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Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder

  • Baosheng Wu , Jinglin Liu , Qi Song EMAIL logo , Zan Lv and Wei Bai
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

In order to improve joint integrity and reduce the amount of intermetallic compounds (IMCs), 6061-T6 Al and AZ31B Mg alloys were successfully joined by stationary shoulder friction stir welding (SSFSW). The stationary shoulder effectively enhanced the joint surface integrity and reduced the thickness reduction of the Al/Mg joint. The elimination of pin adhesion was beneficial to increasing material transfer and then improving interfacial joining length of Al/Mg joint. Extremely thin IMCs layer could be achieved because of the heat sink induced by the stationary shoulder. The maximum tensile strength of the Al/ Mg joint reached 137 MPa at a welding speed of 60 mm/min, rotating velocity of 1000 rpm and offset to Mg sheet of 0.3 mm, which was 130% higher than that of conventional joint. SSFSW is feasible and has the potential to join dissimilar materials with the formation of IMCs, such as Al/Mg alloys, Al/copper alloys, Al/titanium alloys and so on.

Keywords: Friction stir welding; Stationary shoulder; Aluminum/magnesium alloys; Material flow; Intermetallic compounds; Mechanical properties

1 Introduction

Aluminum (Al) and Al alloys have the advantages of the high strength, good formability, excellent corrosion resistance and weight savings, thereby widely applying in aerospace, automotive, electronics, shipbuilding and so on [1, 2, 3, 4, 5, 6]. As the one of lightest structural metals, Magnesium (Mg) alloys have been applied in transportation and electronic industries because of the high specific strength, rigidity and good damping capacities [7, 8, 9]. The welding technologies of Al and Mg alloys have been brought into focus in order to utilize the excellent performances of the both materials and optimize structural configuration. It is difficult to join dissimilar materials of Al and Mg alloys by conventional fusion welding techniques because of the coarse grains, hot cracks, pores, especially amounts of hard and brittle intermetallic compounds (IMCs) [10].

As a solid state welding technique, friction stir welding (FSW) can effectively avoid the welding defects associated with conventional fusion welding because of the higher joint quality, smaller distortion, lower residual stress and pollution-free and so on, which has potential to join dissimilar Al/Mg alloys [11, 12, 13]. Currently, FSW has successfully achieved high-quality joints of similar Al alloys. However, conventional FSW is difficult to obtain dissimilar Al/Mg joints with acceptable joint integrity, such as surface finishing, thickness reduction, mechanical properties and so on [14, 15]. Yan et al. [14] proved that the adhesion materials featured by the IMCs of Al3Mg2 and Al12Mg17 on the surface of the rotating pin easily resulted in bad joint formation. Yan et al. [15] expounded that welding temperature reached eutectic temperature under a rotating velocity of 1000 rpm and welding speed of 30 mm/min, thereby resulting in the crack defects on the joint surface. Furthermore, Sato et al. [16] welded 6 mm thick sheets of 1050 Al and AZ31 Mg alloys under 90 mm/min and 2450 rpm and found that the cracks appeared in the stir zone (SZ) when the peak temperature was higher than 460 °C. Mofid et al. [17, 18], Zhao et al. [19], Wu et al. [20] and Ji et al. [11, 12, 21] used underwater FSW, stationary shoulder FSW (SSFSW) and ultrasonic assisted SSFSW to join Al/Mg dissimilar materials, respectively. Zhao et al. [19] performed underwater FSW of Al and Mg alloys and found that the layer of IMCs was thinner than that in air. Mofid et al. [17, 18] studied effects of water, air and nitrogen on dissimilar FSW joint of Al and Mg alloys and found that large number of IMCs appeared in SZ under air, while water and nitrogen cooling were propitious to decreasing the number of IMCs. In our pre-experiment, SSFSW was beneficial to improving cooling rate, thereby reducing the amounts of IMCs [22]. Wu et al. [20] pointed out that ultrasonic could exert a little preheating effect on the welded workpieces, and did not influence the peak temperature. Meanwhile, Ji et al. [11, 12, 21] reported that ultrasonic could break the IMCs into small particles and then address these problems according to the acoustic streaming of ultrasonic based on the stationary shoulder tool.

