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DAMASK_EICMD/code/config/material.config

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overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
#####################
added version information to all files do NOT edit text like this: $Id: constitutive_phenopowerlaw.f90 406 2009-08-31 14:13:10Z MPIE\f.roters $
2009-08-31 20:39:15 +05:30
# $Id$
#####################
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
<homogenization>
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
[SX]
Taylor homogenization is now called isostrain, changed material.config accordingly. corrected error message in case of unknown homogenization
2009-06-08 18:58:00 +05:30
type isostrain
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
Ngrains 1
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
[Grain_Cluster]
type RGC
ngrains 8
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
clustersize 2 2 2 # product of these numbers must be equal to ngrains(!)
clusterorientation 0.0 0.0 0.0 # orientation of cluster in terms of 313 Euler-angles in degree (random if not present)
# clusterorientation 0.0 26.57 0.0 # [012]
# clusterorientation 0.0 45.00 0.0 # [011]
# clusterorientation 0.0 26.57 24.10 # [112]
# clusterorientation 0.0 45.00 19.47 # [122]
# clusterorientation 0.0 45.00 35.26 # [111]
grainsize 4.0e-6 4.0e-6 2.0e-6 # in [m]
overproportionality 2.0e+0 # typical range between 0.001 to 1000
scalingparameter 1.0e+1 # typical range between 0.001 to 1000
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
(output) constitutivework
(output) magnitudemismatch
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
(output) penaltyenergy
Additional feature to the RGC scheme: The volumetric consistency constraint. This is implemented by penalizing any volumetric discrepancy which occurs due to severe relaxation. The penalty for volume inconsistency is described using a power-law model. The setting for this function can be done in the numerics.config via three new parameters, i.e., maxvoldiscrepancy_RGC, voldiscrepancymod_RGC and discrepancypower_RGC. For monintoring, an extra output variable in prescribed in the material.config in the RGC section, namely "(output) volumediscrepancy". IO.f90 and numerics.f90 has been modified accordingly to accommodate these changes
2009-12-16 21:50:53 +05:30
(output) volumediscrepancy
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
(output) averagerelaxrate
(output) maximumrelaxrate
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
[Taylor2]
type isostrain
Ngrains 2
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
<microstructure>
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
choose textures and phases of example materials according to what the labels suggest
2012-02-21 18:46:59 +05:30
[Aluminum_j2]
crystallite 2
(constituent) phase 1 texture 2 fraction 1.0
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
choose textures and phases of example materials according to what the labels suggest
2012-02-21 18:46:59 +05:30
[Aluminum_pheno_Poly]
/elementhomogeneous/ # put this flag to set ips identical in one element (something like reduced integration)
crystallite 2
(constituent) phase 2 texture 2 fraction 1.0
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
choose textures and phases of example materials according to what the labels suggest
2012-02-21 18:46:59 +05:30
[Aluminum_nonlocal_001]
crystallite 2
(constituent) phase 3 texture 3 fraction 1.0
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
[DP_Steel]
introduction of a possibility to have homogeneous element (all ips in one element are identical, sort of reduced integration) and bugs-fixing in crystallite.f90, homogenization_RGC.f90, numerics.f90.
2009-11-24 20:30:25 +05:30
/elementhomogeneous/
choose textures and phases of example materials according to what the labels suggest
2012-02-21 18:46:59 +05:30
crystallite 2
(constituent) phase 4 texture 1 fraction 0.82
(constituent) phase 5 texture 1 fraction 0.18
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
<crystallite>
#-------------------#
added two more <crystallite> examples
2011-05-13 22:24:08 +05:30
[none]
[aLittleSomething]
(output) f
(output) p
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
[all]
(output) phase
added <crystallite> output "texture" to list of examples
2011-04-12 21:03:29 +05:30
(output) texture
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
(output) volume
added <crystallite> output "texture" to list of examples
2011-04-12 21:03:29 +05:30
(output) orientation # quaternion
(output) eulerangles # orientation as Bunge triple
added some output variables in crystallite: F, Fe, Fp, Ee, P, S
2010-05-18 13:27:13 +05:30
(output) grainrotation # deviation from initial orientation as axis (1-3) and angle in degree (4)
(output) f # deformation gradient tensor; synonyms: "defgrad"
(output) fe # elastic deformation gradient tensor
(output) fp # plastic deformation gradient tensor
added total Green-Lagrange strain to crystallite outputs
2012-01-20 15:55:35 +05:30
(output) e # total strain as Green-Lagrange tensor
added some output variables in crystallite: F, Fe, Fp, Ee, P, S
2010-05-18 13:27:13 +05:30
(output) ee # elastic strain as Green-Lagrange tensor
(output) p # first Piola-Kichhoff stress tensor; synonyms: "firstpiola", "1stpiola"
(output) s # second Piola-Kichhoff stress tensor; synonyms: "tstar", "secondpiola", "2ndpiola"
added "Lp" as crystallite output
2011-02-25 13:45:26 +05:30
(output) lp # plastic velocity gradient tensor
added elastic stiffness matrix as crystallite output
2012-03-01 18:36:09 +05:30
(output) elasmatrix # elastic stiffness matrix
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
<phase>
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
new plasticity: none see material.config for necessary parameters (lattice_structure, elastic constants)
2012-07-03 16:46:38 +05:30
[Aluminium_elastic_only]
elasticity hooke
plasticity none
lattice_structure fcc
c11 106.75e9
c12 60.41e9
c44 28.34e9
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
[Aluminum_J2isotropic]
i think it's elasticity not elaticity, right?
