MICRESS® Downloads

MICRESS® examples

This site comprises results of MICRESS® simulations being performed on various topics. The respective results can be viewed and explored by downloading and using the free visualisation tool Display_MICRESS. The individual examples are stored as .zip archives and comprise a variety of topics.


Version 7.3

Example Description
Training
T00_01_BinaryGlobulitic_E_2D_Lin Globulitic growth of a single solid phase from the liquid of a binary alloy
Intended to be used as template. All material-specific input is specified as order-of-magnitude estimate.
T00_02_Binary_E_Globulitic_2D_TQ Primary globulitic growth and final eutectic solidification in a binary alloy with initially hypoeutectic concentration.
Material specific input is specified as order-of-magnitude estimate.
T00_03_Binary_E_HypoEutectic_2D_Lin Primary globulitic growth and final eutectic solidification in a binary alloy with eutectic phase diagram and initially hypoeutectic concentration.
SOLID_1 is modelled to nucleated on interface of SOLID_2. Intended to be used as template. All material-specific input is specified as order-of-magnitude estimate.
T00_04_Binary_E_HypoEutecticEff_2D_Lin Primary globulitic growth and final eutectic solidification in a binary alloy with initially hypoeutectic concentration. The eutectic growth is modelled in a numerically diffuse way by using the 'unresolved' option for nucleation of the second solid phase.
Material specific input is specified as order-of-magnitude estimate.
T00_05_Binary_D_Eutectic_2D_Lin Directional eutectic growth of a binary alloy in temperature gradient
T01_01_AlCu_E_Dendritic_2D_Lin Primary dendritic growth of (Al)-fcc phase from Liquid in Al-3.at% Cu.
(2D, lin. phase-diagram, heat extraction, latent heat release)
T01_02_AlCu_E_Dendritic_2D_TQ Primary dendritic growth of (Al)-fcc phase from Liquid in Al-3.at% Cu.
(2D, TQ, heat extraction and latent heat release)
T01_03_AlCu_E_HypoEutectic_2D_TQ Primary dendritic growth of (Al)-fcc phase from Liquid in Al-3.at% Cu and subsequent eutectic growth of AlCu-theta phase.
Simulations ends when zero liquid fraction is reached.
(2D, TQ, heat extraction, latent heat release)
T01_04_AlCu_E_HypoEutecticEff_2D_TQ Primary dendritic growth of (Al)-fcc phase from Liquid in Al-3.at% Cu and subsequent unresolved eutectic growth of AlCu-theta phase.
Simulations ends when zero liquid fraction is reached.
(2D, TQ, heat extraction, latent heat release)
T01_05_AlCu_E_Temp1d_2D_TQ Primary dendritic growth of (Al)-fcc phase from Liquid in Al-3.at% Cu and subsequent unresolved eutectic growth of AlCu-theta phase.
Simulations ends when zero liquid fraction is reached.
(2D, TQ, Temp1d solver)
T01_06_AlCu_D_Dendrites_2D_Lin Directional growth of primary (Al)-fcc dendrites from Liquid in Al-3.at% Cu.
Selection of dendrites with orientation well aligned to the imposed gradient. (2D, lin. phase-diagram, temperature gradient, cooling rate)
T01_07_AlCu_D_Dendrites_2D_TQ Directional growth of primary (Al)-fcc dendrites from liquid in Al-3.at% Cu. Selection of dendrites with orientation well aligned to the imposed gradient.
(2D, lin. phase-diagram, temperature gradient, cooling rate)
T01_10_AlSi_E_HypoEutecticEff_2D_Lin Primary dendritic growth of (Al)-fcc phase from Liquid in Al-7.at% Si
Subsequent unresolved eutectic growth of Si-Diamond phase starts by heterogeneous nucleation in the melt (seed-density model). Simulations ends when zero liquid fraction is reached.
(2D, lin. phase-diagram, heat extraction, latent heat release)
T01_20_AlNi_D_DendriteTip_2D_Lin Isothermal free growth of primary (Al)-fcc dendrite from undercooled liquid in Al-3.5wt% Ni
The uniaxial simulation addresses the steady-state velocity and morphology of a single dendrite tip. Growth occurs under assumption of diffusion- control with huge interfacial mobility and zero kinetic ansiotropy.
