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Microstructure, phase composition and oxidation behavior of porous Ti-Si-Mo intermetallic compounds fabricated by reactive synthesis

  • Jinming Ru EMAIL logo , Ya Wang , Yuemei Wang and Xiaojing Xu
Published/Copyright: February 28, 2020
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 39 Issue 1

Abstract

Porous Ti-Si-Mo intermetallic compounds were fabricated by reactive synthesis using C7H10N2O2S as a foaming agent. The effects of Mo content on the microstructure, phase composition and oxidation behavior were investigated. The results show that the porosity and the fractal dimension decreases and then increases as the Mo content increases. It is found that the pore size is mainly distributed in less than 1μm. The phase compositions mainly consist of TiSi, Ti5Si4, Mo5Si3 and TiO, and the Ti5Si3 phase is detected at Mo content of 16 wt.% in particular. In addition, the mass gain of the oxidized samples gradually decreases as the Mo content increases. It is concluded that the oxidation resistance at high-temperature generally decreases as the fractal dimension increases. It is suggested that porous Ti-Si-Mo intermetallic compounds have potential applications in sound absorption and heat dissipation at high-temperature.

Keywords: porous Ti-Si-Mo intermetallic compounds; reactive synthesis; microstructure; phase composition; oxidation resistance

1 Introduction

Porous materials with open pores possess many attractive properties such as low weight,high permeability, high thermal conductivity and high specific surface area and have wide applications in sound absorption, heat dissipation, filtration, separation and catalyst support because of the capillary structure of the open and small pores acting as fluid channels [1, 2, 3]. However, the applications of porous materials are relatively limited in adverse environments, such as porous ceramics with brittleness and poor weldability, porous metals with poor high-temperature oxidation resistance and porous polymers with poor aging resistance and high-temperature resistance [4, 5, 6]. Carbon-carbon composites, superalloys and intermetallic compounds are currently widely applied in the high-temperature environment. Carbon-carbon composites have restricted applications because of their poor oxidation resistance [7]. The extreme working temperature of superalloys such as nickel-based alloys is approximately 1523 K. By comparison, porous intermetallic compounds show advantages of excellent oxidation resistance and high working temperature [8]. Aluminides and metal silicides are typical intermetallic compounds and have been extensively investigated and applied. Al-based intermetallic compounds have low working temperatures of 1173~1373 K to be used as high-temperature structural materials because of their lower melting point [9]. However, refractory metal silicides are widely used as high-temperature structural materials due to their excellent performance at high-temperature. Ti-Si based intermetallic compounds have lower density and Mo-Si based intermetallic compounds have improved high-temperature oxidation resistance in refractory metal silicides [10, 11].Moreover, the addition of Mo could improve the mechanical strength and room temperature plasticity of Ti-Si based intermetallic compounds [12]. Burk et al. [13] synthesized the intermetallic compound of Mo-37Si-40Ti (at.%) in order to obtain nearly single-phase (Mo,Ti)5Si3. The intermetallic compound Mo-37Si-40Ti possessed superior high-temperature oxidation resistance compared to both single-phase Mo5Si3 and single-phase Ti5Si3 due to the formation of a protective SiO2-TiO2 duplex scale. It’s important to consider the advantages of two kinds of metal silicides in the integration and development of new porous Ti-Si-Mo intermetallic compound materials. Yang et al. [14] established the isothermal sections of the Mo-Si-Ti system to describe the solid-state phase equilibrium. The thermodynamic modeling satisfactorily explained the available experimental observation, and two invariant reactions close to the metal-rich region of the Mo-Si-Ti system, which are important in developing high-temperature structural materials, were calculated from this thermodynamic modeling. Porous Ti-Si-Mo intermetallic compounds have the potential for applications in high-temperature oxidative environments.

