceramics containing Cr2O3

The flexural strength is a very important factor for the performance of glass ceramics. The flexural strengths of the glass ceramic samples were determined by the three-point bending method, and the results are given in Figure 4. It is seen that the flexural strength firstly increases and then decreases with increasing amount of Cr2O3. The flexural strength of the sample containing 1.91 wt% Cr2O3 is the highest (101.7 MPa), followed by the sample containing 1.44 wt% Cr2O3 (84.6 MPa). The flexural strength of the sample containing 2.37 wt% Cr2O3 is even lower (56.5 MPa) than the sample containing 1.44 wt% Cr2O3.

Figure 4: Flexural strengths of the samples after heat treatment.
Figure 4:

Flexural strengths of the samples after heat treatment.

The flexural strengths of the samples are closely related to their microstructures. The higher flexural strengths of samples 4 and 5 (containing 1.44 and 1.91 wt% Cr2O3, respectively) are because of the uniformly distributed compact grains. For samples 1 (containing no nucleating agents) and 6 (containing 2.37 wt% Cr2O3), the flexural strengths are lower because they have microcracks, a low crystallization rate, or a heterogeneous crystal grain distribution. The flexural strength of natural granite is 15–38 MPa and that of natural marble is 7–19 MPa [21]. In comparison, the glass ceramics reported in this study have good mechanical properties, with flexural strengths of 84.6–101.7 MPa for mass percentages of Cr2O3 of 1.44–1.91 wt%. Thus, the mechanical strengths of the glass ceramics are much higher than those of natural granite and natural marble [21].

It is feasible that a technique can be developed to produce glass ceramics with high added value using molten BF slag as the main raw material. This is of great significance for improving utilization and the added value of iron smelting slag and reducing environmental pollution.

Conclusions

  1. Parent glass composed of 31 wt% CaO, 49 wt% SiO2, 11 wt% Al2O3, and 9 wt% MgO has been designed by thermodynamic calculations. Among the raw materials, the mass percentage of the BF slag is up to 73%, and the other raw materials are quartz sand and small amounts of pure chemical reagents. When the mass percentage of Cr2O3 is 1.44 or 1.91 wt%, glass ceramics of the diopside phase with uniform crystal grains can be prepared.

  2. The nucleating agent Cr2O3 has a clear effect on the crystallization temperature of the parent glass, which gradually decreases with increasing mass percentage of Cr2O3, and Cr2O3 also promotes crystallization of the glass.

  3. In the process of preparing glass ceramics from BF slag, Cr2O3 promotes precipitation of diopside crystals. When the mass percentage of Cr2O3 is in the range 0.48–1.91 wt%, the expected main crystal phase Ca(Mg,Al)(Si,Al)2O6 precipitates from the parent glass.

  4. When the mass percentage of Cr2O3 is controlled within the range 1.44–1.91 wt%, a microstructure composed of compact uniform grains can be obtained. The sizes of the crystal grains are about 2–3 μm. The flexural strengths of the glass ceramics are 84.6–101.7 MPa and their mechanical strengths are much higher than those of natural granite and natural marble.

Acknowledgements

This work was financially supported by the Natural Science Foundation of Inner Mongolia (Grant No. 2018LH05026), National Natural Science Foundation of China (Grant No. 51364030) and Key Research Projects of Inner Mongolia Colleges and Universities (Grant No. NJZZ16153 and Grant No. NJZZ157).

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Received: 2018-05-09
Accepted: 2018-12-09
Published Online: 2019-07-29
Published in Print: 2019-02-25

© 2019 Wang et al, published by De Gruyter

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

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  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-2019-0029
Keywords for this article
glass ceramics;; blast furnace slag;; nucleation agents;; Cr2O3
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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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