(2D, lin. phase-diagram, undercooled melt)
T02_01_FeCMn_D_DeltaGamma_2D_TQ Directional growth of half a primary delta-ferrite dendrite from the liquid of hyopeutectic Fe-0.25 wt C - 1 wt% Mn
(2D, TQ, temperature gradient, cooling rate)
T02_20_FeCMn_E_GammaAlphaIsotherm_2D_Lin Alpha-Ferrite nucleates and grows from undercooled isothermal gamma-austenite grain structure in Fe-0.1 wt%C- 1wt% Mn
Mn is modelled with NPLE (non partitioning local equilibrium). Since no cooling is applied, the growth slows down with time and the structures ripen while fractions move symptotically towards a temporary partial-equilibrium (with Mn still non-partitioned, but contributing to local driving forces).
(2D, lin. phase-diagram, isothermal)
T02_21_FeCMn_E_GammaAlphaIsotherm_2D_TQ Alpha-Ferrite nucleates and grows from undercooled isothermal gamma-austenite grain structure in Fe - 0.1wt% C - 1.5wt% Mn.
Mn is modelled with NPLE (non partitioning local equilibrium). Since no cooling is applied, the growth slows down with time and the structures ripen while fractions move symptotically towards a temporary partial-equilibrium (with Mn still non-partitioned, but contributing to the local driving forces).
The simulation is identical to T02_20_FeCMn_E_GammaAlphaIsotherm_2D_Lin except for the fact that a thermo-dynamic database is used.
(2D, TQ, isothermal)
T02_22_FeCMn_E_GammaAlphaIsothermPara_2D_TQ Alpha-Ferrite nucleates and grows from undercooled isothermal gamma-austenite grain structure in Fe-0.1 wt%C- 1wt% Mn.
Mn is modelled with para-equilibrium conditions. Since no cooling is applied, the growth slows down with time and the structures ripen while fractions move symptotically towards a temporary partial-equilibrium (with Mn still non-partitioned).
The simulation is identical to T02_20_FeCMn_E_GammaAlphaIsotherm_2D_Lin except for the fact that Mn is here modelled with para-equilibrium conditions, causing higher driving forces and growth rates, as Mn partitioning has no growth-restrictinge effect, i.e. is not contributing to the driving force. A thermo-dynamic database is used.
(2D, TQ, isothermal)
T02_23_FeCMn_E_GammaAlphaIsothermParaTQ_2D_Lin Alpha-Ferrite nucleates and grows from undercooled isothermal gamma-austenite grain structure in Fe-0.1 wt%C- 1wt% Mn.
Mn is modelled with ParaTQ option. Since no cooling is applied, the growth slows down with time and the structures ripen while fractions move symptotically towards a temporary partial-equilibrium (with Mn still non-partitioned).
The simulation is identical to T02_20_FeCMn_E_Gamma_Alpha_Isotherm_Para_2D_TQ except for the fact that Mn is here modelled with ParaTQ option.
(2D, TQ, isothermal)
T02_24_FeCMn_E_GammaAlphaCementite_2D_TQ Alpha-ferrite nucleates and grows from gamma-austenite grain structure during cooling of Fe-0.25 wt%C- 0.174 wt% Mn. Towards the end of the transition cementite nucleates on alpha-gamma interfaces.
Note: The coupled eutectoid growth of cementide and ferrite (pearlite) cannot properly be resolved on this 2D scale. Instead, the pearlite may be modelled as diffuse 'unresolved' region, as demonstrated in example T02_26_FeCMn_E_GammaAlphaPearliteEff_2D_TQ under same conditions.
(2D, TQ, constant cooling rate)
T02_25_FeCMn_E_GammaAlphaCementite_2D_TQ+Lin Alpha-ferrite nucleates and grows from gamma-austenite grain structure during cooling of Fe-0.25 wt%C- 0.174 wt% Mn. Towards the end of the transition cementite nucleates on alpha-gamma interfaces.
In contrast to example T02_24_FeCMn_E_GammaAlphaCementite_2D_TQ, Cementite is here not taken from the database, but modelled user-defined with LinTQ.
Note: The coupled eutectoid growth of cementide and ferrite (pearlite) cannot properly be resolved on this 2D scale. Instead, the pearlite may be modelled as diffuse 'unresolved' region, as demonstrated in example T02_26_FeCMn_E_GammaAlphaPearliteEff_2D_TQ.
