Part I. Thermodynamic and Kinetic Aspects of the Hot Dip (Zn) - Coating Formation

Wołczyński, W.; Pogoda, Zdzisław; Garzeł, G.; Kucharska, Barbara; Sypień, Anna; Okane, Toshimitsu

doi:10.2478/amm-2014-0212

Cited by 13 publications

(11 citation statements)

References 15 publications

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“…For a quasi-binary section made of altogether k components between alloys A a1 B b1 C c1 …Z z1 and A a2 B b2 C c2 …Zz2, altogether (k-1) materials balance equations of type (1) can be written between component A and between all other components, with the numerical coefficients to be calculated using Eq-s (5a-c). However, in fact the number of above equations can be reduced by one further equation, as Calphad codes such as ThermoCalc has the following built-in material balance equation: (6) where I = A, B, C, …. Z.…”

Section: Derivation Of the General Equationsmentioning

confidence: 99%

“…The majority of materials balance equations are built within the commercial Calphad codes [9][10][11][12][13][14][15]. However, when quasi-binary sections of ternary or multi-component phase diagrams are of interest [1][2][3][4][5][6][16][17][18][19][20], the user of those codes should create the appropriate materials balance equations. This is usually done in the following format (as in Thermo-Calc): (1) where I and J present two, arbitrary components in the multi-component system, w I and w J (dimensionless) are the mass fractions or mole fractions or volume fractions of the components, while the Greek letters denote numerical constants.…”

Section: Introductionmentioning

confidence: 99%

“…Ternary and multi-component phase diagrams are important tools in metallurgy and materials science [1][2][3][4][5][6]. They are usually calculated by a Calphad (Calculation of Phase Diagrams) algorithm [7][8].…”

Section: Introductionmentioning

confidence: 99%

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On the General Material Balance Equation(S) to Calculate Quasi-Binary Sections of Multi-Component Phase Diagrams

Dezső¹,

Kaptay²

2016

Archives of Metallurgy and Materials

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Highlights• To calculate quasi-binary sections of multicomponent phase diagrams, special materials balance equations are needed• The general equations to calculate the numerical constants of those equations are derived here• For a k-component system, (k-2) such independent equations are needed. IntroductionTernary and multi-component phase diagrams are important tools in metallurgy and materials science [1][2][3][4][5][6]. They are usually calculated by a Calphad (Calculation of Phase Diagrams) algorithm [7][8]. Material balance equations are vital parts of this Calphad algorithm. The majority of materials balance equations are built within the commercial Calphad codes [9][10][11][12][13][14][15]. However, when quasi-binary sections of ternary or multi-component phase diagrams are of interest [1][2][3][4][5][6][16][17][18][19][20], the user of those codes should create the appropriate materials balance equations. This is usually done in the following format (as in Thermo-Calc):( 1) where I and J present two, arbitrary components in the multi-component system, w I and w J (dimensionless) are the mass fractions or mole fractions or volume fractions of the components, while the Greek letters denote numerical constants. The goal of this paper is to work out simple equations for numerical constants in Eq.(1), being valid for any quasibinary section of any multi-component system. Derivation of the general equationsLet us consider a multi-component system made of A-B-C-….-Z components (generally denoted as I or J). We are interested in one of its quasi-binary sections, having a horizontal concentration axis and a vertical temperature axis, with constant value of pressure. The quasi-binary section connects two alloys with each other: alloy 1 is denoted as A a1 B b1 C c1 …Z z1 , while alloy 2 is denoted as A a2 B b2 C c2 …Z z2 , where a1, b1, c1, …., z1 (generally i1, and j1) and a2, b2, c2,…., z2 (generally i2 and j2) are positive numbers defined between 0 and 1. They can be mass fractions or mole fractions or volume fractions of the components in two alloys. The materials balance requires:It is important to underline that wI and wJ in Eq.(1) and all parameters in Eq-s (2a-b) must have the same definition: they all should be mass fractions, or they all should be mole fractions or they all should be volume fractions.The x-axis of the quasi-binary diagram connects alloy 1 with alloy 2, with fraction x increasing from the value equal to 0 (for alloy 1) to the value equal to 1 (for alloy 2). Then, the component fractions for two arbitrary components I and J can be written as:Arch. Metall. Mater., Vol. 61 (2016) A general form of material balance equations to be used to calculate quasi-binary sections of multi-component phase diagrams is derived here. When this general equation is reduced to ternary systems, it coincides with those, given in the Thermo-Calc manual. For a k-component system, altogether only (k-2) such independent equations should be written from the list of k(k-1)/2 possible equations.

