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Number of results: 14
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Abstract

Processing of metal alloys in semi-solid state is a way of producing many near net-shape parts and nowadays is commercially successful. Particular behaviour of alloys in the partially liquid state, having non-dendritic microstructure, is a base for thixoforming processing. Processing materials in the semi-solid state concerns alloys with relatively wide solidification range. Thermodynamic modelling can be used as a one of a potential tools that allow to identify alloys with proper temperature range. It means that the key feature of alloys suitable for thixoforming is a widely enough melting range, allowing for precise control of material temperature. The data gathered from thermodynamics calculations can also pay off in the industrial thixoforming processes design. The goal of this paper is to identify copper alloys which can be successfully shaped in the semi-solid state. Apart to thermodynamic calculations, the observations on high temperature microscope was carried out. During experiments the solidus, liquidus and also deformation temperatures can be determined. An experimental work allows confirming results obtained within the confines of thermodynamic calculations and firstly to determine the deformation temperatures which are the optimal for shaping processes. The basic achievement of this work is an identification of copper alloy groups possible for shaping in the semi-solid state. At the first part of the paper, the basic criteria of suitable alloys were described. Next, both the solid fraction curves for copper alloys with different alloying elements using ProCAST software and the phase diagrams were determined to identify the solidification temperature ranges of these alloys. In the second part of these paper, the identification of the deformation temperatures was carried out with use of high temperature microscope observation.
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Authors and Affiliations

A. Madetko
1
ORCID: ORCID
K. Sołek
1
ORCID: ORCID
P. Drożdż
1
ORCID: ORCID

  1. AGH University of Science and Technology, Faculty of Metals Engineering and Industrial Computer Science, al. Mickiewicza 30, 30-059 Krakow, Poland
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Abstract

Effect of Cu addition on oxide growth of Al-7 mass%Mg alloy at high temperature was investigated. As-cast microstructures of Al-7 mass%Mg and Al-7 mass%Mg-1 mass%Cu alloys showed α-Al dendrites and area of secondary particles. The 1 mass%Cu addition into Al-7 mass%Mg alloy formed Mg32(Al, Cu)49 ternary phase with β-Al3Mg2. The total fraction of two Mg-containing phases in Cu-added alloy was higher than the β-Al3Mg2 fraction in Cu-free alloy. From measured weight gains depending on time at 500°C under an air atmosphere, it was shown that all samples exhibited significant weight gains depending on time. Al-7mass%Mg-1mass%Cu alloy showed the relatively increased oxidation rate when compared with Cu-free alloy. All the oxidized cross-sections throughout the entire oxidation time showed coarse and dark areas regarded as oxides grown from the surface to inside, but bigger oxidized areas were formed in the Al-7mass%Mg-1mass%Cu alloy containing higher fraction of Mg-based phases in the as-cast microstructure. As a result of compositional analysis on the oxide clusters, it was found that the oxide clusters contained Mg-based oxides formed through internal oxidation during a long time exposure to oxidizing environments.
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Bibliography

[1] J.R. Davis, ASM International, Aluminum and Aluminum Alloys, Materials Park 1993.
[2] H. Watanabe, K. Ohori, Y. Takeuchi, Trans. Iron Steel Inst. Jpn. 27, 730 (1987).
[3] J.L. García-Hernández, C.G. Garay-Reyes, I.K. Gómez-Barraza, M.A. Ruiz-Esparza-Rodríguez, E.J. Gutiérrez-Castañeda, I. Estrada-Guel, M.C. Maldonado-Orozco, R. Martínez-Sánchez, J. Mater. Res. Technol. 8 (6), 5471 (2019).
[4] M . Mihara, C.D. Marioara, S.J. Andersen, R. Holmestad, E. Kobayashi, T. Sato, Mater. Sci. Eng. A, 658, 91 (2016).
[5] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, T.W. Lee, S.H. Lim, S.K. Kim, Int. J. Metalcast. 13, 121 (2019).
[6] G. Wu, K. Dash, M.L. Galano, K.A.Q. O’Reilly, Corros. Sci. 155, 97 (2019).
[7] B.H. Kim, S.H. Ha, Y.O. Yoon, H.K. Lim, S.K. Kim, D.H. Kim, Mater. Lett. 228, 108 (2018).
[8] H. Okamoto, J. Phase Equilibria 19, 598 (1998).
[9] T.S. Parel, S.C. Wang, M. J. Starink, Mater. Des. 31, S2 (2010).
[10] C.W. Bale, E. Bélisle, P. Chartrand, S.A. Decterov, G. Eriksson, A.E. Gheribi, K. Hack, I.H. Jung, Y.B. Kang, J. Melançon, A.D. Pelton, S. Petersen, C. Robelin, J. Sangster, P. Spencer, M.A. Van Ende, Calphad 54, 35 (2016).
[11] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, T.W. Lee, S.H. Lim, S.K. Kim, Sci. Adv. Mater. 10, 697 (2018).
[12] D . Ajmera, E. Panda, Corros. Sci. 102, 425 (2016).
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Authors and Affiliations

