Home Formation Mechanism and Influence Factors of the Sticker between Solidified Shell and Mold in Continuous Casting of Steel
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Formation Mechanism and Influence Factors of the Sticker between Solidified Shell and Mold in Continuous Casting of Steel

  • Fei He EMAIL logo and Li Zhou
Published/Copyright: September 12, 2018
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

Based on the stress characteristics of primary solidified shell in the mold, formation model of the shell’s sticker is established according to the theory of mechanical strength, and the mechanism and internal factors of the shell tearing are analyzed by the model. Furthermore, based on the measured data of many stickers in a slab-continuous caster, the influence of casting process factors on the sticker is analyzed statistically. The possible causes for the stickers in the studied caster are discussed. The results provide a reference for optimizing the continuous casting production process and effectively preventing the occurrence of the sticker from the source.

Keywords: continuous casting; sticker breakout; mold; solidified shell; casting process factors

Introduction

The sticker breakout is a severe accident in continuous casting which frequently happens. It not only severely affects the smooth production of continuous casting, but also damages the continuous casting equipment and reduces the metal yield. The sticker breakout has become one of the key factors restricting the development of the high-speed continuous casting and wide-thick-plate continuous casting technology. Solving sticker breakout is significant for the smooth production of continuous casting and production of high-quality slab. Now two methods [1] are used to solve the sticking continuous casting. First, improve the casting process factors inducing the sticker and proactively prevent against the sticker from the source. Second, develop effective mold breakout alarming system. For a complicated mold metallurgy process, not only the cracking sensitive steel will be frequently cast, but the casting steels are diversified, so casting is difficult. Especially it is difficult to continuously ensure the coordination and match of casting process factors under high-speed continuous casting. Improved casting process factors cannot fully avoid the shell’s sticker. But if the formation mechanism of sticker can be scientifically recognized, the influence law of the casting process factors on sticker can be grasped, and the casting process factors can be correctly improved and occurrence rate of shell sticking will be effectively reduced. Therefore, an in-depth study on the formation mechanism and influence factors of the solidified shell’s sticker inside the mold is carried out, which can provide scientific basis for optimization of the onsite casting process.

Since the 1990s, the formation mechanism and influence factors of sticker breakout [2, 3, 4, 5, 6, 7] have been studied enough at home and abroad, and the following conclusion is provided. The direct inherent factor leading to the sticker breakout is bad lubrication between primary solidified shell and mold near the meniscus, which makes the friction on the primary shell exceed its yield strength, resulting in the tearing. Different factors leading to bad shell’s lubrication are the external factors, e. g. casting powder, mold oscillation, mold level fluctuation, casting speed, degree of superheat heat, etc. Thus, the conclusion can be made that the sticker’s formation is related to bearing state of the primary shell. This paper first analyzes the tearing mechanism of the sticking shell from the stress state of the primary solidified shell, constructs the tearing model of the sticking shell according to mechanical strength theory, then validates the model by many examples of stickers based on the practical measurement data in casting, quantitatively analyzes the influence law of the casting process factors on sticker’s formation, discovers the specific sticker’s occurrence reasons, and improves the casting process factors inducing sticker purposefully.

Formation mechanism of the sticker

The sticker inside the mold mainly starts from the primary solidified shell near the meniscus. Analyzing the stress state on the primary solidified shell is very important for studying the tearing formation and influence factors of the sticker. The stress state of the primary solidified shell inside the mold is shown in Figure 1. The primary solidified shell near the meniscus mainly suffers from the friction and the static pressure of liquid steel is small. The gravity of the primary shell and the buoyancy of liquid steel can be ignored. The up/down oscillation of the mold and down movement of the slab will generate friction on the surface of the shell. The friction is divided into liquid friction and solid friction in accordance with the friction state between the shell and mold. The casting powder will mainly exist as the liquid near the meniscus and takes on the major function of liquid lubrication. The action of static pressure of liquid steel near the meniscus can be ignored, so the friction acting on the primary shell is the liquid friction and can be calculated according to the formula eq. (1) [8, 9].

