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Impurity Distribution after Solidification of Hypereutectic Al-Si Melts and Eutectic Al-Si Melt

  • Yanlei Li EMAIL logo , Jian Chen and Songyuan Dai
Published/Copyright: December 15, 2018
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

Hypereutectic Al-Si melts and eutectic Al-Si melt were solidified to study boron and phosphorus distributions in primary silicon phase, eutectic silicon phase and eutectic aluminum phase during Al-Si solvent refining. The boron and phosphorus contents in the primary silicon phase and the eutectic silicon phase were determined by ICP-OES, and the boron and phosphorus contents in the eutectic aluminum phase were calculated by the principle of mass conservation. The primary silicon phase has lowest boron and phosphorus contents, while the eutectic aluminum phase has highest boron and phosphorus contents.

Keywords: silicon purification; Al-Si alloy; impurity distribution
JEL Classification: 81.10.Fq

Introduction

Photovoltaic modules have been installed in many countries, and it is an effective method for protecting environment. Silicon-based solar modules dominate photovoltaic market, and solar grade silicon is the raw material for silicon-based solar modules. The solar grade silicon needs high purity, and it is refined from metallurgical grade silicon. The traditional processes to purify silicon use chemical methods [1], which change the metallurgical grade silicon into compounds, such as SiHCl3 and SiH4, purify these compounds, and reduce them into high purity silicon. These processes have complicated procedures and high energy consumption. New methods with simple procedures and low cost to purify silicon, such as via metallurgical processes, are needed.

When the metallurgical grade silicon is purified by the metallurgical processes, boron and phosphorus are difficult to remove because they have high segregation coefficients (value of 0.8 and 0.35) in silicon [2]. The solidification of hypereutectic Al-Si melt can remove boron and phosphorus efficiently, because their segregation coefficients in Al-Si melt are smaller than that in silicon [3, 4, 5, 6, 7, 8].

After the solidification of hypereutectic Al-Si melt, there are three kinds of phases existed in theory, primary silicon phase, eutectic silicon phase and eutectic aluminum phase. They form in different stages in the solidification process. The primary silicon phase is the product of uniform grain growth in the early stage. The eutectic silicon phase and the eutectic aluminum phase form in the eutectic reaction in the final solidification stage. The boron and phosphorus contents in the primary silicon phase have been studied by many researchers [9, 10, 11, 12, 13, 14]. But the boron and phosphorus contents in the eutectic silicon phase and the eutectic aluminum phase have never been studied, and it is investigated in this work.

In addition, many researchers, such as K. Morita [3, 4, 5], K. Tang [6], L. Zhao [7], L. Hu [8] studied the boron and phosphorus segregation coefficients in the Al-Si melt, and found that the boron and phosphorus segregation coefficients in the Al-Si melt decrease with decreasing temperature. It means that the boron and phosphorus removal rates increase with decreasing temperature in hypereutectic Al-Si melt. The lowest temperature in the hypereutectic Al-Si melt is the eutectic point temperature, and the eutectic reaction happens at this temperature [15]. The boron and phosphorus removal rates at this temperature have never been studied, and it is investigated in this work.

In this work, two series of experiments were carried out to clarify the boron and phosphorus distributions in the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase. Hypereutectic Al-Si melts (Al-20%Si) were solidified at different cooling rate, and the boron and phosphorus distributions in the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase are discussed. Eutectic Al-Si melt (Al-12.6%Si) was solidified at relatively small cooling rate, and the boron and phosphorus distributions in the eutectic silicon phase and the eutectic aluminum phase are discussed.

Experimental

The raw materials used in this work are industrial grade aluminum and metallurgical grade silicon, and impurities contents in them determined by inductively coupled plasma optical emission spectrometry (ICP-OES) are shown in Table 1.

Table 1:

Impurities contents in the raw materials (ppmw).

Impurity elementBPAlFeCaCuMn
In silicon7117911357471264
In aluminum735Bal.927911371612907

The boron and phosphorus distributions after the solidification of hypereutectic Al-Si melts

The raw materials were prepared for Al-20%Si, which means that it is a hypereutectic Al-Si alloy. As summarized in Figure 1, the raw materials (approximate 250 g) were put in an alumina crucible (I.D.: 55 mm, and depth: 100 mm). The alumina crucible was put in a resistance heating furnace with a proportional-integral-derivative (PID) controller to control temperature. The furnace was heated to 1071 K (100 K above the liquidus temperature of Al-20%Si) in the atmosphere of argon, and the alloy melted. After that, the melt was stirred by a quartz rod to mix it completely, and cooled to 830 K (20 K below the eutectic temperature) to solidify it into an ingot with the cooling rate shown in Table 2. After that, the sample was furnace cooled to room temperature.