(2D, TQ, LinTQ, constant cooling rate)
T02_26_FeCMn_E_GammaAlphaPearliteEff_2D_TQ Alpha-ferrite nucleates and grows from gamma-austenite grain structure during cooling of Fe-0.25 wt%C- 0.174 wt% Mn. Towards the end of the transition cementite nucleates on alpha-gamma interfaces. (2D, TQ, constant cooling rate)
T02_27_FeCMn_E_GammaAlphaIsothermStress_2D_TQ Evaluation of stress distribution during Alpha-Ferrite nucleation and growth from undercooled isothermal gamma-austenite grain structure in Fe - 0.1wt% C - 1.5wt% Mn
T02_30_FeC_E_GammaAlphaAcicularA_2D_Lin Alpha-ferrite nucleates with special-orientation relationship to gamma-austenite parent grains in Fe-0.1 wt%C rows and then grows with strong anisotropy.
The example does not address a specific application, but shall illustrate different ways how to use crystallographic symmetry, special orientation relationship and anisotropy.
(2D, lin. phase-diagram, constant cooling)
T02_31_FeC_E_GammaAlphaAcicularB_2D_Lin Alpha-ferrite nucleates with special-orientation relationship to gamma-austenite parent grains in Fe-0.1 wt%C rows and then grows with strong anisotropy.
The example does not address a specific application, but shall illustrate different ways how to use crystallographic symmetry, special orientation relationship and anisotropy.
(2D, lin. phase-diagram, isothermal)
T02_50_FeCMnPSi_PhosphorPeak_1D_TQ
T02_51_FeCMnPSi_PhosphorPeak_2D_TQ
T02_60_FeCSi_E_CastIronNodule_3D_TQ
  • Slightly hyper-eutectic FeCSi-alloy
  • Graphite nucleates in the center of the domain
  • Nodular growth is modelled by 25 facets
  • Eutectic austenite nucleates on graphite
  • Volumetric expansion model is used with both linearized molar volumes and molar volumes from database.
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
T02_61_FeCSi_E_CastIronDendriteNodules_3D_TQ
  • Slightly hypo-eutectic FeCSi-alloy
  • Austenite dendrite nulceates in a corner of the domain
  • Graphite nucleates on distributed seeds
  • Nodular growth is modelled by 25 facets
  • Eutectic austenite nucleates on graphite
  • Volume_change option is used with molar volumes from database
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
Note: Example domain size has been reduced for sake of simulation time
T02_63_FeCSi_E_CastIronHeatDiffusion_3D_TQ
  • Slightly hypo-eutectic FeCSi-alloy
  • Austenite dendrite nulceates in a corner of the domain
  • Graphite nucleates on distributed seeds
  • Nodular growth is modelled by 25 facets
  • Eutectic austenite nucleates on graphite
  • Volume_change option is used with molar volumes from database
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
  • Temperature is calculated using the 'heat_diffusion' model'
    • Heat diffusibility of the mold: 0.064 J/(K*cm2*s0.5)
    • Casting modulus = volume/surface = 1.2 cm
Note: Example domain size has been reduced for sake of simulation time
T02_64_FeCSi_E_CastIronNodule_2D
  • Slightly hyper-eutectic FeCSi-alloy
  • Graphite nucleates in the center of the domain.
  • Nodular growth is modelled by 6 facets
  • Eutectic austenite nucleates on graphite
  • Eutectoid ferrite nucleates on interface of graphite and austenite
  • Volumetric expansion model is used with both linearized molar volumes and molar volumes from database.
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
  • Temperature is calculated using the 'heat_diffusion' model'
    • Heat diffusibility of the mold: 0.728 J/(K*cm2*s0.5)
    • Casting modulus = volume/surface = 1.1 cm
T02_65_FeCSi_E_CastIronDendriteNodules_2D_TQ
  • Slightly hypo-eutectic FeCSi-alloy
  • Austenite dendrite nulceates in a corner of the domain
  • Graphite nucleates on distributed seeds
  • Nodular growth is modelled by 6 facets
  • Eutectic austenite nucleates on graphite
  • Eutectoid ferrite nucleates on interface of graphite and austenite
  • Volume_change option is used with molar volumes from database
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
  • Temperature is calculated using the 'heat_diffusion' model'
    • Heat diffusibility of the mold: 0.728 J/(K*cm2*s0.5)
    • Casting modulus = volume/surface = 1.1 cm
    • Note: Example domain size has been reduced for sake of simulation time
T03_01_MgAl6_D_Dendritic_2D_Lin
  • Directional growth of Mg-HCP phase from liquid in Mg-6 wt% Al
  • 2D simulation domain, moving-frame, 1D-far_field
  • Solidification of HCP phase in the direction of temperature gradient
T03_02_MgAl6_D_Dendritic_2D_TQ
  • ...