Seong-Ho Ha
1
ORCID: ORCID
Abdul Wahid Shah
1
ORCID: ORCID
Bong-Hwan Kim
1
ORCID: ORCID
Young-Ok Yoon
1
ORCID: ORCID
Hyun-Kyu Lim
1
ORCID: ORCID
Shae K. Kim
1
ORCID: ORCID

  1. Korea Institute of Industrial Technology (KITECH), Advanced Materials and Process R&D Department, Incheon 21999, Republic of Korea
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Abstract

Influence of Si addition on oxide layer growth of Al-6 mass%Mg alloys in molten state was investigated in this study. After melt holding for 24 h, the melt surface of only Si-free alloy became significantly bumpy, while no considerably oxidized surface was observed even with 1 mass%Si addition. There was no visible change on the appearance of melt surfaces with increasing Si content. As a result of compositional analysis on the melt samples between before and after melt holding, the Si-added alloys nearly maintained their Mg contents even after the melt holding for 24 h. On the other hand, the Mg content in the Si-free alloy showed a great reduction. The bumpy surface on Si-free alloy melt showed a large amount of pores and oxide clusters in its cross-section, while the Si-added alloy had no significantly grown oxide clusters on the surfaces. As a result of compositional analysis on the surfaces, the oxide clusters in Si-free alloy contained a great amount of Mg and oxygen. The oxide layer on the Si-added alloy was divided into Mg-rich and Mg-poor areas and contained certain amounts of Si. Such a mixed oxide layer containing Si would act as a protective layer during the melt holding for a long duration.
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Bibliography

[1] J.R. Davis, ASM International, Aluminum and Aluminum Alloys, Materials Park 1993.
[2] G . Wu, K. Dash, M.L. Galano, K.A.Q. O’Reilly, Corros. Sci. 155, 97 (2019).
[3] B.H. Kim, S.H. Ha, Y.O. Yoon, H.K. Lim, S.K. Kim, D.H. Kim, Mater. Lett. 228, 108 (2018).
[4] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, T.W. Lee, S.H. Lim, S.K. Kim, Sci. Adv. Mater. 10, 697 (2018).
[5] D . Ajmera, E. Panda, Corros. Sci. 102, 425 (2016).
[6] N. Smith, A. Kvithyld, G. Tranell, Metall. Mater. Trans. B 49, 2846 (2018).
[7] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, T.W. Lee, S.H. Lim, S.K. Kim, Int. J. Metalcast. 13, 121 (2019).
[8] J. Jeong, J. Im, K. Song, M. Kwon, S.K. Kim, Y.B. Kang, S.H. Oh, Acta Mater. 61, 3267 (2013).
[9] F . Zarei, H. Nuranian, K. Shirvani, Surf. Coat. Technol. 394, 125901 (2020).
[10] Y.L. Zhang, J. Li, Y.Y. Zhang, D.N. Kang, J. Alloys Compd. 827, 154131 (2020).
[11] W. Kai, P.C. Kao, P.C. Lin, I.F. Ren, J.S.C. Jang, Intermetallics 18, 1994 (2010).
[12] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, S.K. Kim, Sci. Adv. Mater. 10, 694 (2018).
[13] C.W. Bale, E. Bélisle, P. Chartrand, S.A. Decterov, G. Eriksson, A.E. Gheribi, K. Hack, I.H. Jung, Y.B. Kang, J. Melançon, A.D. Pelton, S. Petersen, C. Robelin, J. Sangster, P. Spencer, M.A. Van Ende, Calphad 54, 35 (2016).
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Authors and Affiliations