(1)Fl=η(vm−vc)δ
Figure 1: Stress state of primary solidified shell under up/down oscillation of the mold.
Figure 1:

Stress state of primary solidified shell under up/down oscillation of the mold.

where Fl is liquid friction in unit area, N/m2; η is the viscosity of casting powder, Pa· s; vm is the upward oscillation velocity of the mold, m/s; vc is the casting speed, m/min; and δ is the thickness of liquid slag layer, mm.

The tensile stress on the shell is caused by the friction inside the mold and can be calculated by formula eq. (2) [8].

(2)σp=∫0LFldxD=η(vm−vc)LδD

where L is the distance from the meniscus, cm and D is the shell thickness at location L, mm.

In order to ensure that the primary shell is not torn, the maximal tensile stress on the shell should not exceed the yield strength σs according to the first strength theory [10], as shown in formula eq. (3). The maximal tensile stress on the shell can be obtained from the formulas eqs (2), (4) and (5). The result is shown as the formula eq. (6).

(3)σs>[σp]max
(4)vm=2πfh1000cos(2πft60)
(5)D=KLvc
(6)[σp]max=η(2πfh+vc)δKLvc

where h is the mold oscillation amplitude, mm; f is the mold oscillation frequency, min−1; and K is the solidification constant, mm/min1/2. If the mold sinusoidal oscillation is used and the oscillation velocity is as shown in formula eq. (4), the maximal oscillation velocity is 0.002πfh, m/min. The shell thickness D is calculated according to the solidification square root law, as shown in formula eq. (5).

To substitute the obtained maximal tensile stress into the eq. (3), inequality eq. (7) can be obtained, as follows.

(7)σsδK>η(0.002πfh+vc)Lvc

The bigger the left value or the smaller the right value of the inequality eq. (7) is, the less possible the shell will be torn. This inequality can reflect the conditions of the primary shell’s sticker well. And this inequality shows that the main factors affecting the primary shell tearing and sticking include yield strength σs, liquid slag layer thickness δ, casting powder viscosity η, casting speed vc, mold oscillation amplitude h, and oscillation frequency f. The yield strength σs reflects the influences of the steel performance and liquid steel temperature. The shell with a higher temperature and lower strength is more sensitive to be torn. The steel’s strength will reduce with temperature growth and the closer it gets to steel liquid level, the higher the temperature will be, making the shell most easily torn near the liquid level. Or when the degree of superheat is too high, which results in the high temperature of the shell near the meniscus, the strength of the primary shell will accordingly reduce and the tearing sensitivity of the shell will grow. The liquid slags the layer thickness δ and the casting powder viscosity η reflect the performance of casting powder and liquid-level fluctuation. If the liquid slag layer is thicker and the viscosity of casting powder is small, the shell will not be easily torn and stuck and the casting powder can lubricate well. If the liquid level fluctuates too much, the liquid casting powder cannot be supplied and the liquid slag layer becomes thinner. The product of the oscillation amplitude h and oscillation frequency f reflects the influences of mold oscillation. If the amplitude is fixed and the oscillation frequency is higher, the primary shell will be easily torn. Similarly, if the vibration frequency is fixed and the amplitude is higher, the primary shell will also be easily torn. If the casting speed vc is higher, the shell tearing sensitivity and occurrence probability of the sticker will increase. Rapid change of casting speed can also interfere the timely supply of mold powder and then the liquid slag layer will become thinner. It will inevitably affect the lubrication between the shell and copper plate and the shell tearing sensitivity will grow.

Analysis on casting process factors affecting sticker

Based on the above theoretical analysis, the casting process factors affecting the actual sticker are further investigated through the following field experiment. This experiment is carried out in a straight-curved slab-continuous caster. The caster has two strands, an arc radius of 9.5 m, and the casting slab section size is 230×(900 ~ 2,150) mm2. The operation casting speed is 0.80 ~ 2.03 m/min. The corresponding mold in the caster is a combined straight mold with the length of 900 mm, which is comprised of four copper plates: broad face fixed side, broad face loose side, narrow face left, and narrow face right. The width of the mold can be adjusted according to the slab width. In order to detect the formation and propagation behavior of the sticker, more rows of thermocouples in high density are embedded in mold copper plates for monitoring local temperature variation at different locations: 6 rows of 12 columns, a total of 72 thermocouples are embedded in each broad face; 6 rows of 2 columns, a total of 12 thermocouples are embedded in each narrow face. In total, 168 thermocouples are installed in the four copper plates.