Figure 1: The schematic process of sample preparation and analysis.
Figure 1:

The schematic process of sample preparation and analysis.

Table 2:

Lists of samples.

Experiment seriesSample numberSilicon ratioCooling rare (mK/s)
Series 1No.120%47
No.26.5
No.30.81
Series 2No.412.6%0.038

The solidified ingot was cut into two parts along its vertical axis. The cutting surface of one part was polished and analyzed by an optical scanner for macrostructure analysis and scanning electron microscope (SEM) for microstructure analysis. The other part was put in 50% diluted hydrochloric acid at 323 K. The hydrochloric acid dissolved the eutectic aluminum phase, leaving the primary silicon phase (shape of flake) and the eutectic silicon phase (shape of powder). Then the primary silicon phase and the eutectic silicon phase were washed with deionized water, dried and separated by sieving with mesh size of 0.5 mm. Then the boron and phosphorus contents in the primary silicon phase and the eutectic silicon phase were determined by ICP-OES.

The boron and phosphorus distributions after the solidification of eutectic Al-Si melt

The raw materials were prepared for Al-12.6%Si, which means that it is a eutectic Al-Si alloy. As summarized in Figure 1, the raw materials (approximate 250 g) were put in an alumina crucible (I.D.: 55 mm, and depth: 100 mm). The alumina crucible was put in a resistance heating furnace with a proportional-integral-derivative (PID) controller to control temperature. The furnace was heated to 900 K (50 K above the eutectic temperature), and the alloy melted. After that, the melt was stirred by a quartz rod to mix it completely, and cooled to 830 K (20 K below the eutectic temperature) to solidify it into an ingot with the cooling rate shown in Table 2. After that, the sample was furnace cooled to room temperature.

The solidified sample was put in 50% diluted hydrochloric acid at 323 K. The hydrochloric acid dissolved the eutectic aluminum phase, leaving the eutectic silicon phase (shape of powder). The eutectic silicon phase was washed with deionized water and dried. The boron and phosphorus contents in the eutectic silicon phase were determined by ICP-OES.

Results and discussion

The morphology of the primary silicon phase and the eutectic silicon phase

Figure 2 shows the cross section of solidified sample No.2. It can be found that the primary silicon phases (C) locate at the edge of the image, and the eutectic Al-Si matrix (A) and a cavity (B) can be seen.

Figure 2: The cross section of solidified sample No.2.
Figure 2:

The cross section of solidified sample No.2.

In the hypereutectic Al-Si melt, when temperature is lower than liquidus, the primary silicon phase begins to grow. In this work, heat transports from melt into surrounding environment, and the temperature at the edge of the melt is lower than that in the middle of the melt. So the primary silicon phase first nucleates there and grows. According to the lever law and the Al-Si phase diagram [15], the amount of the primary silicon phase is constant. So when the primary silicon phase grows at the edge of the melt, and it cannot form in the middle of the melt.

When the primary silicon phase grows in the hypereutectic Al-Si melt, the composition of the remaining melt changes with liquidus. When the temperature drops at 850 K and the silicon ratio is 12.6%, the eutectic reaction happens. In this reaction, the primary silicon phase and the eutectic silicon phase form, and they show as Al-Si matrix in macrostructure.

A cavity can be found in the image. At high temperature, Al-Si melt can absorb water vapor from environment and react with it, resulting in hydrogen atoms generated and dissolved in the melt. During the solidification of the alloy, the hydrogen atoms are rejected by the growing solid phase. If the hydrogen atoms cannot diffuse out of the melt during the solidification process, they will be trapped by the solid, forming hydrogen bubble. It appears as a cavity after cutting open the solidified ingot.

Figure 3(a) shows the SEM image of solidified sample No.2. It can be found primary silicon phase (D), eutectic silicon phase (E), eutectic aluminum phase (F) and white phases with needle like. To confirm the composition of the white phases, EDS analysis was conducted at Point 1, and the results are shown in Figure 3(b) and Table 3. It can be found that the white phase is an Al-Si-Fe-Mn phase. Because of the impurities in the raw materials, the Al-Si-Fe-Mn intermediate compound phase forms in the solidification process.