  • Use of a thermo-dynamic database
T03_03_MgAl6_E_Dendritic_2D_Lin
  • Equi-axed solidification of Mg-HCP phase from liquid in Mg-6 wt% Al
  • 2D simulation domain
  • Equi-axed solidification of HCP phase in the domain
  • Random nucleation of Mg-HCP phases
T03_04_MgAl6_E_Dendritic_2D_TQ
  • ...
  • Latent heat release
  • Use of a thermo-dynamic database
T03_05_MgAl6_Anisotropy_HCP_3D_TQ
  • Equi-axed solidification of Mg-HCP phase from liquid in Mg-6 wt% Al
  • 3D simulation domain
  • Equi-axed Solidification of HCP phase in the domain
  • One nuclei at the center of the domain
  • Anisotopy of Mg-HCP phase in 3D
T10_01_GrainGrowth_2D Normal grain growth
(2D, no misorientation)
T10_02_GrainGrowthMisorientation_2D Normal grain growth
(2D, misorientation)
T10_03_GrainGrowth_3D Ideal isothermal 3D grain growth (starting from 400 grains)
T10_04_GrainGrowthMisorientation_3D Anistropic isothermal 3D grain growth (200 grains)
T10_05_SubGrainGrowth_2D Evolution of two grains with different density of subgrains considering misorientation.
(2D)
T10_11_GrainGrowthInitialFromFile_2D 2D grain growth starting with initial structure read from file
T10_20_GrainGrowthTempProfiles_2D 2D grain growth starting with vertical temperature profiles and temperature dependent mobility data read from file.
T10_30_GrainGrowthPinning_2D 2D grain growth with particle pinning starting with an initial structure read from file
T10_40_GrainGrowthSoluteDrag_2D 2D grain growth with "solute_drag" option and initial structure read from file
T10_41_GrainGrowthDGDependentMobility_2D 2D grain growth with "dg_dependent" option for mobility and initial structure read from file
T11_01_ReXDeterministic
T11_02_ReXRandom
T11_03_ReXLocalHumphreys Requires revision!
T11_04_ReXLocalRecovery Requires revision!
T11_05_ReXMeanDislocation Requires revision!
T20_01_Stress_2D
T30_01_FlowCylinderLaminar
T40_01_Temperature_2D Heat diffusion
T50_01_Growth5GrainsDifferentSizes Evolution of grains with different curvature at constant undercooling
Grains with undercritical radius will shrink, those with overcritical radius will grow.
(2D, no concentration coupling)
T50_10_GrowthFiniteMobilityATCMobCorr_1D_Lin
T50_11_GrowthFiniteMobilityNoATCMobCorr_1D_Lin
T51_01_AnisotropyFacettedGrain Uncoupled growth of single facetted grain
This example can be used to test different combinations of facet vector.
T51_02_AnisotropyFacettedGrains Uncoupled growth of 5 facetted grains with different grain orientation
This example can be used to test different combinations of facet vector and their numerical resolution.
T51_03_AnisotropyDendriteCubic_2D_Lin Diffusion controlled growth of dendrite with cubic anisotropy in 2D taking advantage of the crystallographic symmetry (1/4 dendrite)
T51_10_NucleationSeedDensityLogN1 Nucleation-model: seed density with logNormal1 option.
T51_11_NucleationSeedDensityLogN2 Nucleation-model: seed density with logNormal2 option.
T51_12_NucleationSeedDensityClass Nucleation-model: seed density by given seed density classes
Benchmark
B001_1D_ConstantDrivingForce 1D solid/liquid front with constant velocity
B002_1D_ConstantDrivingForce_MovingFrame 1D solid/liquid front with constant velocity
global CO-system moves controlled by constant distance of the solid phase to the top
(moving frame)
B003_1Grain_GrowthFromLiquid 2D circular grain of phase 1 growing from liquid (isothermal with constant undercooling of 1 K)
B004_1Grain_GrowthFromLiquid_ZeroInitialSize An initial solid grain of zero size is located in the center of the domain. The initial growth from the liquid is then modelled using the analytical_curvature model.
B005_1Grain_RoundInverse
B006_1Grain_Shrinking_3D Single spherical grain shrinking due to curvature, no thermodynamic driving force.