Optimization of welding parameters in SSFSW of Al/Mg alloys is the key to dominate the joint integrity and mechanical properties. In this study, the effect of welding speed on SSFSW joint was mainly investigated in detail from the aspects of joint integrity, material flow, microstructure and mechanical properties.

2 Experimental procedure

The base materials (BMs) used in this experiment were 3 mm thick 6061-T6 Al and AZ31B Mg alloys sheets. Welding tool system included a stationary shoulder and a rotating tool. The inside and outside diameters of the stationary shoulder toolwere 11 mmand 16 mm,correspondingly. The diameters of the shoulder, pin bottom and top of the rotating tool featured by right tapered-and-threaded were 10, 5 and 3 mm, correspondingly. The length of the rotating pin was 2.8 mm. A tilt angle relative to Z-axis was 2.5∘. A rotating velocity of 1000 rpm was constant. Welding speeds varied from 30 mm/min to 80 mm/min and the interval was 10 mm/min. The welding tool offset 0.3 mm to advancing side (AS). The welding direction was parallel to the rolling direction of sheets. Figure 1 exhibits the schematic during SSFSW of Al/Mg alloys.

Figure 1 Schematic during SSFSW of Al/Mg alloys
Figure 1

Schematic during SSFSW of Al/Mg alloys

The specimens were cut perpendicular to the welding direction using an electrical discharge machine to conduct the microstructural and mechanical characterizations. The microstructural specimens were respectively etched by the two reagents (2 ml HF, 3 ml HCl, 5 ml HNO3 and 190 ml H2O for the Al alloy; 5 ml CH3COOH + 5 g C6H2OH(NO2)3 + 10 ml H2O + 100 ml C2H5OH for the Mg alloy) and then observed using an optical microscope. Partial smashed particle was presented by a scanning electron microscopy (SEM) with an energy dispersive spectrometer. Microhardness of a typical Al/Mg joint was measured using a micro-hardness tester at a load of 200 g and a dwelling time of 10 s along the thickness direction. The interval between the both adjacent points was 0.5 mm. Three tensile specimens were prepared with reference to ISO 9018 [23]. Tensile tests were carried out at a crosshead speed of 2 mm/min. The fracture surfaces of the tensile specimen were also observed by SEM.

3 Results and discussion

3.1 Material transfer

Figure 2 exhibits the pin adhesion morphologies of the rotating tools at typical welding speeds. The severe pin adhesion was formed at a high heat input induced by a low welding speed of 30 mm/min, thereby making a tapered-and-threaded pin into a tapered pin without thread. The material transfer induced by the tapered pin was worse than that of the tapered-and-threaded pin [24]. The frictional heat decreased and the adhesion phenomenon was eliminated with increasing welding speed to 60 mm/min, as displayed in Figure 2b. The shape of the tapered-and-threaded pin remained unchanged under the welding speeds of 60 mm/min and 80 mm/min. The ability of the tapered-and-threaded pin to drive the plasticized materials was enhanced compared with the tapered pin without thread because of the elimination of the adhesion phenomenon. Meanwhile, the volume of the driven materials increased and the material transfers through the vertical and horizontal directions were improved, thereby transforming much more materials from the bottom to the top of the rotating pin. Meanwhile, the material transfer models under conventional FSW and SSFSW processes are displayed in Figure 3. Moreover, the stationary shoulder effectively prevents the plasticized materials overflowing out of the SZ and then reduces the size of flashes, while much more materials can flow into the SZ [25, 26]. The instantaneous cavity can be filled with the abundant plasticized materials. The welding defects, such as flashes and cavities, are prone to be reduced or even eliminated under the synergistic effects.

