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The effect of MgTiO3Adding on Inclusion Characteristics

  • Xu Chen , Zhang Mingya , Li Jianli , Ran Songlin , Shan Mengwei , Yue Qiang and Kong Hui EMAIL logo
Published/Copyright: May 11, 2019
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

MgTiO3 powder was directly added into molten steel at 1873K, and its effect on inclusion characteristics was studied by a scanning electron microscope and an energy dispersive spectrometer. Thermodynamic calculation indicates that MgTiO3 is unstable in molten steel and may decompose into [Ti], [O] and MgO. However, only Ti-bearing inclusions were observed in the treated sample, and Mg-bearing inclusions were absent. This can be explained by the features of wettability and stability for MgO. Compared with a Non-treated sample, both oxide and coarse MnS in treated sample were refined. For the oxide, this originates from the formation of Ti-bearing inclusion. For coarse MnS, this may be due to the fact that Ti can aggravate S segregation. Besides, this aggravation makes coarse MnS less globular. After etching, it was found that in the treated sample, Ti-bearing inclusion can induce the nucleation of intragranular acicular ferrites. This appearance was totally different from that of Non-treated sample, and indicates the effectiveness of external adding method in oxide metallurgy.

Keywords: oxide metallurgy; intragranular acicular ferrite; external adding method
PACS: 81.30.Mh

1 Introduction

In 1990, the concept of Oxides Metallurgy is proposed by Takamura and Mizoguchi [1]. Its key is to utilize fine inclusions to induce nucleation of intragranular acicular ferrite (IAF) during austenite-ferrite transformation. Because of the interlocking nature of IAF, its formation enhances both strength and toughness [2, 3].

Many kinds of inclusions have been suggested as effective sites for IAF nucleation, and their formation can be classified into Internal Precipitation Method (IPM) [4, 5] and External Adding Method (EAM) [6]. The former means that preferred inclusions generate either during de-oxidation or solidification processes. Thus precise control of steel composition and fine adjustment of production process are crucial. The latter means that pre-prepared particles are directly added into steel. So how to evenly distribute them in steel and make them as potential nucleation sites during phase transition is the focus of the research.

Recently, Ti-bearing and Mg-bearing inclusions have attracted much attention. The former is suggested as the most efficient inclusion for IAF nucleating, and the latter’s IAF nucleation effect is still under discussion. Thus, both of them are the hot topic of EAM study, and different methods have been developed, which is summarized respectively.

For Ti-bearing inclusion, three methods have been adapted. Firstly, Ti-bearing oxides and steel were bonded together at solid state [7, 8]. Secondly, Ti-bearing oxides were mixed with steel powder [9, 10] or put inside the hollow of steel cylinder [11, 12]. Then oxide and steel were melted almost simultaneously. Thirdly, Ti-bearing oxides were directly added into molten steel. For example, the

cored wire, which contains a high number density of oxides, was feed into molten steel by Grong et al. [13]. Moreover, different additives with metallic Ti and TiO2 were added into the steel melt just before casting or into the mold during casting to create Ti-bearing inclusions [14].

It can be seen that for the first and second methods, both as-sintered steel and co-melting of oxide and steel are totally different from actual steel-making process, which may limit their application. For the third method, the presence of acicular ferrite could not be confirmed definitely, and the holding time is required as short as possible to avoid particle floating.

For Mg-bearing inclusion, two methods have been adapted. Firstly, an approach for pre-dispersing MgO with AlSi alloy nanoparticleswas established, and the resulting nanoparticles were added into steel melt both in laboratory scale and real production [15, 16]. Secondly, chemical modification of the surface of MgO nanoparticles for steel-making was developed [17].

In this paper, MgTiO3 powder was introduced into molten steel for the first time to our knowledge. The aim is to utilize the decomposition reaction of MgTiO3 to release Mg/Ti into molten steel and play a role in IAF nucleation effect.

2 Experimental Procedure

The preparation of powder mixture consisted of two steps. Firstly, approximate MgTiO3 (Aladdin, purity > 99.9%, size < 2μm) and pure iron powder were weighted. Secondly, planetary ball milling was used to mix them for three hours in order to achieve homogeneous composition.