B007_1Grain_Shrinking Single grain shrinking due to curvature (2D), no thermodynamic driving force.
B008_1Grain_Solidification_FiniteInitialSize
B009_2Phases_1Grain
B010_2Phases_DirectionalShrinking
B011_2Phases_DirectionalShrinking_MovingFrame Directional motion simply driven by curvature, i.e. no thermodynamic driving force applied.
B012_2Phases_DirectionalShrinking_Triple
B013_Liq+2Phases_Triple_Inert Only interaction between liquid and phase 1.
The interface between phase 1 and phase 2 should remain straight without any impact of the triple junction.
B014_Liq+2Phases_Triple_Inert_Wetting No Interaction between liquid and phase 2.
However, the interfacial energy between liquid and phase 2 is smaller than the interfacial energy between phase 1 and phase 2, which leads to wetting of phase 1 on phase 2.
B015_3Phases_Triple Interaction defined between three phases, but
- mobility between phase 1 and phase 3 equals zero
- mobility between phase 2 and phase 3 equals zero
Only phase 2 is growing from phase 1 due to a constant undercooling. The interface between phase 1 and phase 2 should remain planar without any impact of the triple junction.
B016_diffusion_control 1D Interface motion controlled by diffusion in liquid.
Isothermal Simulation with comoving frame, no gradient.
B017_Flow_Cylinder_Karman
B018_1D_Zener_Diffusion_Control 1D Interface motion controlled by diffusion in liquid.
Validation by comparison to precise analytical solution from Zener.
Application
A001_Delta_Gamma Directional growth of half a primary delta-ferrite dendrite from the liquid of hyopeutectic Fe-0.25 wt% C - 1 wt% Mn
A002_AlCu_Temp1d Equiaxed solidification of multiple Al-Cu grains
A003_CastIronDendriteNodules
  • Slightly hypoeutectic FeCSi-alloy
  • Austenite dendrite nucleates in a corner of the domain
  • Graphite nucleates on distributed seeds
  • Nodular growth is modelled by 25 facets
  • Eutectic austenite nucleates on graphite
  • Volume_change option is used with molar volumes from database
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
  • Temperature is calculated using the 'heat_diffusion' model'
  • Additional elements can easily be added.
(3D, isolated, symmetric, TQ, Fe-C-Si, ternary, cast iron, hypereutectic, volume_change, interstitial, out_expansion, out_molar_volume, out_moles, tab_volume, seed_density, interface nucleation, harmonic_expansion, faceted, mob_corr, mobility_correction, lat_heat, heat_diffusion)
A004_Gamma_Alpha_TQ Alpha-Ferrite nucleates and grows from undercooled isothermal gamma-austenite grain structure in Fe - 0.1wt% C - 1.5wt% Mn.
Mn is modelled with NPLE (non partitioning local equilibrium). Since no cooling is applied, the growth slows down with time and the structures ripen while fractions move symptotically towards a temporary partial-equilibrium (with Mn still non-partitioned, but contributing to the local driving forces).
(2D, TQ, isothermal, Fe, C, Mn)
A005_Grain_Growth_Misorientation_3D Isothermal anisotropic grain growth with misorientation conditions, Random voronoi structure with 172 grains, periodic boundary conditions (read_shockley, humphreys, special_orient)
A006_CMSX4 (database, TQ, 2D, NI, CR, CO, MO, W, TA, AL, TI, RE, HF) reviewed!
A007_Dendrite_AlSi_3D Equiaxed 3D Dendrite AlSi7 at 0.3 K/s cooling rate
(Al, Si, 3D)
A008_Dendrite_AlSi_3D_flow Equiaxed 3D Dendrite AlSi7 at 0.1 K/s cooling rate in forced melt flow at 1 mm/s
(Al, Si, flow, 3D)
A009_Flow_Permeability (flow, 3D)
A011_Flow_Readfrac (3D, flow)
A013_GammaAlphaPearlite_TQ
  • Hypo-eutectoid FeCMn-alloy
  • Ferrite nucleates at austenitic grain boundaries. System is cooled down with constant heat extraction rate while latent heat is released.
  • Mn is not partitioning at austenite/ferrite interface (option: 'nple').
  • Cementite grows in eutectoid transformation together with ferrite thus forming pearlite. Pearlite is modelled as an effective phase, by defining nucleation of cementite with option 'unresolved'. Note that the effective pearlite phase is represented in the output files *phas, *korn and *orie by a checkerboard pattern. The effective fraction is given out as additional column in *TabF.
