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Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation

  • Dong Tian-Shun , Wang Ran , Li Guo-Lu EMAIL logo and Liu Ming EMAIL logo
Published/Copyright: May 20, 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 work, the substrate, NiCr coating, Al2O3 coating with NiCr undercoating and Al2O3 coating were tested by an impact indentation device equipped with an acoustic emission (AE) detection equipment. The surface morphology, dimension, cross-sectional image, 3D topography of indention and bonding strength of coatings were analyzed. The failure mechanism and AE signal characteristics of the coatings under impact were studied. The results demonstrate that the failure mode of NiCr coating was dominated by interface cracking, and that of Al2O3 coating is fracture and accompanied by a small amount of interface cracking, while Al2O3 coating with NiCr undercoating possesses common characteristics of the first two. The energy counting and wave voltage of AE signal were more sensitive to the bonding strength of coating in the impact process, which can be used to characterize the bonding strength of coating.

Keywords: Coating; bonding strength; impact indentation method; acoustic emission

1 Introduction

Thermal spraying technique has been widely used in various mechanical parts as a surface modification technique. Because of the combination between the coating and the substrate is mainly mechanical bonding, the bonding strength of coating is usually taken as one of the most important indexes to evaluate the coating’s quality. The methods available today to test bonding strength of coating are mainly tensile method [1], scratch method [2], bending method [3], shearing method [4], etc. However, all of these methods need to prepare specialized samples for indirect test on the testing machine, so they cannot be used for field direct test.

Song [5] proposed that an ideal method to detect the bonding strength of coating needs to meet at least two basic conditions: one is the model that characterizes the failure between the coating and the substrate; the other is the characteristic parameters which can response to the failure of the coating. Based on this idea, we have adopted the approach of "static load indentation + AE detection" to measure the bonding strength of coating, which can provide theoretical basis and experimental support for "indentation method +AE detection "[6, 7, 8]. In previous research, which we have carried out, we demonstrated that the process of static load indentation was too moderate to induce the failure of the coating effectively, which led to the extracted signal showing greater dispersion. Therefore, the impact indentation method was adopted in this work, which was easy to induce the failure of the coating and reduce the dispersion of the AE signals.

In this work, high efficiency supersonic plasma spraying system was employed to prepare three types of coatings, namely the metal coating (NiCr), ceramic coating with the undercoating (NiCr as transition coating and Al2O3 as working coating) and Al2O3 coating, whose bonding strength varies greatly. Subsequently, impact indentation method was used to evaluate the bonding strength of the above coatings, whereupon the relationship between the failure mechanism of coatings and acoustic emission (AE) signal characteristics under impact condition were studied. This study has important reference value for coating field detection.

2 Experimental materials and methods

2.1 Coating preparation

Self-developed high efficiency supersonic plasma spraying system [10] was employed to prepare NiCr coating, Al2O3 ceramic coating with NiCr undercoating and Al2O3 coating on AISI 1045 steel substrate with dimension of 80mm×50mm×4mm. The powder morphology of NiCr and Al2O3 is shown in Figure 1. Prior to spraying, the surface of substrate was cleaned with an acetone solution and sandblasted [11]. In this experiment, “#”spraying path was applied on the specimen. The spraying parameters are listed in Table 1

Figure 1 Powder pictures (a)NiCr powder; (b)Al2O3 powder
Figure 1

Powder pictures (a)NiCr powder; (b)Al2O3 powder

Table 1

Spraying parameters

Spraying parametersNiCrAl2O3
Main gas flow Ar (L/min)130110
Secondary air flow H2 (L/min)6.414.2
Spraying current (A)380400
Spraying voltage (V)150160
Spraying distance (mm)11090
Delivery amount (g/min)3030

2.2 Impact indentation and extraction of AE signal

In this experiment, the 120∘ cemented carbide indenter was impacted by the 1 Kg of mass, which freely fell from a height of 400mm. During the process, crack originated and the failure of the coating was induced. Since the indenter was small, it was necessary to make an indenter cover to fix it. The indenter should be connected closely with the indenter cover; in addition, sliding or friction should be avoided. The bottom of weights and the top of indenter should be adhered by rubber with the thickness of 8mm in order to avoid interference signals produced by metal impact. In order to ensure the reliability of AE signals, a five-group impact indentation tests on each sample were conducted.

The process of impact indentation was monitored in real time by PCI -2 type AE monitoring equipment, which was produced by Physical Acoustics Corporation. The sensor probe and the sample surface was pasted closely by vacuum coupling agent The distance between probe and the impact point was about 15 mm, the model of sensor was Nano30, the gain of pre-amplifier was 40 dB, the software of data acquisition was AEwin, threshold value was 55 dB (only record the signals over more than 55 dB). The working principle of test equipment is shown in Figure 2. During the experiment, the sample need to be moved to the next position after a point signal has been collected.