Commercial low-carbon steel (about 1500g) was used as raw material and put in an alumina crucible. The alumina crucible was located inside the graphite crucible in a high-heat tube-type resistance furnace. The experimental temperature was 1873K, and high purity argon gas was used as protecting gas during the melting experiment. The powder mixture was directly added into the molten steel and the mixture dissolved quick. Then after being held for 10 minutes at 1873K, the crucible was taken out. After solidification, steel sample was quenched into water. It should be mentioned that the surface of EAM-treated sample was smooth and no laminations were observed. Moreover, a comparison sample without EAM treatment was also prepared. The samples were sent to NCS Testing Technology Co., Ltd (China National Analysis Center for Iron and Steel) for composition analysis, and the content of Als and Ti were measured by the method of ICP-AES. The composition of both samples is shown in Table 1.

Table 1

Chemical composition of steel samples (mass percentage)

Mass Pct.CSiMnPSAlsTiMg
EAM-Treated Sample0.160.361.110.0330.0280.00210.00230.0006
Non-Treated Sample0.180.391.200.0220.0220.0008--

The morphology and composition of inclusions were characterized by scanning electron microscope (SEM: JSM-6510LV) and energy dispersive spectrometer (EDS: INCA Feature X-Max 20). In both samples, inclusions were classified as oxide and sulfide. The latter was pure MnS. In fact, MnS segregation, which heterogeneously nucleates on oxides, was also observed. This kind of inclusion was attributed as oxide.

The data processing for EDS point analysis was carried out following Wang Xinhua et al. [18]. Firstly, iron was excluded to eliminate the contribution of signals from steel matrix. Then oxygen was ruled out due to insufficient accuracy. Finally, the content of remaining elements was normalized to 100%, and reported in mass percentage. Beside point analysis, area mapping functions of EDS was also applied to intuitively characterize the distribution of each element in inclusion. This is helpful to reveal the inclusion complexity [19, 20, 21].

Software of INCA Feature was applied to automatically find and analyze inclusions in preselected area. It should be mentioned that the inclusion size is its Feret maximum, and the inclusion aspect ratio φ is the ratio of its Feret maximum to Feret minimum.

3 Results and discussion

Thermodynamic calculation of MgTiO3 in molten steel is carried out based on following equations [22, 23]:

(1)MgO⋅TiO2s=MgOs+TiO2sΔG1 θ =−2271200−157.5TJ⋅mol−1
(2)TiO2(s)=[Ti]+2[O]ΔG2θ=−675600+234T    J⋅mol−1

It should be mentioned that Ti in molten steel can form many oxides, such as TiO, Ti2O3, Ti3O5, and TiO2, and inconsistent results have been present. To simplify, equation (2) is applied. Thus, equation (3) can be derived:

(3)MgO⋅TiO2(s)=MgO(s)+[Ti]+2[O]ΔG3θ=−2946800+76.5T   J⋅mol−1

If the activities of MgO·TiO2(s) and MgO(s) are assumed as unity and the activity of [Ti] is simplified as its mass percentage, the ΔG3θis negative in 1873K even though the mass percentage of [O] is 1. Thus the deposition of MgO·TiO2(s) in molten steel may occur, which releases [Ti], [O] and MgO at the same time. To confirm this effect, systematic inclusion analysis has been conducted.

Based on SEM-EDS mapping analysis, the figures of typical oxide are shown in Figure 1 ((a) for Non-treated sample and (b) for EAM-treated sample). In Non-treated sample, the oxide was Mn-Si-Al-O. For EAM-treated sample, the elements of Ti, Mn, Si, and Al coexisted in oxide, while element of Mg was not found. In fact, the similar results have been also observed in our previous studies in addition of TiO2 and MgO, respectively. To confirm this characteristic, statistically analysis for inclusion has been carried out by INCA Feature software. The total number of measured inclusions in EAM-Treated Sample was 2080. Among them, only 5 Mg-bearing inclusions were observed. For these Mg-bearing inclusions, the Mg contents were all below 1%, and their sizes were all smaller than 1μm. As for Ti-bearing oxide, its number was much larger. Considering accuracy, only the inclusion, whose size was larger than 1μm, was taken into account. The resulting number was 1310. Among them, 35% inclusions (number percentage) can be classified as Ti-bearing oxide, and their average content of Ti was 14%.

