# Model¶

In this section the basic models have to be specified. I.e. each model contributes an equation or a set of equations to be solved.

### Type of coupling¶

If `concentration`

is selected, the phase-field will be coupled to concentration-fields, and solute partitioning and solute diffusion is simulated. This option is the most common for the analysis of alloys. If `temperature`

is selected instead, a temperature field will be coupled, and local latent heat release and heat transfer are calculated.

**Important:** `concentration`

coupling should not be applied for the simulation of pure metal solidification!

Example: Only phase-field model`... # Type of coupling? # Options: phase concentration [volume_change] temperature temp_cyl_coord # [stress{U|CE|MC}{1|2|3}] [flow] [flow_coarse] [dislocation] phase ...`

In addition to the basic coupling options, several optional parameters can be specified: The optional parameter `volume_change`

can only be used in combination with `concentration`

and allows considering the volume change due to phase-transformation or temperature change. In order to obtain a homogeneous expansion of the whole simulation domain, local volume changes are compensated by internal material transport which is assumed to be sufficiently fast that the system can always relax to a stress-free state.

Alternatively, the comprehensive calculation of an elastic stress field can be activated by one of the optional keywords starting with the string `stress`

, followed by the coupling type string `U`

, `CE`

, or `MC`

and the homogenisation model number (x=`1`

, `2`

, `3`

). All these 9 options require a license for the MICRESS® elastic module. In the uncoupled stress mode `stressUx`

no elastic contributions to the driving forces for phase transformation are calculated, and the solution of the mechanical problem is only required for the stress output. Using `stressCEx`

, elasto-chemical coupling is performed, and the elastic contributions are added to the driving force. Finally, mechano-chemical coupling (`stressMCx`

) includes the effects of composition on the eigenstrains, thus adding more complex interactions between stresses, diffusion and phase equilibria which can be important particularly in high alloyed multicomponent systems and close to spinoidal points. For homogenisation of stresses and strains inside the diffuse interface regions, three different models (x=`1`

, `2`

, `3`

) are available: Voigt-Taylor (`1`

), Khachaturyan(`2`

) and Reuss-Sachs. Please note that the standard keywords `stress`

and `stress_coupled`

used in former versions of MICRESS are still supported and are equivalent to `stressU2`

and `stressCE2`

. It should also be noted that the choice of stress options will significantly increase calculation time and should not be specified if not really needed. Especially, the options with chemo-elastic (`CE`

) or mechanochemical (`MC`

) coupling are very time-consuming, because they require a stress calculation in every numerical time step.

The `dislocation`

parameter activates an alternative recrystallization (RX) model based on a local dislocation density field. The dislocation field, which may for example stem from a Crystal Plasticity-Finite Element analysis (CP-FEM), can be read from a specific VTK file.

For `phase`

or `concentration`

simulations the optional `flow`

or `flow_coarse`

parameter can be given to enable the flow module, which allows simulation of fluid flow for phase 0. For the `flow_coarse`

option an additional coarsening factor must be provided. An in depth description of the flow module and its usage is found under the flow solver topic.

Example: Enabling flow on a coarse grid`... # Model # ===== # Type of coupling? # Options: phase concentration [volume_change] temperature temp_cyl_coord # [stress{U|CE|MC}{1|2|3}] [flow] [flow_coarse] [dislocation] concentration flow_coarse # Grid coarsening factor ? (integer,even) 2 ...`

### Thermal Conditions¶

Latent heat describes the amount of energy released or absorbed during phase transitions. The latent heat option should be applied to phase transformation processes where latent heat is dominating the temperature trend. With this option, latent heat is released averaged over the calculation domain. This is ideally the case for small samples where temperature gradients are negligible (DTA approximation). MICRESS® also allows the use of latent heat in connection with thermal gradients, but in such cases rather the use of the `1d_temp`

option is recommended.

In this input section, latent heat can be switched on or off by choosing one of the keywords `no_lat_heat`

, `lat_heat`

and `no_lat_heat_dsc`

. Alternatively, the `1d_temp`

option can be selected. If latent heat is used, the enthalpy of each phase (including the phase 0) as well as its specific thermal capacity need to be specified when giving the phase properties (see Phases). It has further implications for the definition of the Boundary Conditions, Process Conditions, and Numerical Parameters.