Young-Ok Yoon
1
ORCID: ORCID
Seong-Ho Ha
1
ORCID: ORCID
Abdul Wahid Shah
1
ORCID: ORCID
Bong-Hwan Kim
1
ORCID: ORCID
Hyun-Kyu Lim
1
ORCID: ORCID
Shae K. Kim
1
ORCID: ORCID

  1. Korea Institute of Industrial Technology (KITECH), Advanced Materials and Process R&D Department, Incheon 21999, Republic of Korea
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Abstract

Mechanical, electronic, thermodynamic phase diagram and optical properties of the FeVSb half-Heusler have been studied based on the density functional theory (DFT) framework. Studies have shown that this structure in the MgAgAs-type phase has static and dynamic mechanical stability with high thermodynamic phase consistency. Electronic calculations showed that this compound is a p-type semiconductor with an indirect energy gap of 0.39 eV. This compound’s optical response occurs in the infrared, visible regions, and at higher energies its dielectric sign is negative. The Plasmon oscillations have occurred in 20 eV, and its refraction index shifts to zero in 18 eV.
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Authors and Affiliations

A. Bagheri
1
A. Boochani
2
S.R. Masharian
1
F.H. Jafarpour
3

  1. Department of Physics, Hamedan Branch, Islamic Azad University, Hamedan, Iran
  2. Department of Physics, Kermanshah Branch, Islamic Azad University, Kermanshah, Iran
  3. Physics Department, Bu-Ali Sina University, 65174-4161 Hamedan, Iran
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Abstract

Dissolution of Si in Al-5 mass%Mg alloy melt by the reduction of SiO2 and its effect on microstructure formation of the alloy after solidification were investigated. Al-5 mass%Mg alloy without silica powder had approximately 0.05 mass%Si as an impurity. No significant difference in Si content was observed after the reaction with silica for 10 min, while the Si content increased up to about 0.12 mass% after 30 min. From the microstructure analysis and calculation of Scheil-Gulliver cooling, it was considered that as-cast microstructures of Al-5 mass%Mg-1 mass% SiO2 alloys had the distribution of eutectic phase particles, which are comprised of β-Al3Mg2 and Mg2Si phases. Based on the phase diagrams, only limited amount of Mg can be selectively removed by silica depending on the ratio of Si and Mg. Addition of silica of more than approximately 1.5 mass% in Al-5 mass%Mg alloy led to the formation of spinel and removal of both Mg and Al from the melt.
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Bibliography

[1] J.R. Davis, ASM International, Aluminum and Aluminum Alloys, Materials Park 1993.
[2] T. Hashiguchi, H. Sueyosh, Mater. Trans. 51, 838 (2010).
[3] B.H. Kim, S.H. Ha, Y.O. Yoon, H.K. Lim, S.K. Kim, D.H. Kim, Mater. Lett. 228, 108 (2018).
[4] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, S.K. Kim, Sci. Adv. Mater. 10, 694 (2018).
[5] R. Muñoz-Arroyo, H.M. Hdz-García, J.C. Escobedo-Bocardo, E.E. Granda-Gutierrez, J.L. Acevedo-Dávila, J.A. Aguilar-Martínez, A. Garza-Gomez, Adv. Mater. Sci. Eng. 2014, 1 (2014).
[6] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, S.K. Kim, Sci. Adv. Mater. 10, 694 (2018).
[7] C.W. Bale, E. Bélisle, P. Chartrand, S.A. Decterov, G. Eriksson, A.E. Gheribi, K. Hack, I.H. Jung, Y.B. Kang, J. Melançon, A.D. Pelton, S. Petersen, C. Robelin, J. Sangster, P. Spencer, M.A. Van Ende, Calphad 54, 35 (2016).
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Authors and Affiliations