Figure 2 Morphologies of rotational tool after welding based on stationary shoulder process at typical welding speeds: (a) 30 mm/min, (b) 60 mm/min and (c) 80 mm/min
Figure 2

Morphologies of rotational tool after welding based on stationary shoulder process at typical welding speeds: (a) 30 mm/min, (b) 60 mm/min and (c) 80 mm/min

Figure 3 Material flow behaviors using different welding processes: (a) conventional FSW and (b) SSFSW
Figure 3

Material flow behaviors using different welding processes: (a) conventional FSW and (b) SSFSW

3.2 Surface integrity

Figure 4 displays the surface integrity of the SSFSW joints under different welding speeds. The high frictional heat leaded to the severe rotating tool adhesion when welding speed was 30 mm/min or 40 mm/min. This phenomenon caused the surface of the rotating shoulder to be higher than that of the stationary shoulder, thereby leading to the deep shoulder marks (Figures 4a and 4b). As the welding speed increased to 50 mm/min, 60 mm/min and 70 mm/min, the size of the shoulder marks drastically reduced, as displayed in Figures 4c-4e. One of the most important reasons is that increasing welding speed leads to the reductions in the heat input and the pin adhesion. This problem of pin adhesion can be solved by reducing heat input under a high welding speed, thereby improving the vertical material flow and reducing the outflowing of material from the SZ. The good surface integrity of the joint could be obtained by regulating and controlling welding speed. In the meantime, the elimination of the flash defects resulted in the micro thickness reduction, which was propitious to improving the ability of load bearing. The frictional heat further reduced with further increasing the welding speed to 80 mm/min, thereby resulting in the more discontinuous groove defect on the joint surface (Figure 4f).

Figure 4 Surface integrity of the SSFSW joints at different welding speeds: (a) 30 mm/min, (b) 40 mm/min, (c) 50 mm/min, (d) 60 mm/min, (e) 70 mm/min and (f) 80 mm/min
Figure 4

Surface integrity of the SSFSW joints at different welding speeds: (a) 30 mm/min, (b) 40 mm/min, (c) 50 mm/min, (d) 60 mm/min, (e) 70 mm/min and (f) 80 mm/min

3.3 Macrostructure

The macrostructures of the joints under different welding speeds are displayed in Figure 5. The welding speed had an important influence on the macrostructures in cross-section. The severe adhesion phenomenon occurred on the surface of the rotating tool at a welding speed of 30 mm/min. This phenomenon was difficult to increase the vertical transfer of the plasticized materials, thereby leading to a cavity defect with large size, as exhibited in Figure 5a. With increasing welding speeds to 40 mm/min and 50 mm/min, the size of the cavity defects gradually reduced due to the reduction of the pin adhesion. As the welding speed further reached 60 mm/min, the sound joint was attained (Figure 5d). This is because that the clear thread in Figure 2b is observed on the surface of the rotating tool because of the elimination of the pin adhesion. However, when the welding speed was 70 mm/min, the cavity defect appeared again because of the insufficient material flow induced by the low frictional heat under the condition without the pin adhesion, as indicated in Figure 5e. For FSW of Al/Mg alloys, the low welding speed leads to the longer time of stir action and the higher heat input, thereby resulting in the pin adhesion phenomenon and deteriorating the joint formation. Although increasing welding speed is beneficial to reducing the pin adhesion and excessively increasing welding speed may cause the insufficient material transfer, forming the cavity defects. Therefore, the welding speed of 60 mm/min was optimum for the improvement of the joint integrity for the 3 mm thick 6061-T6 and AZ31B alloys sheets.

Figure 5 Macrostructures in cross-section of the Al/Mg joints at different welding speeds: (a) 30 mm/min, (b) 40 mm/min, (c) 50 mm/min, (d) 60 mm/min and (e) 70 mm/min
Figure 5

Macrostructures in cross-section of the Al/Mg joints at different welding speeds: (a) 30 mm/min, (b) 40 mm/min, (c) 50 mm/min, (d) 60 mm/min and (e) 70 mm/min