Figure 3: The SEM image of solidified sample No.2 and EDS image of Point 1 (a) SEM image of solidified sample No.2, (b) EDS image of Point 1.
Figure 3:

The SEM image of solidified sample No.2 and EDS image of Point 1 (a) SEM image of solidified sample No.2, (b) EDS image of Point 1.

Table 3:

EDS quantitative analysis of point 1 located in Figure 3(a).

EDS analysisElement (Atom %)
AlSiFeMnTotal
Point 158.5419.7619.662.04100

Figure 4 shows the morphology of the primary silicon flakes and eutectic silicon powder. They are obtained after the hydrochloric treatment of solidified sample No.2. The primary silicon flake is corresponding to the primary silicon phase (D) in Figure 3(a), and the eutectic silicon phase is corresponding to eutectic silicon phase (E) in Figure 3(a). The eutectic aluminum phase and the Al-Si-Fe-Mn phase in Figure 3(a) were reacted with the hydrochloric acid.

Figure 4: The morphology of primary silicon flakes and eutectic silicon powder, (a) primary silicon flakes, (b) eutectic silicon powder.
Figure 4:

The morphology of primary silicon flakes and eutectic silicon powder, (a) primary silicon flakes, (b) eutectic silicon powder.

As discussed before, the primary silicon phase grows in the temperature range between 971 K and 850 K, and it grows into the shape of flake. The eutectic silicon phase forms at 850 K in the eutectic reaction. It does not have enough time to grow up and appears as powder after solidification.

The boron and phosphorus distributions after the solidification of the hypereutectic Al-Si melt

According to the result of microstructure in Figure 3, the primary silicon phase, the eutectic silicon phase, the eutectic aluminum phase and the Al-Si-Fe-Mn intermediate compound phase form after the solidification of hypereutectic Al-Si melt in this work. The amount of Al-Si-Fe-Mn intermediate compound phase is small because of small Fe and Mn contents (＜1%) in the raw materials. Besides, according to the EDS result in Figure 3(b) and Table 3, The Al-Si-Fe-Mn intermediate compound phase does not contain boron and phosphorus. So the boron and phosphorus contents in the Al-Si-Fe-Mn intermediate compound are ignored in the following calculation.

We take boron as example to discuss the distribution of impurity element. The boron contents in the raw materials industrial grade aluminum and metallurgical grade silicon can be determined by ICP-OES, and they are shown in Table 1. The boron contents in the primary silicon phase and the eutectic silicon phase after solidification of Al-Si melt can be confirmed by ICP-OES, and the values are shown in Table 4. The boron content in the eutectic aluminum phase can be obtained as following.

Table 4:

Boron and phosphorus contents in the primary silicon phase and the eutectic silicon phase.

Sample numberBoron content (ppmw)Phosphorus content (ppmw)
In the primary silicon phaseIn the eutectic silicon phaseIn the primary silicon phaseIn the eutectic silicon phase
Series 1 No.14.385.2726.2429.48
Series 1 No.21.213.1712.0624.60
Series 1 No.30.693.0610.8221.26

According to the Al-Si phase diagram [15] and level rule, the mass fractions of the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase after solidification of Al-20%Si can be calculated as 0.00847, 0.1153, and 0.8, respectively.

According to the conservation of mass, the boron distribution should follow eq. (1).

(1)0.00847CPSi+0.1153CESi+0.8CEAl=0.2CSi+0.8CAl

where, CPSi, CESi, CEAl, CSi and CAl are the boron contents in the primary silicon phase, the eutectic silicon phase, the eutectic aluminum phase, the raw material metallurgical grade silicon and the raw material industrial grade aluminum respectively.

As discussed before, CSi and CAl are shown in shown in Table 1, and CPSiCESi are shown in Table 4. So CEAl can be obtained in eq. (2).

(2)CEAl=(0.2CSi+0.8CAl)−(0.00847CPSi+0.1153CESi)0.8

At last, the values of CEAl are all obtained.

Figure 5 shows the boron contents in the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase after the solidification of Al-20%Si melt with different cooling rates (experiment series 1, sample No.1, 2, 3). It is obvious that it is a hypereutectic Al-Si solidification. The initial boron content in the melt is 7 ppmw which is obtained by 0.2CSi+0.8CAl, and it is marked with dotted line in Figure 5.