Measured data from the slab-continuous caster are collected and sorted for nearly 10 months. According to the actual breakout record, sticker’s alarm record, thermocouples’ temperature, casting speed and mold level change, etc., 31 samples of slab sticker are obtained. By these samples, the influence of casting process factors (such as casting speed, mold level fluctuation, degree of superheat heat, slab dimension, etc.) on the stickers is analyzed statistically.

Casting speed

Table 1 shows the stickers’ times and frequency under different casting speeds for the slabs with the width of 1,500 ~ 1,550 mm. The frequency of stickers is equal to the stickers’ times over the corresponding casting heats. The stickers under casting speeds of 0.8 and 0.9 m/min occur at the initial stage of casting process, which are not to be considered. Under casting speeds of 1.0 ~ 1.2 m/min, the frequency of stickers will grow significantly at a high casting speed. Because if the casting speed is higher, the solidified shell becomes thinner inside the mold, and meanwhile the consumption of casting powders will reduce, and the powders will be easily distributed more unevenly inside the mold. So, under high-speed condition, flow-in conditions of the powders are easier to deteriorate and even liquid slags are broken, giving rise to direct contact between the primary shell and copper plate and thereby generate the sticker. Proper casting powder is also one important means to avoid the sticker at high casting speed. For the slabs with the width of 1,500 ~ 1,550 mm, improper physical and chemical performance of casting powder is one key reason for high incidence of stickers.

Table 1:

Number of stickers under different casting speeds.

Slab dimension, mm2230×(1,500 ~ 1,550)
Casting speed, m/min0.80.91.01.11.2
Stickers’ times113215
Frequency of stickers, times/heat––0.002560.002720.00505

Mold level fluctuation

Normally, the liquid level of the mold fluctuates within 3 mm. Mold level fluctuation prior to sticking is investigated by the above 31 samples of the sticker, as shown in Table 2. From the table, mold level fluctuation prior to sticking is bigger or equal to 4 mm in 22 stickers. The bigger liquid-level fluctuation is one key factor of inducing sticker. As shown in Figure 2, the liquid-level fluctuation reaches about 9 mm prior to one sticker breakout. When the liquid-level fluctuation is bigger, it will affect the liquid slag which uniformly flows into the gap between the copper plate and shell, and uniformity of primary solidification of the shell.

Figure 2: A sample of sticker caused by bigger liquid-level fluctuation.
Figure 2:

A sample of sticker caused by bigger liquid-level fluctuation.

Table 2:

Relationship between level fluctuation prior to sticking and number of stickers.

Mold level fluctuation prior to sticking, mm≤3456≥7total
Number of stickers91073231

Degree of superheat heat

As shown in Figure 3, the degree of the superheat of four samples is over the required normal range in effective 27 samples of the sticker, especially when the degree of the superheat is too low, e. g. for the sample 22, the degree of the superheat is only 1 ℃, the melting rate of the casting powders is reduced, and insufficient flow-in liquid slag leads to this sticker. If the degree of the superheat is too high, it will reduce the strength of the shell near the meniscus and increase the sticking risk too. Proper degree of superheat will facilitate melting and lubrication of the casting powders and improve the uniform distribution of casting powders. So the degree of superheat is one key factor of affecting sticker and the casting temperature should be stably controlled to be within the proper range.

Figure 3: Effect of degree of the superheat on slab sticker.
Figure 3:

Effect of degree of the superheat on slab sticker.

Slab dimension and sticker’s position

Table 3 shows that the sticker’s position of slabs with medium and small width may be located at the middle and corner. The sticker’s positions of the wide slab mainly occur at the middle of the broad face and are related to many field conditions, such as insertion depth and side holes’ design of the submerged entry nozzle. For the slab, the possibility of sticker at the middle of the broad face is high, which is given by the two narrow faces featuring high cooling and shrinkage. The shell will protrude outward at the middle of the broad face under the action of static pressure of molten steel. The shell is thinner, the liquid slag layer becomes thinner, and the shell is easy to directly contact the copper plate and stick.