Sun-Ki Kim
1
ORCID: ORCID
Seong-Ho Ha
2
ORCID: ORCID
Bong-Hwan Kim
2
ORCID: ORCID
Young-Ok Yoon
2
ORCID: ORCID
Hyun-Kyu Lim
2
ORCID: ORCID
Shae K. Kim
2
ORCID: ORCID
Young-Jig Kim
1
ORCID: ORCID

  1. Sungkyunkwan University, School of Advanced Materials Science and Engineering, Suwon 16419, Republic of Korea
  2. Korea Institute of Industrial Technology (KITECH), Advanced Materials and Process R&D Department, Incheon 21999, Republic of Korea
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Abstract

The application of aqueous two-phase systems (ATPS) is a cost-effective and simple method of protein separation (including enzymes) from complex systems. The first stage of designing the protein purification process in an ATPS involves the identification of the conditions for the formation of a given extraction system. For this purpose, the conditions for the formation of ATPSs in a thermoseparating EO50PO50 polymer/potassium phosphates system have been studied. Factors determining the ATPS formation comprised: separation temperature (4ºC or 20ºC), phosphate solution pH (6, 7.5 or 9) as well as the concentration of NaCl introduced into the systems (0.085 M, 0.475 M and 0.85 M). ATPS without NaCl were prepared as well. The conditions for the formation of the primary EO50PO50/potassium phosphate ATPS were determined with their phase diagrams. It was observed that with an increase of phosphate pH and NaCl concentration in the system, there was a decrease of the EO50PO50 and phosphate concentrations necessary to form a primary ATPS. After the primary two-phase separation, the top phase (rich in the EO50PO50 polymer) was partitioned from the bottom phase (rich in phosphates). Next, by means of polymer phase thermoseparation, a secondary two-phase system was formed. In the secondary EO50PO50/phosphate ATPS, the bottom phase was formed by the concentrated EO50PO50 polymer (30-80% concentration), while the top phase by a solution composed mainly of water, containing phosphate ions and remains of EO50PO50 polymer (3-7%).

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Authors and Affiliations

Radosław Dembczyński
Wojciech Białas
Tomasz Jankowski
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Abstract

In this study, precipitation of Ca in Al-Mg alloys containing a trace of Ca during homogenization was investigated using a transmission electron microscope (TEM) and calculated phase diagrams. TEM result indicated that the Ca-based particles found in the examined sample are Ca7Mg7.5Si14. From the calculation of Scheil-Gulliver cooling, it was found that the Ca was formed as Al4Ca and C36 laves phases with Mg2Si and Al13Fe4 from other impurities phase during solidification. No Ca-Mg-Si ternary phase existed at the homogenization temperature in the calculated phase diagram. From the phase diagram of Al-Al4Ca-Mg2Si three-phase isothermal at 490℃, it was shown that Ca7Mg6Si14 phase co-exists with Al, Mg2Si and Al4Ca in the largest region and with only Al and Mg2Si in Al4Ca-poor regions. It was thought that the Ca7Mg6Si14 ternary phase was formed by the interaction between Mg2Si and Al4Ca considering that the segregation can occur throughout the entire microstructures.
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Bibliography