(2D, periodic, TQ, database, Fe, C, Mn, ternary, pearlite, analytical_curvature, unresolved, mob_corr, mobility_correction, nple, latent_heat)
A014_CMSX4_Rafting 6h Ripening + 10 h rafting of gammaprime in CMSX4
(Size and rafting period can be deliberately extended.)
(3D, TQ, database, NI, CR, CO, MO, W, TA, AL, TI, RE, HF)
A015_AlSiMg_Unresolved (2D, TQ, database, Al, Si, Mg, unresolved)
A016_NiAlMo_Cubic_Precipitate_3D (3D, TQ, database, Al, Mo, Ni)
A017_M247_Additive_constGV An already liquid layer of CM247LC powder (30 microns thick) is solidified under constant thermal gradient and cooling rate. The substrate consists of two initial flat grains with different orientation, leading to cellular-dendritic growth and formation of a grain boundary. As interdendritic phases gammaprime (FCC_L12#2) and MC (FCC_L12#3) are considered.
Diffusion coefficients in the melt are taken from database (MOBNI5) and averaged over 10 equi-distant segments in z-direction. For simplicity, only effective diagonal terms are obtained by taking the dilute limit for each element ("diagonal_dilute").
Rest liquid pockets are removed using the "split_from_grain" function by converting to gamma-prime phase when the local temperature falls below 1100 grade Celsius. The simulation automatically ends when liquid has completely vanished ("end_at_fraction").
The growth kinetics of the primary phase has been calibrated against a higher-resolution simulation.
(2D, isolated, periodic, additive, SLM, L-PBF, TQ, database, M247, CM247LC, superalloy, ni-base, NI, C, CR, CO, MO, W, TI, AL, TA, HF, dendritic, cellular, interface nucleation, split_from_grain, mob_corr, mobility correction, end_at_fraction, tic_lin_seg, diff_comp_sets, vol_comp_sets, penalty, ordered, temp_limit_TQ, grain selection, gamma prime)
A018_Al4Cu_Additive_Rosenthal An solid homogeneous layer of Al4Cu (as single fcc-phase, virtually representing the base metal plus powder layer) is heated from the top assuming thermal conditions of an (arbitrary) heat source ("Rosenthal solution"), which is applied in form of time-dependent temperature profiles (A018_Rosenthal.txt). This solid layer, which is represented by the simulation domain, is partially molten and then re-solidified. As interdendritic phase theta phase (AL2CU_C16) is forming during the solidification stage. Formation of new fcc-grains is considered only by fragmentation during melting.
(2D, isolated, periodic, TQ, database, Aluminium, Al, Cu, dendritic, interface, nucleation, split_from_grain, mob_corr, mobility correction, profiles_from_file, temperature, end_at_temperature, tic_tq_segments, diff_comp_sets, temp_limit_TQ, penalty, ordered, temp_limit_TQ)
A019_01_MgAl6_D_Dendritic_3D_Lin Directional solidification of Mg-HCP phase from liquid in Mg-6 wt% Al
  • 3D simulation domain
  • 80 nuclei in XY plane
  • Directional solidification of HCP phase in the diection of temperature gradient(Z-axis)
  • Random nucleation of Mg-HCP phases
  • Temperature gradient 150 K/cm and cooling rate -1 K/S
A019_02_MgAl6_E_Dendritic_3D_TQ Equi-axed solidification of Mg-HCP phase from liquid in Mg-6 wt% Al
  • 3D simulation domain
  • Equi-axed Solidification of HCP phase in the domain
  • Random distribution of nuclei in the domain
A020_CastIronDendriteNodulesBCC_3D_TQ
  • Slightly hypo-eutectic FeCSi-alloy
  • Austenite dendrite nulceates in a corner of the domain
  • Graphite nucleates on distributed seeds
  • Nodular growth is modelled by 25 facets
  • Eutectic austenite nucleates on graphite
  • Eutectoid ferrite nucleates on interface of graphite and austenite
  • Volume_change option is used with molar volumes from database
  • Diffusion of carbon in Austenite is modelled as 'interstitial'
  • Temperature is calculated using the 'heat_diffusion' model'
    • Heat diffusibility of the mold: 0.728 J/(K*cm2*s0.5)
    • Casting modulus = volume/surface = 1.1 cm