Figure 2 Schematic diagram of impact indentation method
Figure 2

Schematic diagram of impact indentation method

2.3 Observation of indentation and treatment of AE signal

An scanning electron microscope (SEM) was used to observe the surface and cross section morphology of indentation. The 3D topography and dimension of the indentation were observed by a 3D profilometer. The AE signal data was processed by Origin software.

3 Experimental results and analysis

3.1 Analysis of indentation topography of the coating

3.1.1 SEM morphology of the coating indentation edge

Figure 3 shows the indentation surface morphology measured by SEM. It is shown that the indentation edges of substrate was more regular, while NiCr coating was slightly rough, and Al2O3 ceramic coating with NiCr undercoating was relatively coarse accompanied by cracking and spalling. But in terms of Al2O3 ceramic coating, there were large areas of spallings. The difference of indentation surface morphology of these four samples are due to the hardness of the substrate, NiCr coating, Al2O3 ceramic coating with NiCr undercoating and Al2O3 coating increased sequentially. Moreover, the bonding strength of them decreased successively [20].

Figure 3 The surface morphology of indentation: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating
Figure 3

The surface morphology of indentation: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating

The bonding strength of NiCr coating was better. The combination of Al2O3 ceramic coating with NiCr undercoating consists of two parts: one is the combination between NiCr undercoating and substrate, the other is the combination between NiCr undercoating and Al2O3 coating. As a whole, the combination of Al2O3 ceramic coating with NiCr undercoating was weaker than that of NiCr coating. As the bonding strength of hard coating can be improved effectively by the transition coating or undercoating [13], the bonding strength of Al2O3 ceramic coating with NiCr undercoating was higher than that of Al2O3 ceramic coating. By virtue of lower hardness and better plasticity, the edge of the substrate was relatively regular when impacted. NiCr coating owning higher hardness and lower plasticity than that of the substrate was liable to fracture at the edge of the coating, so the edge was a little coarse. The surface hardness of the Al2O3 ceramic coating with NiCr undercoating was higher and the plasticity was worse, so serious fracture was produced in the impact process, which led to rougher indentation edge. In addition, due to the bonding strength between the Al2O3 ceramic coating and NiCr undercoating is poor, a certain cracks appeared between the working coating and the transition coating, which led to a certain spalling at the edge of the indentation. Because of the bonding strength of the Al2O3 ceramic coating was very low, serious cracking occurred between the coating and substrate during the impact process, which eventually led to a large area of spalling at the edge of the indentation.

3.1.2 3D topography analysis of coating indentation

Figure 4 shows a 3D topography of indentation. It was evident that the indentation edge of the substrate was smooth, and there was almost no bulge, which was attributed to low hardness and good plasticity of the substrate. There was local bulge at the indentation edge of NiCr coating, and the reasons are as follows: firstly, the coating was subjected to impact indentation to produce plastic deformation, the internal coating of the indentation was extruded to the edge, thus a certain bulge was produced; secondly, cracking was produced between indentation edge of the coating and the substrate, which led to the tilting upwards and local bulge of the coating. A wide range of bulges emerged on the indentation edge of Al2O3 ceramic coating with NiCr undercoating. This was because the bonding strength between Al2O3 coating surface and NiCr undercoating was insufficient. A certain cracks and spallings between the coating and the undercoating were produced under impact indentation, which resulted in a larger range of bulge at the indentation edge. The indentation edge of the Al2O3 ceramic coating had a wider range of bulges because there was no transition coating between Al2O3 coating and substrate, leading to a large area of cracking and spalling were produced between the coating and the substrate under impact indentation.

Figure 4 3D topography of indentation: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating
Figure 4

3D topography of indentation: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating

3.1.3 Indentation size analysis of coating

Table 2 shows the indentation size detected by the 3D profilometer. As shown in Table 2, Figure 3 and Figure 4, the indentation size of substrate, NiCr coating and Al2O3 coating with NiCr undercoating decreased in turn. The reason is the hardness of the substrate, NiCr coating and Al2O3 coating with NiCr undercoating increased in turn, which resulted in the indentation depth of indenter decreased in turn. Although the surface hardness of Al2O3 ceramic coating was the same as that of Al2O3 ceramic coating with NiCr undercoating, the indentation size of the former was larger. The reason is that the poor bonding strength between the coating and the substrate led to the greater cracking tendency, which failed to provide greater resistance for the indenter.