[1] J.R. Davis, ASM International, Aluminum and Aluminum Alloys, Materials Park 1993.
[2] G . Wu, K. Dash, M.L. Galano, K.A.Q. O’Reilly, Corros. Sci. 155, 97 (2019).
[3] B.H. Kim, S.H. Ha, Y.O. Yoon, H.K. Lim, S.K. Kim, D.H. Kim, Mater. Lett. 228, 108 (2018).
[4] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, T.W. Lee, S.H. Lim, S.K. Kim, Sci. Adv. Mater. 10, 697 (2018).
[5] D. Ajmera, E. Panda, Corros. Sci. 102, 425 (2016).
[6] S.H. Ha, J.K. Lee, S.K. Kim, Mater. Trans. 49, 1081 (2008).
[7] S.H. Ha, B.H. Kim, Y.O. Yoon, H.K. Lim, T.W. Lee, S.H. Lim, S.K. Kim, Int. J. Metalcast. 13, 121 (2019).
[8] J.W. Jeong, J.S. Im, K. Song, M.H. Kwon, S.K. Kim, Y.B. Kang, S.H. Oh, Acta Mater. 61, 3267 (2013).
[9] K. Ozturk, L.Q. Chen, Z.K. Liu, J. Alloys Compd. 340, 199 (2002).
[10] C.W. Bale, E. Bélisle, P. Chartrand, S.A. Decterov, G. Eriksson, A.E. Gheribi, K. Hack, I.H. Jung, Y.B. Kang, J. Melançon, A.D. Pelton, S. Petersen, C. Robelin, J. Sangster, P. Spencer, M.A. Van Ende, Calphad 54, 35 (2016).
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Authors and Affiliations

Seong-Ho Ha
1
ORCID: ORCID
Young-Chul Shin
1
ORCID: ORCID
Bong-Hwan Kim
1
ORCID: ORCID
Young-Ok Yoon
1
ORCID: ORCID
Hyun-Kyu Lim
1
ORCID: ORCID
Sung-Hwan Lim
2
ORCID: ORCID
Shae K. Kim
1
ORCID: ORCID

  1. Korea Institute of Industrial Technology (KITECH), Incheon 21999, Republic of Korea
  2. Kangwon National University, Department of Advanced Materials Science and Engineering, Chuncheon 24341, Republic of Korea
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Abstract

Ti-containing steel weld metals with Al contents of 0.01-0.085% were prepared. The effects of Al contents on the inclusions evolution were investigated by means of thermodynamic calculations coupled with electron probe micro-analyses and transmission electron microscopy. The results show that the inclusions in the 0.01% Al weld metal are mainly composed of ilmenite with some amounts of (Mn-Si-Al)-oxide and titanial_spinel. When Al content is increased up to 0.035%, a more amount of corundum and a small amount of pseudobrookite are formed. In 0.085% Al weld metal, the (Mn-Si-Al)-oxide disappears completely, and the inclusions contain a substantial amount of corundum, in addition to a minimal amount of pseudobrookite. Ti3O5, MnTi2O4 and MnTiO3 are the primary constituents of pseudobrookite, titanial_spinel and ilmenite, respectively. Titanial_spinel and ilmenite have higher amounts of Mn, but lower Ti levels compared with pseudobrookite. In the case of presence of a considerable amounts of titanial_spinel and ilmenite, Mn-depleted zone is formed in matrix around the inclusions.

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Authors and Affiliations

Bingxin Wang
Yingtian Jiang
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Abstract

Thermodynamic descriptions of the ternary Fe-B-Cu system and its binary sub-system B-Cu aredeveloped in the context of a new Fe-B-X (X = Cr, Cu, Mn, Mo, Ni, Si, Ti, V, C) database. The thermodynamic parameters of the other binary sub-systems (Fe-B and Fe-Cu) are taken from earlier assessments. Experimental thermodynamic and phase equilibrium data available in the literature have been used for the optimization of the Fe-B-Cu and B-Cu systems’ thermodynamic parameters. The solution phases are described using a substitutional solution model and the compounds (two borides of the Fe-B system) are treated as stoichiometric phases. A good agreement was obtained between the calculated and the experimental thermodynamic and phase equilibrium data.

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Authors and Affiliations

Jyrki Miettinen
Ville-Valtteri Visuri
Timo Fabritius
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Abstract

Thermodynamic descriptions of the ternary Fe-B-Si system and its binary sub-system, B-Si, are developed in the context of a new Fe-B-X (X = Cr, Ni, Mn, V, Si, Ti, C) database. The thermodynamic parameters of the other binary sub-systems, Fe-Si and Fe-B, are taken from earlier assessments. Experimental thermodynamic and phase equilibrium data available in the literature has been used for the optimization of the thermodynamic parameters of the Fe-B-Si and B-Si systems. The solution phases are described using substitutional solution model and the compounds (silicides and borides) are treated as stoichiometric phases. The calculated and experimental thermodynamic and phase equilibrium data were found to be in good agreement.