Porous intermetallic compounds can be prepared by powder metallurgy techniques, such as hot isostatic pressing, reactive synthesis, combustion synthesis, mechanical alloying and thermal or plasma spraying. Reactive synthesis and combustion synthesis have been applied to prepare various intermetallic compound materials. Feng et al. [15] produced porous titanium silicides with an open porosity ranging from 17% to 55% by combustion synthesis from elemental powders of Ti to Si in varying molar ratios. It was concluded that the formation of pores resulting from the melting and flow of reactants or products with low melting points during the combustion process is an especially rapid synthesis process. Gao et al. [16] prepared porous Fe-Al intermetallics with an open porosity of approximately 40% by the reactive synthesis of Fe and Al elemental powders. The liquid Al reaction and the phase transformation during sintering partly resulted in forming pores.He et al. [17] fabricated Ti-Al micrometer/nanometersized porous alloys with adjustable pore sizes ranging from the micrometer to nanometer scale via the Kirkendall effect, and the open porosity ranged from 40% to 60%. Pore formation resulted from the Kirkendall effect due to the different diffusion rates of different elements [18]. It was concluded that the low diffusion rate of Mo atoms in the Ti-Mo diffusion couples results in the formation of pores [19]. Porous intermetallic compounds fabricated by reactive synthesis and the Kirkendall effect possess higher porosity and a wide pore size distribution range. Hence, the reactive synthesis and Kirkendall effect have advantages for the production of porous intermetallic compounds.

In this paper, porous Ti-Si-Mo intermetallic compounds are produced via reactive synthesis using C7H10N2O2S as a foaming agent. This study will focus on the porous structure and oxidation behavior. The effects of the Mo content on the microstructure and high-temperature oxidation behavior were investigated.

2 Experimental

2.1 Material Preparation

The typical processing of porous Ti-Si-Mo intermetallic compounds fabricated by reactive synthesis involved four steps: ball milling, pressing, foaming and sintering. After several attempts, titanium (200-300 mesh, 99.0% purity), silicon (200 mesh, 99.9% purity) and molybdenum (200 mesh, 99.0% purity) elemental powders were mixed in four different mass ratios: (a) Ti-8Si-12Mo, (b) Ti-8Si-14Mo, (c) Ti-8Si-16Mo and (d) Ti-8Si-18Mo respectively, considering the forming performance during the sintering procedure and various performances such as fracture toughness of the sintered samples. The powder mixtures were high-energy ball milled in a planetary ball mill in the air for 48 h using agate balls without milling media. The ball-to-powder weight ratio was 10:1 and the speed of the planetary ball mill was 500 r/min. The SEM images of Ti-Si-Mo powder mixtures before and after ball milling, as shown in Figure 1. It is can be seen that Ti-Mo-Si powders with particle size in the range of submicron and micron scales could be obtained by ball milling with Ti powders with particle size of 50 μm, Mo powders with particle size of 5 μm and Si powders with particle size in the range of 5 μm – 25 μm as raw materials. After adding 2 wt.% C7H10N2O2S (>98.0% purity) with particle size of approximately 75 μm into the powder mixtures as a foaming agent, the powder mixtures were ball milled in the planetary ball mill for 30 min at the speed of 200 r/min to be more uniform. The powder mixtures were then cold-pressed into cylindrical compacts with the size of ϕ30×3 mm under 50~100 MPa pressure. Before sintering, the compacts were dried at 383 K in vacuum of 10−1 Pa for 2 h to remove C7H10N2O2S. Finally, the green compacts weresintered at 1123 K for 2 h and then at 1473 K for 4 h under a vacuum of 10−1 Pa with a heating rate of 4 K/min throughout the sintering procedure.

Figure 1 The SEM images of Ti-Si-Mo powder mixtures before and after ball milling: (a) Ti powders before ball milling; (b) Mo powders before ball milling; (c) Si powders before ball milling; (d) Ti-Si-Mo powders after ball milling
Figure 1

The SEM images of Ti-Si-Mo powder mixtures before and after ball milling: (a) Ti powders before ball milling; (b) Mo powders before ball milling; (c) Si powders before ball milling; (d) Ti-Si-Mo powders after ball milling

2.2 Characterization

The microstructure of the sintered and oxidized samples was observed using a scanning electron microscope (SEM, JSM-IT300) operated at 10.0 kV. A Micromeritics’ AutoPore IV 9510 automatic mercury porosimeter was employed to characterize the porosity and pore size distribution. The phase composition of the sintered and oxidized samples was detected by a D8-Advance X-ray diffraction (XRD) with a scanning angle of 20°~90° and a scanning speed of 5°/min. High-temperature oxidation behavior of the samples was tested in a Muffle furnace at 1473 K for 100 h. The mass gain of the oxidized samples was measured using an electronic analytical balance every 20 h. The fractal dimension was calculated by Eq. (1) [20].

(1)D=3−ln⁡ϵ/ln⁡(rmin/rmax)

where ∈ is the porosity and, rmin and rmax are the smallest and largest pore radius, respectively.