3.4 Microstructure

The typical Al/Mg joint was divided into four regions: BM, heat affected zone (HAZ), thermo-mechanically affected zone (TMAZ) and SZ, as displayed in Figure 5d. Figure 6 exhibits the microstructures at different positions marked in Figure 5d. The strength is dominated by the microstructures of the SZ for the Al/Mg joint, especially the Al/Mg joining interface. There was no crack at the interface of Al/Mg joint at different positions, while the interlayer in SZ was complex. The mechanical interlocking was beneficial to improving the tensile properties. Importantly, the white bands appeared at the Al/Mg joining interfaces at the both AS and retracting side (RS) (Figures 6g and 6h). The white bands were corresponding to elements of the IMCs, which had been reported by Zhao et al. [19]. Moreover, the Al/Mg joining interface at the RS was far longer and more complex than that at the AS. Firouzdor et al. [27] and Huang et al. [28] found that the longer interfacial length and the interpenetrating feature thickness were beneficial to improving mechanical interlocking. Therefore, the strength of the joining interface at the RS may be stronger than that at the AS.

Figure 6 Microstructures at different locations marked in Figure 5d of joint at the welding speed of 60 mm/min and rotational speed of 1000 rpm
Figure 6

Microstructures at different locations marked in Figure 5d of joint at the welding speed of 60 mm/min and rotational speed of 1000 rpm

3.5 Mechanical properties

Microhardness distribution of the dissimilar Al/Mg joint is displayed in Figure 7. The hardness of the dissimilar Al/Mg joint exhibited an uneven distribution, which was closely related to strengthening phase distribution and grain size. Especially, size and distribution of the IMCs easily leaded to the non-uniform distribution of hardness [21]. The maximum hardness value in Figure 7 is 128 Hv, which is higher than those of both BMs. The IMCs can improve the micro-hardness. The hardness variations of other locations in the SZ were dominated by the interlayer microstructures and grain size induced by the degree of dynamic recrystallization.

Figure 7 Hardness of the typical Al/Mg joint
Figure 7

Hardness of the typical Al/Mg joint

Figure 8 displays the tensile test results of the Al/Mg joints at different welding speeds. The tensile properties firstly increased and then slightly decreased with the increase of welding speed. The maximum tensile strength and elongation respectively reached 137 MPa and 1.6% under the welding speed of 60 mm/min, which were far higher than those of conventional joint [13]. As mentioned above, the cavity defects induced by the pin adhesion formed in the SZ under the welding speeds lower than 60 mm/min. This defect often leaded the stress concentration and the reduction of loading area, thereby reducing the tensile properties of the Al/Mg joint. The defect-free joint with the longer interface joining layer at the Al/Mg joint interface of the SZ was attained under a welding speed of 60 mm/min, which could bear big load and then enhance the tensile properties. The cavity defects induced by the inadequate material transfer appeared in the SZ again at the welding speeds of 70 mm/min and 80 mm/min, thereby reducing the tensile properties. Liu et al. [29] stated that an introduction of ultrasonic into SSFSW of Al/Mg alloys could material flow behavior and eliminate welding defects, which further expanded the welding speed ranges from 60 mm/min to 80 mm/min.

Figure 8 Tensile properties of the Al/Mg joints based on SSFSW
Figure 8

Tensile properties of the Al/Mg joints based on SSFSW

Figure 9 displays the fracture locations of the SSFSW Al/Mg joints at different welding speeds. Obviously, there were two fracture mechanisms, which were the fracture along the welding defects and the fracture along the continuous IMCs layer at the SZ, respectively. When the welding speed varied from 30 mm/min to 50 mm/min, the welding defect appears at the SZ, which leaded to the initiation of the cracks and then further propagates along the Al/Mg joining interface during tensile test (Figures 9a-9c). The continuous IMCs layer occurred at the Al/Mg joining interface of the sound joint at the welding speed of 60 mm/min.