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Section: Derivation Of the General Equationsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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On the General Material Balance Equation(S) to Calculate Quasi-Binary Sections of Multi-Component Phase Diagrams

Dezső¹,

Kaptay²

2016

Archives of Metallurgy and Materials

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“…Additionally, because of the high value of the undercooling ΔT, it has been assumed that the isothermal crystallization of individual intermetallic phases is proceeding in a dynamic mode [1][2][3][4][5][6][7][8][9][10][11][12]. An important factor that affects the growth of the protective layer is flux [4].…”

Section: Introductionmentioning

confidence: 99%

Shaping optimal zinc coating on the surface of high-quality ductile iron casting. Part II – Technological formula and value of diffusion coefficient

Kopyciński¹,

Guzik²,

Szczęsny³

2017

Archives of Metallurgy and Materials

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The completed research presented in the first part of the article has allowed linking the manufacturing technology of ductile iron castings with the process of hot dip galvanizing. On the basis of these data simulations were carried out to examine the behaviour of zinc diffusion coefficient D in the galvanized coating. The adopted model of zinc coating growth helped to explain the cases of excessive growth of the intermetallic phases in this type of coating. The paper analyzes covered the relationship between the roughness and phase composition of the top layer of product and the thickness and kinetics of zinc coating growth referred to individual sub-layers of the intermetallic phases.Roughness and phase composition in the surface layer of product were next related to the diffusion coefficient D examined in respective sublayers of the intermetallic phases.

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“…In general, the technology of bimetal casting consisting of working surface layer and a base part is achieved based on two systems, i.e. liquid-liquid [1,2] and liquid-solid [3,4].…”

Section: Introductionmentioning

confidence: 99%

Gravity Sand Casting of Metallurgical Bonded Bimetallic Grinding Roll Made of White Cast Iron-Nodular Cast Iron

Purwadi¹

2017

IJERA

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Bimetallic castings are widely used in the mining industries as construction material for crushers which have to perform high abrasive resistance at the outer side and excellent machinability at the inner side. To manufacture bimetallic casting goods cconsecutive centrifugal and gravity casting methods are commonly applied. Centrifugal and consecutive casting come up with geometrical constraints at the parting line of both materials. This research dealed with the manufacturing of tapered grinding roll by applying gravity casting method. The possibilities of casting the white cast iron outer ring in the preheated ductile cast iron of the inner ring were investigated. The inner ring was first heated up by casting liquid metal around the inner side, which prevented the inner ring from cracking due to rapid expansion during the casting process and to provide adequyate shrinkage of inner ring during solidification. After achieving the desired temperature of the inner ring, the liquid metal of white cast iron was then poured into the cavity to form the outer ring. The preheating temperature of the inner ring was mainly derived from the linear thermal expansion of both quasi isotrophic material and the diffusion at the parting line. This preheating temperature has to facilitate the formation of metallurgical bonding and avoid cracks due to the difference of shrinkage value between inner and outer ring. The preheating temperature was set up in the range of 500°C -1000 °C and the flushing time was fixed for 7 seconds. Studies on the microstructure of sample material have revealed a formation of metallurgical bonding at all of the preheating temperature. The width of the diffusion at the interface area varied between 291 µm at 500 o C preheating temperature, 301 µm at 625 o C, 834,8 µm at 750 °C, 909,1 µm at 875 °C and 1027,7 µm at 1000 °C. By preheating temperature of higher than 750°C fusion occured at the interface area between inner and outer material. This research concludes that the casting of bimetallic by applying gravity casting method can be done by preheating the inner ring to 625 o C, interface temperature of 1150 o C, flushing time of 7 seconds and pouring the white cast iron outer ring at the temperature of 1430 o C

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Part I. Thermodynamic and Kinetic Aspects of the Hot Dip (Zn) - Coating Formation

Cited by 13 publications

References 15 publications

On the General Material Balance Equation(S) to Calculate Quasi-Binary Sections of Multi-Component Phase Diagrams

On the General Material Balance Equation(S) to Calculate Quasi-Binary Sections of Multi-Component Phase Diagrams

Shaping optimal zinc coating on the surface of high-quality ductile iron casting. Part II – Technological formula and value of diffusion coefficient

Gravity Sand Casting of Metallurgical Bonded Bimetallic Grinding Roll Made of White Cast Iron-Nodular Cast Iron

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