Figure 5: The boron contents in experiment series 1.
Figure 5:

The boron contents in experiment series 1.

Figure 5 indicates that the boron content in primary silicon phase is lowest, and the boron content in the eutectic aluminum phase is highest. It can be explained and discussed below.

In the hypereutectic Al-Si melt, the primary silicon phase begins to grow when temperature falls below its liquidus, and the composition of the remaining melt changes with liquidus. At the same time boron atoms are excluded by the growing primary silicon phase, because its segregation coefficient is smaller than 1. When the silicon ratio is 12.6% and the temperature is 577 °C, the eutectic reaction happens, and the eutectic silicon phase and the eutectic aluminum phase form. At the time the boron content in the melt is higher than that in the primary silicon phase because boron atoms are enriched in the melt as discussed before. According to the work of M.M. Makhlouf [16], the eutectic silicon phase is the leading phase in the Al-Si eutectic reaction. So boron atoms are rejected by the eutectic silicon phase, and they are enriched in the eutectic aluminum phase. So the boron content in the primary silicon phase is lowest, and the boron content in the eutectic aluminum phase is highest.

Figure 5 also shows that the cooling rate has great influence on the boron contents in the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase. It can be explained and discussed below.

As discussed before, when the primary silicon phase grows, boron atoms are rejected. They are enriched at the solid liquid interface, and diffuse into the remaining melt. The boron content in the primary silicon phase depends on the boron segregation coefficient and the boron content at the solid liquid interface as shown in eq. (3).

(3)CPSi=kCinterface

where, CPSi, k and Cinterface are the boron content in the primary silicon phase, the segregation coefficient of boron, and the boron content at the solid liquid interface respectively.

When the cooling rate is low, the enriched boron atoms at the solid liquid interface has enough time to diffuse into the remaining melt, and the boron content at the solid liquid interface decreases. According to eq. (3), the boron content in the primary silicon phase is low.

In equilibrium solidification, the Al-Si eutectic reaction happens at the temperature of 577 °C, but the equilibrium solidification cannot be satisfied in this work. When the cooling rare is low, the eutectic reaction happens slowly. As mentioned before, the eutectic silicon phase is the leading phase in the Al-Si eutectic reaction. So boron atoms are rejected by the eutectic silicon phase and enriched in the eutectic aluminum phase. At last, when the cooling rate is low, the boron content in eutectic silicon phases is low, and the boron content in the eutectic aluminum is high.

Figure 6 shows the phosphorus contents in the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase after the solidification of Al-20%Si melt with different cooling rates (experiment series 1, sample No.1, 2, 3). The initial phosphorus content in the melt is 30.2 ppmw obtained by the same way as that of boron, and it is marked with dotted line in Figure 6. The distribution of phosphorus is similar to that of boron as discussed before.

Figure 6: The phosphorus contents in experiment series 1.
Figure 6:

The phosphorus contents in experiment series 1.

The boron and phosphorus distributions after the solidification of the eutectic Al-Si melt

After the solidification of the eutectic Al-Si melt (experiment series 2 No.4 in this work), the eutectic silicon phase and the eutectic aluminum phase form, and the primary silicon phase does not form. With the same calculation method mentioned before, the boron and phosphorus contents in the eutectic silicon phase and the eutectic aluminum phase can be obtained.

Figure 7(a) shows the boron contents in the eutectic silicon phase and the eutectic aluminum phase after the solidification of sample series 2 No.4. The boron contents in the eutectic silicon phase and the eutectic aluminum phase are 3.5 and 7.5 ppmw, respectively. The black dotted line shows the initial average boron content in the melt (value of 7 ppmw).

Figure 7: The boron and phosphorus distributions in sample series 2 No.4, (a) boron distribution, (b) phosphorus distribution.
Figure 7:

The boron and phosphorus distributions in sample series 2 No.4, (a) boron distribution, (b) phosphorus distribution.

It can be found that the boron content in the eutectic silicon phase is lower than that in the eutectic aluminum phase. As discussed before, the eutectic silicon phase is the leading phase in the eutectic reaction. So the eutectic silicon phase can reject boron atoms, and has lower boron content after solidification. This result is in accordance with the result of the hypereutectic Al-Si melts solidification.

Figure 7(b) shows the phosphorus contents in the eutectic silicon phase and the eutectic aluminum phase after the solidification of sample series 2 No.4. The red dotted line shows the initial average phosphorus content in the melt (32 ppmw). The phosphorus distribution in the eutectic silicon phase and the eutectic aluminum phase is similar to that of boron as discussed before.