2012-03-15 14:16:51 +05:30
elasticity hooke
replaced keyword constitution with plasticity in preparation of upcomming generalized elasticity
2012-03-12 19:39:37 +05:30
plasticity j2
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
(output) flowstress
(output) strainrate
c11 110.9e9
c12 58.34e9
taylorfactor 3
tau0 31e6
gdot0 0.001
n 20
h0 75e6
tausat 63e6
added Onurs modified description for tausat in j2 law. Polishing phenopowerlaw
2012-04-11 19:31:02 +05:30
#---- if tausat == 0.0 --------!!!VALUES HERE ARE NOT FOR ALUMINUM!!!
tausat_SinhFitA 2.4175e-7
tausat_SinhFitB 5.9804e-8
tausat_SinhFitC 1.0
tausat_SinhFitD 3.9
# h0_slope
#---------------------------#
renamed w0 and w0_slip to a and a_slip
2011-11-23 20:18:39 +05:30
a 2.25
* former "relevantRho" and "relevantResistance" is renamed to "atol_rho" and "atol_resistance" and now used as an absolute tolerance for the state residuum. before it was used rather as significant state, so whenever the state dropped below that value it was considered converged. (In dislotwin and titanmod constitutive law there is only one value atol_rho which is used for all the states, though the state array consists not only of densities. We need further parameters here!) * somewhat simplified convergence check for adaptive euler and runge-kutta
2010-10-26 18:46:37 +05:30
atol_resistance 1
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
added Onurs modified description for tausat in j2 law. Polishing phenopowerlaw
2012-04-11 19:31:02 +05:30
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
[Aluminum_phenopowerlaw]
# slip only
i think it's elasticity not elaticity, right?
2012-03-15 14:16:51 +05:30
elasticity hooke
replaced keyword constitution with plasticity in preparation of upcomming generalized elasticity
2012-03-12 19:39:37 +05:30
plasticity phenopowerlaw
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
(output) resistance_slip
(output) shearrate_slip
(output) resolvedstress_slip
(output) totalshear
(output) resistance_twin
(output) shearrate_twin
(output) resolvedstress_twin
(output) totalvolfrac
lattice_structure fcc
Nslip 12 0 0 0 # per family
Ntwin 0 0 0 0 # per family
added examples for j2
2009-03-06 16:45:55 +05:30
exchanged new lattice_structure ("fcc", "bcc", "hexagonal")
2009-03-20 20:49:21 +05:30
c11 106.75e9
c12 60.41e9
c44 28.34e9
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
update of sample material.config parts
2009-03-05 22:12:05 +05:30
gdot0_slip 0.001
n_slip 20
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
tau0_slip 31e6 # per family
tausat_slip 63e6 # per family
renamed w0 and w0_slip to a and a_slip
2011-11-23 20:18:39 +05:30
a_slip 2.25
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
gdot0_twin 0.001
n_twin 20
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
tau0_twin 31e6 # per family
quite some changes: # non-greedy memory allocation # generation of outputConstitutive to allow for script-based T16 extraction # exchange of phenomenological by more general phenopowerlaw # lattice is based on slip and twin families which can be treated as individual entities (switched on/off, separate hardening, etc.) # nicer debugging output # changed some error/warning codes # plus potentially some minor additional brushes here and there
2009-07-22 21:37:19 +05:30
s_pr 0 # push-up factor for slip saturation due to twinning
twin_b 0
twin_c 0
twin_d 0
twin_e 0
h0_slipslip 75e6
h0_sliptwin 0
h0_twinslip 0
h0_twintwin 0
interaction_slipslip 1 1 1.4 1.4 1.4 1.4
interaction_sliptwin 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
interaction_twinslip 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
interaction_twintwin 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
* former "relevantRho" and "relevantResistance" is renamed to "atol_rho" and "atol_resistance" and now used as an absolute tolerance for the state residuum. before it was used rather as significant state, so whenever the state dropped below that value it was considered converged. (In dislotwin and titanmod constitutive law there is only one value atol_rho which is used for all the states, though the state array consists not only of densities. We need further parameters here!) * somewhat simplified convergence check for adaptive euler and runge-kutta
2010-10-26 18:46:37 +05:30
atol_resistance 1
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
i think it's elasticity not elaticity, right?