Figure 9 Fracture locations of the joints by different welding speeds: (a) 30 mm/min, (b) 40 mm/min, (c) 50 mm/min, (d) 60 mm/min and (e) 70 mm/min
Figure 9

Fracture locations of the joints by different welding speeds: (a) 30 mm/min, (b) 40 mm/min, (c) 50 mm/min, (d) 60 mm/min and (e) 70 mm/min

The incompatible deformation appeared at the Al/Mg joining interface because of the hard and brittle IMCs during the bigger tensile load, which easily leaded to the stress concentration and the initiation of the cracks. In this study, the interfacial joining length of the RS was bigger than that of the AS, thereby resulting in the joint fracture at the joining interface between the SZ and the TMAZ of AS (Figure 9d). As the welding speed further increased to 70 mm/min, the fracture location occurred at the cavity defect (Figure 9e). Therefore, the welding defects induced by the adhesion phenomenon and the reduction of heat input were the prominent reason of the joint fracture, while the IMCs layer was the main factor for the sound joint.

Fracture surface morphologies of the typical Al/Mg joint at the welding speed of 60 mm/min were shown in Figure 10. All the fracture surface morphologies through the thickness direction were featured by the cleavage feature (Figures 10b-10d), illustrating the typical brittle fracture because of the occurrence of the IMCs. The fracture morphologies in Figure 10 were consistent with the fracture location of the Al/Mg joint in Figure 10d.

Figure 10 Fracture surface morphologies at the welding speed of 60 mm/min: (a) macroscopic of fracture surface; micro fracture surfaces at different locations in Figure 10a: (b) position b, (c) position c and (d) position d
Figure 10

Fracture surface morphologies at the welding speed of 60 mm/min: (a) macroscopic of fracture surface; micro fracture surfaces at different locations in Figure 10a: (b) position b, (c) position c and (d) position d

4 Conclusions

In order to improve joint integrity and reduce thickness reduction and IMCs, 6061-T6 Al and AZ31B Mg alloys were joined by SSFSW. Meanwhile, surface integrity, material transfer, microstructure and mechanical properties of the Al/Mg joint were mainly investigated. Based on the present investigations, the following conclusions can be drawn:

  1. Defect-free joint with good surface integrity and micro thickness reduction could be obtained based on SSFSW under the optimum welding parameter.

  2. The stationary shoulder tool could eliminate the pin adhesion and then enhance material transfer, which was propitious to increasing the mixture degree of the Al/Mg alloys and then improving mechanical interlocking and interface joining length. Meanwhile, the extremely thin IMCs layer formed at the Al/Mg joining interface because of the fast cooling rate induced by the stationary shoulder.

  3. The tensile properties firstly increased and then decreased with the increase of welding speed. The maximum tensile strength of 137 MPa was achieved under the welding speed of 60 mm/min, which was far higher than that of conventional joint.

  4. The SSFSW has potential to join dissimilar materials, such as Al/Mg alloys, Al/copper alloys, Al/titanium alloys and so on, from the viewpoints of good surface integrity, no pin adhesion, micro thickness reduction and extremely thin IMCs layer.

Baosheng Wu and Jinglin Liu contributed equally to this work

Acknowledgement

This work is supported by the National Natural Science Foundation of China (No. 51705339) and the Education Department Foundation of Liaoning Province (L201615).