3 Result and discussions

Table 1 summarizes the pore structure and oxidation behavior of samples with different Mo contents. The open porosity of the sintered samples decreases from 44.18% to 40.58% and then increases to 42.54% and the fractal dimension decreases from 2.891 to 2.880 and then increases to 2.886 as the Mo content increases from 12 wt.% to 18 wt.%. The bcc Ti and bcc Mo are completely soluble above 882°C.However, the interdiffusion coefficients of the Ti-Mo binary system decreased with Mo content increased [21]. Hence, the porosity of porous Ti-Si-Mo intermetallic compounds decreased with Mo content increased. Meanwhile, the content of Mo oxides in Ti-Si-Mo powder mixtures increased with Mo content increased during ball milling. Volatilization of Mo oxides led to the increase of porosity when the Mo content is 18 wt.%. The pore size is mainly distributed in less than 1 μm and the average pore diameter of the sintered samples is very close, ranging from merely 246.5 nm to 287.1 nm according to the results. It was concluded that the pore sizes are larger while the porosity is higher. The surface area which is needed to obtain reliable oxidation behavior has little difference and ranges from 2.622 m2·g−1 to 2.862 m2·g−1. The mass gain gradually decreases from 0.136 g·m−2 to 0.092 g·m−2 after being oxidized for 100 h as the content of Mo increases from 12 wt.% to 18 wt.%. It is found that the mass gain of porous Ti-Si-Mo intermetallic compounds decreased with porosity decreased from 44.18% to 40.58%. Lower porosity reduced the oxygen intake and resulted in the decrease of mass gain. Meanwhile, the stability of the oxides in porous Ti-Si-Mo intermetallic compounds follows the trend of TiO2 > SiO2 > MoO3 > MoO2 according to standard free energy (ΔG°).More MoO3 volatilized during the oxidation process and the mass gain of porous Ti-8Si-18Mo intermetallic compounds continued to decrease. Hence, the mass gain of porous Ti-8Si-18Mo was only 0.092 g·m−2 for more Mo oxides volatilized during the oxidation process.

Table 1

Microstructure and oxidation behavior of sintered samples with different Mo contents

SamplePorosity (%)Surface area (m2·g−1)Fractal dimensionAverage pore diameters (nm)Mass gain after oxidation for 100 h (g·m−2)
a44.182.7282.891287.10.136
b41.942.8622.887246.50.111
c40.582.6222.880253.10.106
d42.542.6762.886268.30.092

3.1 Microstructure and Pore Size Distribution

The internal pore structure and pore size distribution of porous Ti-Si-Mo intermetallic compounds fabricated by reactive synthesis are shown in Figure 2. The samples consisting of a few large pores and many small pores have excellent complexity and connectivity. The distribution of pores less than 1 μm is magnified, as shown in Figure 2a”-d”. It is can be seen that the pore sizes of all samples are mainly distributed from 200 nm to 400 nm. A small number of pores have a size of approximately 90 μm due to the decomposition of C7H10N2O2S with particles of approximately 75 μm. However, the pore size is mainly less than 1 μm because the powders became extremely fine (submicron in size) after ball milling. During high-temperature sintering, the generation of big pores (>1 μm) were probably due to stacking between particles with size of >1 μm and the generation of small pores (>1 μm) were probably due to the diffusion and reaction between Ti/Mo and Si. It was concluded that the small pores were formed because of the reaction between Ti /Mo and Si and the mutual diffusion between the Ti and Mo particles. An abundance of pores with sizes less than 1 μmcould influence the properties of porous Ti-Si-Mo intermetallic compounds.

Figure 2 SEM morphologies and pore size distributions of sintered samples with different Mo contents: (a) 12 wt.%, (b) 14 wt.%, (c) 16 wt.%, (d) 18 wt.%
Figure 2

SEM morphologies and pore size distributions of sintered samples with different Mo contents: (a) 12 wt.%, (b) 14 wt.%, (c) 16 wt.%, (d) 18 wt.%

3.2 Phase Composition

The phase composition of the samples with different Mo contents is shown in Figure 3. It was concluded that porous Ti-Si-Mo intermetallic compounds fabricated by reactive synthesis consist of Mo5Si3, TiSi, Ti5Si4, Ti5Si3 and TiO. There are TiSi and Mo5Si3 phases in all the samples. As the Mo content in the powder mixtures increased, the Ti5Si4 phase was formed. In particular, the Ti5Si3 phase was detected at Mo content of 16 wt.%. In addition, a small amount of titanium oxide was formed due to the unavoidable presence of oxygen during the ball milling and sintering procedure, and the titanium oxides could have an effect on the oxidation behavior for the sintered porous Ti-Si-Mo intermetallic compounds [22].