2012-03-15 14:16:51 +05:30
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
[Aluminum_nonlocal]
i think it's elasticity not elaticity, right?
2012-03-15 14:16:51 +05:30
elasticity hooke
replaced keyword constitution with plasticity in preparation of upcomming generalized elasticity
2012-03-12 19:39:37 +05:30
plasticity nonlocal
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
/nonlocal/
constitutive_nonlocal: - dipole dislocations with evolution crystallite.f90: - collect state uses subdt and subTstar0_v - in nonlocal modus: set all crystallites to broken if one is not on track anymore after either stress integration or state update - constitutive_microstructure is now called inside state update and not in integrate_stress anymore material.config: - new parameter for nonlocal constitution CPFEM.f90: - age Tstar after increment was finished
2009-08-28 19:20:47 +05:30
(output) rho
(output) rho_edge
(output) rho_screw
- introduction of immobile (used) single dislocation densities as new state variables - changed nomenclature (rho -> rhoSgl) to distinguish precisely between single dislocation density and total dislocation density - changed material.config accordingly
2010-01-05 21:37:24 +05:30
(output) rho_sgl
(output) rho_sgl_edge
(output) rho_sgl_edge_pos
(output) rho_sgl_edge_neg
(output) rho_sgl_screw
(output) rho_sgl_screw_pos
(output) rho_sgl_screw_neg
(output) rho_sgl_mobile
(output) rho_sgl_edge_mobile
(output) rho_sgl_edge_pos_mobile
(output) rho_sgl_edge_neg_mobile
(output) rho_sgl_screw_mobile
(output) rho_sgl_screw_pos_mobile
(output) rho_sgl_screw_neg_mobile
(output) rho_sgl_immobile
(output) rho_sgl_edge_immobile
(output) rho_sgl_edge_pos_immobile
(output) rho_sgl_edge_neg_immobile
(output) rho_sgl_screw_immobile
(output) rho_sgl_screw_pos_immobile
(output) rho_sgl_screw_neg_immobile
(output) rho_dip
(output) rho_dip_edge
(output) rho_dip_screw
(output) excess_rho
constitutive_nonlocal: - dipole dislocations with evolution crystallite.f90: - collect state uses subdt and subTstar0_v - in nonlocal modus: set all crystallites to broken if one is not on track anymore after either stress integration or state update - constitutive_microstructure is now called inside state update and not in integrate_stress anymore material.config: - new parameter for nonlocal constitution CPFEM.f90: - age Tstar after increment was finished
2009-08-28 19:20:47 +05:30
(output) excess_rho_edge
(output) excess_rho_screw
(output) rho_forest
- introduction of immobile (used) single dislocation densities as new state variables - changed nomenclature (rho -> rhoSgl) to distinguish precisely between single dislocation density and total dislocation density - changed material.config accordingly
2010-01-05 21:37:24 +05:30
(output) delta
(output) delta_sgl
constitutive_nonlocal: - read in activation energy for dislocation glide from material.config - changed naming of dDipMin/Max to dLower/dUpper - added new outputs: rho_dot, rho_dot_dip, rho_dot_gen, rho_dot_sgl2dip, rho_dot_dip2sgl, rho_dot_ann_ath, rho_dot_ann_the, rho_dot_flux, d_upper_edge, d_upper_screw, d_upper_dot_edge, d_upper_dot_screw - poisson's ratio is now calculated from elastic constants - microstrucutre has state as first argument, since this is our output variable - periodic boundary conditions are taken into account for fluxes and internal stresses. for the moment, flag has to be set in constitutive_nonlocal. - corrected calculation for dipole formation by glide - added terms for dipole formation/annihilation by stress decrease/increase constitutive: - passing of arguments is adapted for constitutive_nonlocal model crystallite: - in stiffness calculation: call to collect_dotState used wrong arguments - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults homogenization: - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults IO: - changed error message 229 material.config: - changed example for nonlocal constitution according to constitutive_nonlocal all: - added some flush statements
2009-10-20 20:06:03 +05:30
(output) delta_dip