Table 2

Indentation dimensions of coating

Indentation dimensionssubstrateMetal coatingCeramic coatingBottomless ceramic coating
Diameters /mm1.6021.3121.1421.486
Depth/mm0.4140.3460.3030.472
Area/mm21.4241.0920.9301.326
Volume /mm30.2630.1490.1070.212

3.1.4 Evaluation for bond strength of coating

Figure 5 shows a quality standard obtained from a Germanengineer manual to measure bonding strength of coatings by indentation method. In this figure, HF-1~HF-4 indicated that the bonding strength of the coating was sufficient, while HF-5~HF-6 indicated that strength was insufficient. If the indentation surface morphology and 3D topography of the coating in Figure 3 and Figure 4 were compared with the quality standard of bonding strength in Figure

Figure 5 Quality standard for bond strength by indentation method
Figure 5

Quality standard for bond strength by indentation method

5, it was found that the indentation morphology of the substrate was similar to HF-1, the NiCr coating was similar to HF-2, Al2O3 coating with NiCr undercoating was similar to HF-3 and HF-4, which indicating that all of these three kinds of coatings had sufficient bond strength. Their bonding strength in descending order is substrate, NiCr coating and Al2O3 coating with NiCr undercoating. But the indentation morphology of Al2O3 coating was similar to HF-5 and HF-6, hence its bonding strength was insufficient.

3.2 Mechanism analysis of coating cracking

Figure 6 shows the cross section of the micro-structure of the substrate, NiCr coating, Al2O3 coating with NiCr undercoating and Al2O3 coating, respectively. As indicated in the figure, there was no cracking in the substrate indentation, but a certain number of bulges could be observed. The reason is that the hardness of substrate was lower and the plasticity was better, which led to a larger plastic deformation when impacted. In the impact process, the substrate materials of indentation was extruded to the edge, and a certain bulges were produced (Figure 7). But owing to the degree of bulges were small, the bulges were difficult to be observed under SEM and 3D profilometer. Cracking was produced around the NiCr coating indentation, because the NiCr coating at the indentation edge uplifted during the impact process, which produced greater transverse shear stress and longitudinal tensile stress, and because of the low hardness and good plasticity of this metal coating, fracture was not easy to produce, but cracking occurred between the coating and the substrate. Both cracking and fracture were observed at the indentation edge of Al2O3 ceramic coating, the reason for which was the center of the indentation was subjected to greater impact compressive stress, and due to the Al2O3 coating possessed higher hardness and greater brittleness, fracture was produced under the stress. Because of the process of fracture is accompanied by a certain stress release, cracking was observed near the fracture position. There were three failure positions in Al2O3 coating with NiCr undercoating. The first was fracture of Al2O3 coating itself at the edge of indentation; the second was cracking between the surface Al2O3 coating and the NiCr undercoating near the edge of indentation; and the third was the cracking between the NiCr undercoating and the substrate around the indentation. The reason for that was the coating not only contains Al2O3 coating with higher hardness and greater brittleness, but also NiCr undercoating with low hardness and good plasticity. When they were subject to impact indentation stress, Al2O3 coating with higher hardness and greater brittleness would produce fracture, which resulted in stress release, so Al2O3 coating and NiCr undercoating cracked once again near the fracture position. At the same time; cracking appeared between the substrate and the NiCr undercoating with lower hardness and better plasticity under the action of transverse shear stress and longitudinal tensile stress.

Figure 6 Micrograph of indentation section: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating
Figure 6

Micrograph of indentation section: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating

Figure 7 Cross-section of Indentation micromorphology
Figure 7

Cross-section of Indentation micromorphology

3.3 Analysis of AE signal

3.3.1 Analysis of energy counting and amplitude

Figure 8 shows the AE signals of substrate, NiCr coating, Al2O3 coating with NiCr undercoating and Al2O3 coating in the impact indentation process. The Y-axis represents AE energy counting and AE amplitude signal, and the X-axis represents time. As shown in the figure, the energy counting produced by the substrate was 400-800, and the amplitude was 70 -90dB. There were a number of noise signals, which were from weight impacting the indenter, indenter impacting the substrate and the deformation of the substrate. During the impact process, the AE signals produced by the substrate can be used as a reference standard and compared with the AE signals produced by the coating. After the interference signals having been filtered out, the real cracking and fracture signals of the coating were extracted.

Figure 8 Acoustic emission(AE) signals analysis of coating: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coatingtion SEM micromorphology
Figure 8

Acoustic emission(AE) signals analysis of coating: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coatingtion SEM micromorphology

During the impact process, the energy counting of NiCr coating was about 1000~1500 and the amplitude was 80~85dB; Al2O3 coating with NiCr undercoating about 2000~4000, and the amplitude about 90~99dB; Al2O3 coating about 5000~10000 and the amplitude reached maximum, which was about 99dB. The energy counting of coatings were higher than that of substrate obviously and the higher part could be regarded as the signal of coating cracking and fracture. Compared with NiCr coating, the energy counting of Al2O3 coating was obviously larger. There were two reasons for this phenomenon: firstly, the hardness and brittleness of Al2O3 coating was larger, so the energy was larger during the impact process; secondly, the combination of the Al2O3 coating was poor and the cracking was more serious, so the energy counting was larger. Compared with the Al2O3 coating with NiCr undercoating, the energy counting of Al2O3 coating was more obvious although the hardness of them was identical. The reason was that the bonding strength of Al2O3 coating is lower, the cracking and fracture was more serious, so the energy counting was larger. Generally, in the impact process, the energy counting was affected by the bonding strength and hardness of coating, but the bonding strength had a greater influence on the energy counting [20].