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Received: 2018-09-28
Accepted: 2018-11-08
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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  56. A Multi Scale Strategy for Simulation of Microstructural Evolutions in Friction Stir Welding of Duplex Titanium Alloy
  57. Partition Behavior of Alloying Elements in Nickel-Based Alloys and Their Activity Interaction Parameters and Infinite Dilution Activity Coefficients
  58. Influence of Heating on Tensile Physical-Mechanical Properties of Granite
  59. Comparison of Al-Zn-Mg Alloy P-MIG Welded Joints Filled with Different Wires
  60. Microstructure and Mechanical Properties of Thick Plate Friction Stir Welds for 6082-T6 Aluminum Alloy
  61. Research Article
  62. Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
  63. Calorimetric study on Bi-Cu-Sn alloys
  64. Mineralogical Phase of Slag and Its Effect on Dephosphorization during Converter Steelmaking Using Slag-Remaining Technology
  65. Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder
  66. Cellular Automaton Modeling of Phase Transformation of U-Nb Alloys during Solidification and Consequent Cooling Process
  67. The effect of MgTiO3Adding on Inclusion Characteristics
  68. Cutting performance of a functionally graded cemented carbide tool prepared by microwave heating and nitriding sintering
  69. Creep behaviour and life assessment of a cast nickel – base superalloy MAR – M247
  70. Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation
  71. Reducing Surface Cracks and Improving Cleanliness of H-Beam Blanks in Continuous Casting — Improving continuous casting of H-beam blanks
  72. Rhodium influence on the microstructure and oxidation behaviour of aluminide coatings deposited on pure nickel and nickel based superalloy
  73. The effect of Nb content on precipitates, microstructure and texture of grain oriented silicon steel
  74. Effect of Arc Power on the Wear and High-temperature Oxidation Resistances of Plasma-Sprayed Fe-based Amorphous Coatings
  75. Short Communication
  76. Novel Combined Feeding Approach to Produce Quality Al6061 Composites for Heat Sinks
  77. Research Article
  78. Micromorphology change and microstructure of Cu-P based amorphous filler during heating process
  79. Controlling residual stress and distortion of friction stir welding joint by external stationary shoulder
  80. Research on the ingot shrinkage in the electroslag remelting withdrawal process for 9Cr3Mo roller
  81. Production of Mo2NiB2 Based Hard Alloys by Self-Propagating High-Temperature Synthesis
  82. The Morphology Analysis of Plasma-Sprayed Cast Iron Splats at Different Substrate Temperatures via Fractal Dimension and Circularity Methods
  83. A Comparative Study on Johnson–Cook, Modified Johnson–Cook, Modified Zerilli–Armstrong and Arrhenius-Type Constitutive Models to Predict Hot Deformation Behavior of TA2
  84. Dynamic absorption efficiency of paracetamol powder in microwave drying
  85. Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
  86. Influence of unburned pulverized coal on gasification reaction of coke in blast furnace
  87. Effect of PWHT Conditions on Toughness and Creep Rupture Strength in Modified 9Cr-1Mo Steel Welds
  88. Role of B2O3 on structure and shear-thinning property in CaO–SiO2–Na2O-based mold fluxes
  89. Effect of Acid Slag Treatment on the Inclusions in GCr15 Bearing Steel
  90. Recovery of Iron and Zinc from Blast Furnace Dust Using Iron-Bath Reduction
  91. Phase Analysis and Microstructural Investigations of Ce2Zr2O7 for High-Temperature Coatings on Ni-Base Superalloy Substrates
  92. Combustion Characteristics and Kinetics Study of Pulverized Coal and Semi-Coke
  93. Mechanical and Electrochemical Characterization of Supersolidus Sintered Austenitic Stainless Steel (316 L)
  94. Synthesis and characterization of Cu doped chromium oxide (Cr2O3) thin films
  95. Ladle Nozzle Clogging during casting of Silicon-Steel
  96. Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process
  97. Research Article
  98. Effect of Boundary Conditions on Residual Stresses and Distortion in 316 Stainless Steel Butt Welded Plate
  99. Numerical Analysis on Effect of Additional Gas Injection on Characteristics around Raceway in Melter Gasifier
  100. Variation on thermal damage rate of granite specimen with thermal cycle treatment
  101. Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag
  102. Effect of Basicity on Precipitation of Spinel Crystals in a CaO-SiO2-MgO-Cr2O3-FeO System
  103. Review Article
  104. Exploitation of Mold Flux for the Ti-bearing Welding Wire Steel ER80-G
  105. Research Article
  106. Furnace heat prediction and control model and its application to large blast furnace
  107. Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment
  108. Study of the Viscosity of a La2O3-SiO2-FeO Slag System
  109. Tensile Deformation and Work Hardening Behaviour of AISI 431 Martensitic Stainless Steel at Elevated Temperatures
  110. The Effectiveness of Reinforcement and Processing on Mechanical Properties, Wear Behavior and Damping Response of Aluminum Matrix Composites
https://doi.org/10.1515/htmp-2019-0001
Keywords for this article
Friction stir welding; Stationary shoulder; Aluminum/magnesium alloys; Material flow; Intermetallic compounds; Mechanical properties
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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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