Figure 1 SEM micrographs and EDS mapping images of various elements for typical oxide (a) For Non-treated sample (b) For EAM-treated sample
Figure 1

SEM micrographs and EDS mapping images of various elements for typical oxide (a) For Non-treated sample (b) For EAM-treated sample

Then a question should be answered: why only Ti-bearing inclusions were observed, nevertheless, Mg-bearing inclusions were absent? This can be explained by the wettability between molten steel and MgO.

In 2017, sessile drop method has been employed to study the wettability between liquid iron and sintered MgO substrate at 1823K by Ren et al. [24]. In their experiments, two iron samples were used, and their Al concentrations were 18 ppm and 370 ppm, respectively. The former sample’s results were used to analyze since the Al concentration in our sample was 21 ppm.

On the one hand, the stable contact angle between the sintered MgO substrate and the liquid iron was approximately 134∘ at 1823K. This means that in our sample with similar Al content, MgO is nonwetting with molten iron, and can easily float up. On the other side, EDS analysis indicated that the composition of iron sample surface after sessile drop experiment was relatively uniform Fe. However, the iron sample with 370 ppm Al was covered with an oxide layer. This hints that for the low Al sample, a reaction between MgO and liquid steel is difficult.

Based on upper two sides, the released MgO was absent in our sample. In fact, to introduce MgO into molten steel, special technology should be applied [15, 16, 17]. While for [Ti], it can easily react with other elements in molten steel, and simultaneously released [O] may accelerate these reactions. These lead to the formation of Ti-bearing oxides, which may refine the oxides.

To confirm this conclusion, the relationship between oxide size and number density in EAM-treated sample and Non-treated sample is present in Figure 2. Considering accuracy, only the oxide with size larger than 1μm,was taken into account. It can be seen that oxide was fined, and its number density was increased. This was consistent with upper analysis.

Figure 2 The relationship between oxide size and number density in EAM-treated sample and Non-treated sample
Figure 2

The relationship between oxide size and number density in EAM-treated sample and Non-treated sample

Except oxide, pure MnS was also observed in both samples, and their typical figures are shown in Figure 3 ((a) for Non-treated sample and (b) for EAM-treated sample). It’s known that due to high concentration of product (a[Mn]×a[S], a means the activity), MnS normally cannot form in molten steel. Based on origination, Zheng et al.’s [25] indicates that MnS may be classified as coarse (>1.5μm) and fine (<1μm). The former originates from the eutectic reaction during solidification, and the latter is attributed to the probable precipitation after complete solidification.

Figure 3 SEM micrographs and EDS mapping images for typical pure MnS (a) For Non-treated sample (b) For EAM-treated sample
Figure 3

SEM micrographs and EDS mapping images for typical pure MnS (a) For Non-treated sample (b) For EAM-treated sample

Since the external adding method is closely related to solidification, coarse MnS was our focus.

The relationship between coarse MnS size and number density in the EAM-treated sample and non-treated sample is shown in Figure 4. It can be seen that with EAM treatment, coarse MnS was refined, and its number density was increased. Moreover, the number percentage (aspect ratio 1<φ<2) has decreased from 87.5 to 79.4, which means that the adding of MgTiO3 makes coarse MnS less globular.

Figure 4 The relationship between coarse MnS size and number density in EAM-treated sample and Non-treated sample
Figure 4

The relationship between coarse MnS size and number density in EAM-treated sample and Non-treated sample

The contrary trend has been reported and explained by Zheng’s et al. [25]. They found that surfactants of Te can increase the percentage of coarse MnS (aspect ratio 1<φ<2) and decrease its number density. Based on their theory, our results can be well explained, which is shown bellowing in brief and divided into following five parts.

Firstly, Sulfur segregation is the key to MnS precipitation since S (partition coefficient ks = 0.05) [26] segregates much easier than Mn (ks = 0.76) [26] during solidification.

Secondly, since the content of Ti is only about 23 ppm, its effect on activity coefficient of Sulfur can be negligible.

Thirdly, since Ti doping decreases the surface tension of liquid iron [27], it preferentially accumulates at the liquid-solid steel interfaces as surfactant.