Figure 3 XRD patterns of sintered samples with different Mo contents: (a) 12 wt.%, (b) 14 wt.%, (c) 16 wt.%, (d) 18 wt.%
Figure 3

XRD patterns of sintered samples with different Mo contents: (a) 12 wt.%, (b) 14 wt.%, (c) 16 wt.%, (d) 18 wt.%

3.3 Oxidation Behavior

The microstructure, phase composition and mass gain curve of the oxidized samples are shown in Figure 4. It was found that the weight of each sample remains nearly stable after 20 h of oxidation. As the Mo content increased, the mass gain gradually decreased from 0.136 g·m−2 to 0.092 g·m−2 after 100 h of oxidation. A continuous oxides scale was formed at the oxide/air interface, and the oxidized sample surface was basically covered with the TiO2 layer. The outward diffusion of Ti controlled the oxidation rate at temperatures beyond 1173 K, and the external TiO2 layer originated from the substrate surface. The samples were not oxidized further after 20 h due to the external TiO2 layer. Particularly, the oxidized sample surface with an Mo content of 16 wt.% consisted of a TiO2-SiO2 duplex layer because the sample with an Mo content of 16 wt.% was the only sample that did not contain the TiO phase composition in all the sintered samples, as shown in Fig. 2. The inward diffusion of oxygen without the titanium oxides was worse and it resulted in a TiO2-SiO2 duplex layer underneath [23]. The microstructure has a slight effect on the oxidation behavior because there is little difference among the pore characteristics of the sintered samples, such as porosity, pore size, surface area and fractal dimension. The oxidation weight of porous Ti-Si-Mo intermetallic compounds with various Mo content oxidized at 1473 K decreased with increasing Mo content. It is supposed that MoO3 volatilized during the oxidation process [24]. According to the Ti-Mo binary phase diagram [25], the Ti-8Si-18Mo alloy is composed of β-Ti at 1473 K. The oxygensolid-solubility of β-Ti is only 4% [26]. Hence, the oxidation resistance of sintered samples increases with the increasing of the Mo content. By comparison, the mass gain of porous Ti-8Si-18Mo intermetallic compounds was only approximately4%of that of the porous 316 L stainless steel after 100 h of oxidation [17]. In summary, porous Ti-Si-Mo intermetallic compounds possess superior oxidation resistance at high-temperature.

Figure 4 SEM morphologies, XRD patterns and mass gain curves of samples with different Mo contents oxidized at 1473 K for 100 h: (a) 12 wt.%, (b) 14 wt.%, (c) 16 wt.%, (d) 18 wt.%
Figure 4

SEM morphologies, XRD patterns and mass gain curves of samples with different Mo contents oxidized at 1473 K for 100 h: (a) 12 wt.%, (b) 14 wt.%, (c) 16 wt.%, (d) 18 wt.%

3.4 Fractal Dimension

The fractal dimension effectively characterizes the complexity and connectivity of pores [27]. The larger the fractal dimension, the more complex the spatial distribution of the material’s pores [28]. The fractal dimension of samples with different Mo contents are shown in Table 1 according to Eq. (1). The fractal dimension decreased from 2.891 to 2.880 and then increased to 2.886 as the Mo content increased. The large fractal dimension proves that the pores of the samples have excellent complexity and connectivity. It is concluded that the fractal dimension is consistent with the porosity for the pore structures with the approximate smallest and largest pore radius. In addition, wider pore size distributions corresponded to larger fractal dimensions when the porosity was constant. In addition, the spatial filling capability is greater as the fractal dimension increases,which could have an effect on the mass and heat transfer performance. It was concluded that the oxidation performance gradually declines as the fractal dimension increased in general because the fractal dimension is higher and because, the area to be oxidized is larger. However, the sample with an Mo content of 18 wt.% did not conform to this rule because of the evaporation of MoO3 [13]. Thus, the Mo content has an impact on the oxidation performance in addition to the microstructure.