Conclusions

The hypereutectic Al-Si melts and the eutectic Al-Si melt were solidified to study the boron and phosphorus distributions in the primary silicon phase, the eutectic silicon phase and the eutectic aluminum phase during Al-Si solvent refining. In hypereutectic Al-Si melt, the primary silicon phase can reject boron and phosphorus atoms, and it has lowest boron and phosphorus contents after solidification. In the eutectic reaction, the eutectic silicon phase is the leading phase, and it can reject boron and phosphorus atoms. The eutectic aluminum phase has highest boron and phosphorus contents after solidification.

Acknowledgements

This work was supported by Project of Science and Technology Department of Henan Province (No. 172102210460), Doctoral Scientific Research Foundation of Xinyang Normal University, and Nanhu Scholars Program for Yong Scholars of XYNU.

References

[1] A. Saito, A. Sakurai and H. Habuka, J. Cryst. Growth, 468 (2017) 204–207.10.1016/j.jcrysgro.2016.10.035Search in Google Scholar

[2] F.A. Trumbore, Bell Syst. Techn. J., 39 (1960) 205–233.10.1002/j.1538-7305.1960.tb03928.xSearch in Google Scholar

[3] T. Yoshikawa and K. Morita, Metall. Mater. Trans. B, 36 (2005) 731–736.10.1007/s11663-005-0076-2Search in Google Scholar

[4] T. Yoshikawa and K. Morita, J. Cryst. Growth, 311 (2009) 776–779.10.1016/j.jcrysgro.2008.09.095Search in Google Scholar

[5] T. Yoshikawa and K. Morita, Sci. Techn. Advan. Mater., 4 (2003) 531–537.10.1016/j.stam.2003.12.007Search in Google Scholar

[6] K. Tang, E.J. Øvrelid, G. Tranell and M. Tangstad, Mater. Trans., 50 (2009) 1978–1984.10.2320/matertrans.M2009110Search in Google Scholar

[7] L.X. Zhao, Z. Wang, Z.C. Guo and C.Y. Li, Tran. Nonferrous Met. Soc. China, 21 (2011) 1185–1192.10.1016/S1003-6326(11)60841-8Search in Google Scholar

[8] L. Hu, Z. Wang, X.Z. Gong, Z.C. Guo and H. Zhang, Metall. Mater. Trans. B, 44 (2013) 828–836.10.1007/s11663-013-9850-8Search in Google Scholar

[9] X. Gu, X.G. Yu and D.R. Yang, Sep. Purif. Technol., 77 (2011) 33–39.10.1016/j.seppur.2010.11.016Search in Google Scholar

[10] P.P. Wang, H.M. Lu and Y.S. Lai, J. Cryst. Growth, 390 (2014) 96–100.10.1016/j.jcrysgro.2013.12.024Search in Google Scholar

[11] J.W. Li, Z.C. Guo, H.Q. Tang and J.C. Li, High Temp. Mater. Proc, 32 (2013) 503–510.10.1515/htmp-2012-0157Search in Google Scholar

[12] Y.L. Li, J. Chen, B.Y. Ban, T.T. Zhang and S.Y. Dai, High Temp. Mater. Proc., 34 (2015) 43–49.Search in Google Scholar

[13] B.B. Ban, X.L. Bai, J.W. Li, J. Chen and S.Y. Dai, J. Alloy Compd., 685 (2016) 604–609.10.1016/j.jallcom.2016.05.312Search in Google Scholar

[14] X.L. Bai, B.Y. Ban, J.W. Li, Z.Q. Fu, Z.J. Peng, C.B. Wang and J. Chen, Sep. Purif. Technol., 174 (2017) 345–351.10.1016/j.seppur.2016.11.002Search in Google Scholar

[15] J.L. Murray, A. J. McAlister, 5 (1984) 74–84.10.1007/BF02868729Search in Google Scholar

[16] M.M. Makhlouf and H.V. Guthy, J. Light Met., 1 (2001) 199–218.10.1016/S1471-5317(02)00003-2Search in Google Scholar

Received: 2018-07-18
Accepted: 2018-10-02
Published Online: 2018-12-15
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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  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-2018-0117
Keywords for this article
silicon purification; Al-Si alloy; impurity distribution
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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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