3.3.2 Analysis of wave voltage

Table 3 shows the wave voltage values of AE signals; the second wave of AE signals of each coating was extracted and was shown in Figure 9. It can be seen from Table 3 and Figure 9 that the wave voltage of substrate was about 0.4~0.7V, NiCr coating was about 1V, Al2O3 coating with NiCr undercoating was about 4~6V, and the Al2O3 coating reached the highest value, which was about 9~9.9V. The reasons for the difference of wave voltages was similar to that of energy counting. To some extent, the wave voltage was affected by hardness of the coating, but it mainly affected by bonding strength. The bonding strength of substrate, NiCr coating, Al2O3 coating with NiCr undercoating and Al2O3 coating decreased gradually, the cracking and fracture degree of coating increased successively, so the stress wave in the process of cracking and fracture increased in turn, and the wave voltage of the corresponding AE signals increased in turn as well.

Table 3

Waveform voltage values of AE signals

Test countwaveform voltage (V)
substrateNiCr coatingAl2O3 coatingbottomless Al2O3 coating,
10.721.34.59.7
20.581.1510
30.420.95.29.1
40.71.16.310
50.581.24.39.9
Figure 9 Spectrum analysis of coating: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating
Figure 9

Spectrum analysis of coating: (a)Substrate; (b)NiCr coating; (c)Al2O3 coating with the undercoating of NiCr; (d)Al2O3 coating

When comparing the bonding strength and AE signals of the above four samples, it was evident that the bonding strength of them decreased in turn, but the AE signals increased in turn, among which the energy counting and wave voltage were more sensitive to the variation of bonding strength [11]. So it can be concluded that the bonding strength of the coating was related to energy counting and wave voltage of AE signals, and the greater the bonding strength of the coating was, the smaller will be the energy counting and wave voltage.

4 Conclusions

In this paper, the bonding strength of NiCr coating, Al2O3 coating with NiCr undercoating and Al2O3 coating were studied using impact indentation method, whereupon the relationship between the failure mechanism of coatings and acoustic emission signal characteristics under impact condition was studied. The following conclusions can be drawn:

  1. Through analysis of the surface morphology and 3D topography of the indentation, it was found that the cracking and spalling degree of substrate, NiCr coating, Al2O3 coating with NiCr undercoating and Al2O3 coating at the edge of indentation increased sequentially, and the bond strength reduced successively.

  2. The analysis of micromorphology of the indentation section shows that local cracking of the interface or internal coating could be effectively induced by impact indentation method, and the cracking mechanism of these coatings are different. The failure mode of NiCr coating was dominated by interface cracking, and that of Al2O3 coating is fracture and is accompanied by a small amount of interface cracking, while Al2O3 coating with NiCr undercoating possesses common characteristics of the first two.

  3. The bonding strength of the coating was related to AE signal produced in the impact process. The greater the bonding strength of the coating was, the smaller were the energy counting, the amplitude and the wave voltages. The energy counting and wave voltage were more sensitive to the variation of bond strength, which were suitable for characterizing the bond strength of coatings.

    In a word, the impact indentation method accompanied with acoustic emission technology is feasible to characterize the bonding strength of the coating in the field.

  1. Availability of data and materials: All data generated or analyzed during this study are included in this published article and its supplementary information files.

  2. Competing interests: The authors declare that they have no competing interests.

  3. Funding: This work was supported by the National Natural Science Foundation of China (Grant No. 51675158 and No. 51535011) and Natural Science Foundation of Hebei Province (Grant No. E2016202325)

  4. Authors’ contributions: D-TS analyzed the results and wrote the manuscript. W R and L-GL reviewed the whole manuscript and both made significant revisions. L M raised the basic concept of this work.WR provided the real worn surfaces data. D-TS and L]L provided the method of processing the surfaces data with bi-Gaussian method. M-HJ conducted the revising of the Gaussian acoustic emission model. D-TS overall instructed this research.

Acknowledgement

The authors gratefully acknowledge the financial supports of National Natural Science Foundation of China (51675158) and Natural Science Foundation of Hebei Province (E2016202325).

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Received: 2018-12-15
Accepted: 2019-01-10
Published Online: 2019-05-20
Published in Print: 2019-02-25

© 2019 D. Tian-Shun et al., published by De Gruyter

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

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  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-2019-0007
Keywords for this article
Coating; bonding strength; impact indentation method; acoustic emission
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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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