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Authors and Affiliations

J. Miettinen
V-V. Visuri
T. Fabritius
N. Milcheva
G. Vassilev
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Abstract

Thermodynamic optimizations of the ternary Fe-B-Ti system and its binary sub-system, B-Ti are presented. The thermodynamic descriptions of the other binaries, Fe-Ti and Fe-B, are taken from the earlier studies slightly modifying the Fe-Ti system assessment. The adjustable parameters of the Fe-B-Ti and B-Ti systems are optimized in this study using the experimental thermodynamic and the phase equilibrium data from the literature. The solution phases of the system are described using the substitutional solution model and the compounds (including borides) are treated as stoichiometric phases. The results show a good correlation between the calculated and measured thermodynamic and phase equilibrium data.

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Authors and Affiliations

J. Miettinen
V-V. Visuri
T. Fabritius
N. Milcheva
G. Vassilev
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Abstract

Thermodynamic description of the Fe-B-C system in its iron-rich corner is developed in the context of a new Fe-B-X (X = Cr, Ni, Mn, Si, Ti, V, C) database. The thermodynamic parameters of the binary sub-systems, Fe-B, Fe-C and B-C, are taken from earlier assessments modifying the B-C description. The parameters of the Fe-B-C system are optimized in this study using experimental thermodynamic and phase equilibrium data from the literature. Liquid, beta-rhombo-B and graphite phases are described using the substitutional solution model, while the ferrite (bcc), the austenite (fcc), the cementite (M3C) and the M23C6 phases are described with the sublattice model and the borides, Fe2B, FeB and B4C, are treated as stoichiometric phases. A good correlation was obtained between the calculated and the experimental thermodynamic and phase equilibrium data. The description is recommended to be used at the composition region of wt% C + wt% B < 15 and at temperatures below 2700oC.

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Authors and Affiliations

J. Miettinen
V.-V. Visuri
T. Fabritius
G. Vassilev
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Abstract

Thermodynamic descriptions of the ternary Fe-B-V system and its binary sub-system B-V, are developed using experimental thermodynamic and phase equilibrium data from the literature. The thermodynamic parameters of the other binaries, Fe-V and Fe-B, are taken from earlier assessments slightly modifying the Fe-V description. The work is in the context of a new Fe-B-X (X = Cr, Ni, Mn, V, Si, Ti, C) database.

The solution phases are described using substitutional solution model. The borides are treated as stoichiometric or semi-stoichiometric phases and described with two-sublattice models.

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Authors and Affiliations

J. Miettinen
V.-V. Visuri
T. Fabritius
N. Milcheva
G. Vassilev
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Abstract

Thermodynamic optimizations of the ternary Fe-B-Mo system and its binary sub-system B-Mo are presented. The Fe-B-Mo description is then extended to the quaternary Fe-B-Cr-Mo system by assessing the ternary B-Cr-Mo system. The thermodynamic descriptions of the other binaries (Fe-B, Fe-Cr, Fe-Mo, B-Cr, and Cr-Mo) and the other ternaries (Fe-B-Cr and Fe-Cr-Mo) are taken from earlier studies. In this study, the adjustable parameters of the B-Mo, Fe-B-Mo, and B-Cr-Mo systems were optimized using the experimental thermodynamic and the phase equilibrium data from the literature. The solution phases of the system (liquid, bcc and fcc) are described with the substitutional solution model, and most borides are treated as stoichiometric phases or semistoichiometric phases, using a simple two-sublattice model for the latter. The system’s intermetallic phases, Chi, Mu, R, and Sigma (not dissolving boron) as well as boride M3B2, based on a formulation of (Cr,Fe)(Cr,Fe,Mo)2(B)2, are described with a three-sublattice model. Reasonable agreement is obtained between the calculated and measured phase equilibria in all four systems: B-Mo; ­Fe-B-Mo; B-Cr-Mo; and Fe-B-Cr-Mo.

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Authors and Affiliations

Jyrki Miettinen
Ville-Valtteri Visuri
Timo Fabritius

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