Table 3:

Relationship between slab dimension and sticker’s position.

Slab width, mmNumber of corner stickersNumber of medium stickers
1,30011
1,500416
1,55002
1,80006
2,00001

Mold cooling

To ensure uniform solidification of the shell in slab-continuous casting, generally heat flux ratio of narrow and broad face for the mold is controlled to be within 0.8 ~ 0.9. Table 4 shows that the heat flux ratio of narrow and wide face is over 0.9 and the heat flux ratio is lower on the broad face in the 6 counted sticker breakout samples. It indicates that the broad face cooling is weaker and the narrow face cooling is stronger under the existing process condition, so the cooling water volume of the broad face should be properly increased. The heat flux of the narrow face can be properly weakened via the narrow side taper, cooling water volume and casting powders to ensure uniform cooling and solidification of the slab. Figure 4 shows that the heat flux of the narrow face is significantly higher than that of the wide face prior to breakout and fluctuates much. It may be caused by nonuniform flow-in of the casting powders due to higher mold level fluctuation. It will make the shell directly contact the cooper plate, increase the friction, and generate the sticker. From Figure 5, the heat flux of the narrow face is significantly higher than that of the wide face, which indicates that the narrow face is excessively cooled. It is found that before this sticker breakout, the heat flux of each face of the mold does not change obviously. So it can be seen that after sticking, the propagation behavior of the sticker cannot be effectively identified by the heat flux variation.

Figure 4: Heat flux variation of each face of the mold before breakout for sample 2.
Figure 4:

Heat flux variation of each face of the mold before breakout for sample 2.

Figure 5: Heat flux variation of each face of the mold before breakout for sample 6.
Figure 5:

Heat flux variation of each face of the mold before breakout for sample 6.

Table 4:

Average heat flux in 3 min before a sticker breakout.

Sticker breakout sampleCasting speed, m/minHeat flux of each face of mold, MW/m2Heat flux ratio of narrow and broad face
Fixed sideLoose sideLeft sideRight side
10.90.89100.90871.01361.08611.09 ~ 1.28
21.00.90380.94541.29241.25071.26 ~ 1.53
31.11.14031.16861.20081.08730.90 ~ 1.08
41.11.03871.04471.29841.08550.99 ~ 1.49
51.21.05991.04701.08541.03560.98 ~ 1.31
61.21.01991.05911.40851.39941.29 ~ 1.41

Conclusions

This paper establishes the tearing model of the shell’s sticker according to the mechanical strength theory based on the stress characteristics of primary solidified shell inside the mold, analyzes the inherent formation mechanism of the shell’s sticker, gets the inherent factors affecting the shell tearing and sticking, including yield strength, liquid slag layer thickness inside the mold, viscosity of casting powder, casting speed, mold oscillation amplitude and frequency, and qualitatively studies the law of their influences on sticker.

The influence of casting process factors on the sticker is investigated according to the actual measurement data of plentiful samples of actual stickers. On the one hand, the investigation results have verified theoretical formation model of the shell’s sticker. Analysis results of actual data are consistent with the qualitative analysis of theoretical model. On the other hand, it is found that the current possible reasons inducing stickers include understability of casting powder operation condition, too low degree of superheat of molten steel, too big fluctuation of liquid level, weaker cooling of broad face of the mold, excessive cooling of narrow face, etc.

Proper casting process parameters are the foundation and guarantee for realizing stable and efficient continuous casting. To proactively prevent against sticker from the source, it is necessary to reasonably design the casting process parameters, such as casting powder, submerged entry nozzle and mold taper, and make sure to get proper and stable casting degree of superheat, develop a rational mold cooling system for uniformity of the cooling and solidification of slab, and reasonably control the heat flux of the mold.

Funding statement: The authors are grateful to the financial support for this project from the National Natural Science Foundation of China (Grant No. 51504002).

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Received: 2018-01-09
Accepted: 2018-07-30
Published Online: 2018-09-12
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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https://doi.org/10.1515/htmp-2018-0005
Keywords for this article
continuous casting; sticker breakout; mold; solidified shell; casting process factors
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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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