4 Conclusions

In summary, porous Ti-Si-Mo intermetallic compounds were successfully fabricated by the reactive synthesis with C7H10N2O2S as a foaming agent. The porosity of the samples decreased from 44.18% to 40.58% and then increased to 42.54% as the Mo content increased from 12 wt.% to18 wt.%. The pore size distribution was on submicron level, and the average pore diameters were extremely small, ranging from 246.5 nm to 287.1 nm. The fractal dimension ranged from 2.880 to 2.891 indicating that the pores of samples have excellent complexity and connectivity. The phase compositions of the porous Ti-Si-Mo intermetallic compounds mainly consisted of TiSi, Ti5Si4, Mo5Si3 and TiO. The porous Ti-Si-Mo intermetallic compounds were not oxidized any more after 20 h because the surface was mainly covered with a continuous TiO2 layer. As the Mo content increased from 12 wt.% to18 wt.%, the mass gain of porous Ti-Si-Mo intermetallic compounds gradually decreased from 0.136 g·m−2 to 0.092 g·m−2 after oxidation at 1473 K for 100 h. In addition, the oxidation performance gradually decreased as the fractal dimension increased. Thus, porous Ti-Si-Mo intermetallic compounds possess excellent oxidation at high temperature.

Acknowledgement

The authors acknowledge the financial support of Natural Science Foundation of Jiangsu Province (No. BK20181448), Natural Science Research of Jiangsu Higher Education Institutions of China (No. 17KJB430009) and Senior Talent Foundation of Jiangsu University (No. 15JDG150).

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Received: 2019-04-11
Accepted: 2019-04-27
Published Online: 2020-02-28