Fourthly, Zheng et al. [25] pointed out that due to fast solidification, solute concentration in the newly formed solid monolayer is in excess of the equilibrium solubility. Then, the solute will diffuse back to the liquid phase across the interface because of its supersaturated state. Thus it’s feasible to assume that surfactant, which accumulates at solid-liquid interface, could affect mass transfer rate across interface [28, 29].

Fifthly, the interaction between S and Ti is stronger than that of between Fe and S. This is confirmed by the negative interaction coefficient eSTi(−0.27,JSPS).Based on Zheng’s discussions [25], this may increase vacant sites for adsorption, accelerating solute back-diffusion from the solid phase to the liquid phase across the solid-liquid interface. This would aggravate the segregation of Sulfur into the interdendritic regions, and increase its supersaturation.

Thus, Ti doping made coarse MnS less globular and higher density. This trend is contrary to Te doping effect. This is due to the fact that the interaction between S and Te is weaker than that of between Fe and S, which is contrary to Ti property.Moreover, since Te is extremely surface active in liquid steel [30], its effect on coarse MnS is more obvious than that of Ti.

Figure 5(b) describes SEM micrograph and EDS mapping images of typical Ti-bearing oxide in EAM-treated sample after etching in 3Vol%Nital solution. It can be seen that IAF plates initiates from a single Ti-bearing inclusion. This phenomenon was similar to the induced nucleation effect of Ti-bearing inclusion originating from IPM method [4], and totally different from that of Non-treated sample (shown in Figure 5(a)).

Figure 5 SEM micrograph and EDS mapping images for typical oxide after etching (a) For Non-treated sample (b) For EAM-treated sample
Figure 5

SEM micrograph and EDS mapping images for typical oxide after etching (a) For Non-treated sample (b) For EAM-treated sample

Figure 1(b) has indicated that with EAM treatment, Ti-bearing oxides were formed. Till now, different mechanisms have been proposed to explain the reasons why Ti-bearing inclusion can promote IAF nucleation [2], such as inert surface, lattice disregistry, thermal coefficient, and Mn-depletion zone (MDZ). Among them, MDZ mechanism has been widely accepted. This mechanism is based on the assumption that inclusions can absorb neighboring Mn atoms from Fe matrix. If a corresponding supplement isn’t applied, Mn depleted zone will be formed in Fe matrix around inclusion. This promotes the nucleation of ferrites since Mn element is the stabilizer of austenite.

In 2018, Li et al. [20] indicates that in Al-Ti-Mg killed steel with low Al content, MDZ is formed by the combined effect of the precipitation of MnS and diffusion of Mn atoms into TiOx and MgTiOx. In EAM-treated sample, Al content was as low as 21ppm and Ti-bearing oxide was also found. This hint that a similar absorption may occur, which promote acicular ferrite nucleation. While in the Non-treated sample, no Ti-bearing oxides were found. The difference of inclusion characteristic leads to the different microstructure in two samples.

4 Conclusion

MgTiO3 powder was directly added into molten steel, and its effect on inclusion characteristic has been explored. At 1873K, MgTiO3 may decompose into [Ti], [O] and MgO, which results in the formation of Ti-bearing complex inclusions and the refinement of oxide. While for MgO, its wettability and stability leaded to the absent of Mg-bearing inclusion. Compared with a Non-treated sample, coarse MnS in the EAM-treated sample became less globular and higher density. This may be interpreted by the fact that Ti can aggravate S segregation. After etching, IAF plates have been observed in the EAM-treated sample, which is induced by Ti-bearing inclusions. This appearance was consistent with the Ti-bearing inclusion originating from internal precipitation method, and indicates the effectiveness of external adding method in oxide metallurgy.

Acknowledgement

This work was supported by the National Natural Science Foundation of China (No.51474001), the State Key Laboratory of Refractories and Metallurgy, Wuhan University of Science and Technology (No. G201710), Anhui Provincial Natural Science Foundation (No.1608085J10), Financial support for academic and technical leaders (No.2016H092), Open fund of Key Laboratory of Metallurgical Emission Reduction & Resources Recycling (KF17-3), and Anhui University of Technology graduate innovation research (No. 2017148).

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Received: 2018-12-10
Accepted: 2018-12-25
Published Online: 2019-05-11
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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  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-2019-0004
Keywords for this article
oxide metallurgy; intragranular acicular ferrite; external adding method
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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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