If latent heat is included in the simulation, an extra output file with extension **dTLat** is written which contains the amounts of latent heat, enthalpy data etc.

If `no_lat_heat`

is specified, no latent heat is taken into account. Instead, the temperature trend must be specified explicitly in section Process Conditions. `no_lat_heat_dsc`

is identical to `no_lat_heat`

, but triggers the output of latent heat data (enthalpies, specific heat, heat flow) in the **dTLat** file. This permits conduction of virtual DSC experiments displaying the heat flow for a specified temperature-time curve.

`1d_temp`

¶

If concentration coupling is activated, an explicit 1D temperature field in z-direction can optionally be defined by the keyword `1d_temp`

. This field can be used as an improved thermal boundary condition for the microsimulation domain and thus replaces the normal definition of thermal boundary conditions (see section Process Conditions. With the 1D temperature field, heat flow and release of latent heat are solved explicitly. For numerical reasons, temperature in the 1D temperature field is calculated using a direct explicit solver with a default kinetic coefficient (Boettger J. Comput Phys 2009). The default value is preconfigured for typical casting processes and needs not to be changed in most cases. A different value can given as optional parameter.

The temperature field will be evaluated in a linear (`cartesian`

), cylindrical (`cylindrical`

), or polar (`polar`

) coordinate system. All of these options require further inputs for the field size (number of cells) and the field resolution (cell width in micrometer) as well as further input of thermal diffusivities (see process conditions: Thermo-physical properties for 1D temperature solver) and boundary conditions. The total size of the temperature field must be equal or larger than the height of the microstructure simulation domain (in z-direction). As temperature is solved explicitly in the 1D temperature field, the effects of latent heat are included automatically. Next, the user has to specify the relative position of the bottom of the 1d-temperature field relative to the bottom of the microstructure domain. The 1d-temperature field must be positioned such that the 2D/3D simulation domain is located completely inside this field.

**Important:** the initial position of the bottom of the 1d temperature field is always negative with respect to the micro-domain.

Example: Type of coupling: concentration with 1D_temp_field`... # Model # ===== # Type of coupling? # Options: phase concentration [volume_change] temperature temp_cyl_coord # [stress] [stress_coupled] [flow] [flow_coarse] [dislocation] concentration # Thermal Conditions # Options: no_lat_heat no_lat_heat_dsc lat_heat 1d_temp [kin. Coeff.] # kin. Coeff: Kinetics of latent heat release (default is 0.01) 1d_temp # Kind of coordinate system for the 1D temperature field? # Options: cartesian cylindrical polar cartesian # Number of cells for 1D temperature field? 500 # Cell dimension (in micrometer) for 1D temperature field ? 100.00 # Initial position (in micrometer) of the 1D temperature field ? # (distance between bottom of 1D temp field and bottom (Z-direction) of simulation area, <0!) -500.00 ...`

### Assumption for elastic 2D model¶

If one of the 9 options for stress coupling has been chosen, and the dimensionality of the simulation is 2D, additional input for the 2D-abstraction of the stress/strain is required. With the `plain_stress`

approximation, stresses in the third dimension (y-direction) are assumed to be constant inside the 2D-plane. This is typically the case in thin plates. However, in MICRESS® the typical 2D-assumption is that we consider a plane inside a (infinitely) thick sample. Then, the `plane_strain`

approximation, which assumes the strains in y-direction to be constant, is more realistic.

Example: Concentration and stress coupling`... # Model # ===== # Type of coupling? # Options: phase concentration [volume_change] temperature temp_cyl_coord # [stress{U|CE|MC}{1|2|3}] [flow] [flow_coarse] [dislocation] concentration stressCE2 # Thermal Conditions # Options: no_lat_heat no_lat_heat_dsc lat_heat 1d_temp [kin. Coeff.] # kin. Coeff: Kinetics of latent heat release (default is 0.01) no_lat_heat # Assumption for elastic 2D model # Options: plane_stress plane_strain plane_strain ...`