© 2020 J. Ru et al., published by De Gruyter

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

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  38. Corrosion behaviors of 316 stainless steel and Inconel 625 alloy in chloride molten salts for solar energy storage
  39. Determination of chromium valence state in the CaO–SiO2–FeO–MgO–CrOx system by X-ray photoelectron spectroscopy
  40. Electric discharge method of synthesis of carbon and metal–carbon nanomaterials
  41. Effect of high-frequency electromagnetic field on microstructure of mold flux
  42. Effect of hydrothermal coupling on energy evolution, damage, and microscopic characteristics of sandstone
  43. Effect of radiative heat loss on thermal diffusivity evaluated using normalized logarithmic method in laser flash technique
  44. Kinetics of iron removal from quartz under ultrasound-assisted leaching
  45. Oxidizability characterization of slag system on the thermodynamic model of superalloy desulfurization
  46. Influence of polyvinyl alcohol–glutaraldehyde on properties of thermal insulation pipe from blast furnace slag fiber
  47. Evolution of nonmetallic inclusions in pipeline steel during LF and VD refining process
  48. Development and experimental research of a low-thermal asphalt material for grouting leakage blocking
  49. A downscaling cold model for solid flow behaviour in a top gas recycling-oxygen blast furnace
  50. Microstructure evolution of TC4 powder by spark plasma sintering after hot deformation
  51. The effect of M (M = Ce, Zr, Ce–Zr) on rolling microstructure and mechanical properties of FH40
  52. Phase evolution and oxidation characteristics of the Nd–Fe–B and Ce–Fe–B magnet scrap powder during the roasting process
  53. Assessment of impact mechanical behaviors of rock-like materials heated at 1,000°C
  54. Effects of solution and aging treatment parameters on the microstructure evolution of Ti–10V–2Fe–3Al alloy
  55. Effect of adding yttrium on precipitation behaviors of inclusions in E690 ultra high strength offshore platform steel
  56. Dephosphorization of hot metal using rare earth oxide-containing slags
  57. Kinetic analysis of CO2 gasification of biochar and anthracite based on integral isoconversional nonlinear method
  58. Optimization of heat treatment of glass-ceramics made from blast furnace slag
  59. Study on microstructure and mechanical properties of P92 steel after high-temperature long-term aging at 650°C
  60. Effects of rotational speed on the Al0.3CoCrCu0.3FeNi high-entropy alloy by friction stir welding
  61. The investigation on the middle period dephosphorization in 70t converter
  62. Effect of cerium on the initiation of pitting corrosion of 444-type heat-resistant ferritic stainless steel
  63. Effects of quenching and partitioning (Q&P) technology on microstructure and mechanical properties of VC particulate reinforced wear-resistant alloy
  64. Study on the erosion of Mo/ZrO2 alloys in glass melting process
  65. Effect of Nb addition on the solidification structure of Fe–Mn–C–Al twin-induced plasticity steel
  66. Damage accumulation and lifetime prediction of fiber-reinforced ceramic-matrix composites under thermomechanical fatigue loading
  67. Morphology evolution and quantitative analysis of β-MoO3 and α-MoO3
  68. Microstructure of metatitanic acid and its transformation to rutile titanium dioxide
  69. Numerical simulation of nickel-based alloys’ welding transient stress using various cooling techniques
  70. The local structure around Ge atoms in Ge-doped magnetite thin films
  71. Friction stir lap welding thin aluminum alloy sheets
  72. Review Article
  73. A review of end-point carbon prediction for BOF steelmaking process
https://doi.org/10.1515/htmp-2020-0022
Keywords for this article
porous Ti-Si-Mo intermetallic compounds; reactive synthesis; microstructure; phase composition; oxidation resistance
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  3. Study on the Appropriate Production Parameters of a Gas-injection Blast Furnace
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  36. Influence of electrode tip diameter on metallurgical and mechanical aspects of spot welded duplex stainless steel
  37. Effect of multi-pass deformation on microstructure evolution of spark plasma sintered TC4 titanium alloy
  38. Corrosion behaviors of 316 stainless steel and Inconel 625 alloy in chloride molten salts for solar energy storage
  39. Determination of chromium valence state in the CaO–SiO2–FeO–MgO–CrOx system by X-ray photoelectron spectroscopy
  40. Electric discharge method of synthesis of carbon and metal–carbon nanomaterials
  41. Effect of high-frequency electromagnetic field on microstructure of mold flux
  42. Effect of hydrothermal coupling on energy evolution, damage, and microscopic characteristics of sandstone
  43. Effect of radiative heat loss on thermal diffusivity evaluated using normalized logarithmic method in laser flash technique
  44. Kinetics of iron removal from quartz under ultrasound-assisted leaching
  45. Oxidizability characterization of slag system on the thermodynamic model of superalloy desulfurization
  46. Influence of polyvinyl alcohol–glutaraldehyde on properties of thermal insulation pipe from blast furnace slag fiber
  47. Evolution of nonmetallic inclusions in pipeline steel during LF and VD refining process
  48. Development and experimental research of a low-thermal asphalt material for grouting leakage blocking
  49. A downscaling cold model for solid flow behaviour in a top gas recycling-oxygen blast furnace
  50. Microstructure evolution of TC4 powder by spark plasma sintering after hot deformation
  51. The effect of M (M = Ce, Zr, Ce–Zr) on rolling microstructure and mechanical properties of FH40
  52. Phase evolution and oxidation characteristics of the Nd–Fe–B and Ce–Fe–B magnet scrap powder during the roasting process
  53. Assessment of impact mechanical behaviors of rock-like materials heated at 1,000°C
  54. Effects of solution and aging treatment parameters on the microstructure evolution of Ti–10V–2Fe–3Al alloy
  55. Effect of adding yttrium on precipitation behaviors of inclusions in E690 ultra high strength offshore platform steel
  56. Dephosphorization of hot metal using rare earth oxide-containing slags
  57. Kinetic analysis of CO2 gasification of biochar and anthracite based on integral isoconversional nonlinear method
  58. Optimization of heat treatment of glass-ceramics made from blast furnace slag
  59. Study on microstructure and mechanical properties of P92 steel after high-temperature long-term aging at 650°C
  60. Effects of rotational speed on the Al0.3CoCrCu0.3FeNi high-entropy alloy by friction stir welding
  61. The investigation on the middle period dephosphorization in 70t converter
  62. Effect of cerium on the initiation of pitting corrosion of 444-type heat-resistant ferritic stainless steel
  63. Effects of quenching and partitioning (Q&P) technology on microstructure and mechanical properties of VC particulate reinforced wear-resistant alloy
  64. Study on the erosion of Mo/ZrO2 alloys in glass melting process
  65. Effect of Nb addition on the solidification structure of Fe–Mn–C–Al twin-induced plasticity steel
  66. Damage accumulation and lifetime prediction of fiber-reinforced ceramic-matrix composites under thermomechanical fatigue loading
  67. Morphology evolution and quantitative analysis of β-MoO3 and α-MoO3
  68. Microstructure of metatitanic acid and its transformation to rutile titanium dioxide
  69. Numerical simulation of nickel-based alloys’ welding transient stress using various cooling techniques
  70. The local structure around Ge atoms in Ge-doped magnetite thin films
  71. Friction stir lap welding thin aluminum alloy sheets
  72. Review Article
  73. A review of end-point carbon prediction for BOF steelmaking process
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