constitutive_nonlocal: - dipole dislocations with evolution crystallite.f90: - collect state uses subdt and subTstar0_v - in nonlocal modus: set all crystallites to broken if one is not on track anymore after either stress integration or state update - constitutive_microstructure is now called inside state update and not in integrate_stress anymore material.config: - new parameter for nonlocal constitution CPFEM.f90: - age Tstar after increment was finished
2009-08-28 19:20:47 +05:30
(output) shearrate
(output) resolvedstress
dislocation stress does not add to stress field anymore, but is only available as constitutive output for purposes of postprocessing. instead, we now use a backstress term (which is added to the resolved shear stress) that depends on the gradient of excess density on the same slip system.
2012-01-17 15:56:57 +05:30
(output) resolvedstress_back
constitutive_nonlocal: - reworked contribution of immobile dislocation density for rate equations - flux is now calculated on the basis of interpolated velocities and densities at the interface; both incoming and outgoing fluxes are considered, so every material point only changes his own dotState - dislocation velocity is now globally defined and calculated by subroutine constitutive_nonlocal_kinetics; the subroutine is called inside _LpAndItsTangent as well as _microstructure; therefore, microstructure now needs Tstar_v as additional input; in the future one should perhaps create a subroutine constitutive_kinetics that calls constitutive_nonlocal_kinetics separately, to clearly distinguish between microstructural and kinetic variables - better use flux density vector as output variable instead of scalar flux values for each interface - added output variables internal and external resolved stress crystallite: - added flag to force local stiffness calculation in case of nonlocal model - misorientation angle is explicitly set to zero when no neighbor can be found debug: - added flag "selectiveDebugger" that is used when debugging statements should only affect a specific element, ip and grain; these are specified with the new variables debug_e, debug_i and debug_g - debugger can now be used in its original sense
2010-02-17 18:51:36 +05:30
(output) resolvedstress_external
constitutive_nonlocal: - dipole dislocations with evolution crystallite.f90: - collect state uses subdt and subTstar0_v - in nonlocal modus: set all crystallites to broken if one is not on track anymore after either stress integration or state update - constitutive_microstructure is now called inside state update and not in integrate_stress anymore material.config: - new parameter for nonlocal constitution CPFEM.f90: - age Tstar after increment was finished
2009-08-28 19:20:47 +05:30
(output) resistance
constitutive_nonlocal: - read in activation energy for dislocation glide from material.config - changed naming of dDipMin/Max to dLower/dUpper - added new outputs: rho_dot, rho_dot_dip, rho_dot_gen, rho_dot_sgl2dip, rho_dot_dip2sgl, rho_dot_ann_ath, rho_dot_ann_the, rho_dot_flux, d_upper_edge, d_upper_screw, d_upper_dot_edge, d_upper_dot_screw - poisson's ratio is now calculated from elastic constants - microstrucutre has state as first argument, since this is our output variable - periodic boundary conditions are taken into account for fluxes and internal stresses. for the moment, flag has to be set in constitutive_nonlocal. - corrected calculation for dipole formation by glide - added terms for dipole formation/annihilation by stress decrease/increase constitutive: - passing of arguments is adapted for constitutive_nonlocal model crystallite: - in stiffness calculation: call to collect_dotState used wrong arguments - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults homogenization: - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults IO: - changed error message 229 material.config: - changed example for nonlocal constitution according to constitutive_nonlocal all: - added some flush statements
2009-10-20 20:06:03 +05:30
(output) rho_dot
- introduction of immobile (used) single dislocation densities as new state variables - changed nomenclature (rho -> rhoSgl) to distinguish precisely between single dislocation density and total dislocation density - changed material.config accordingly
2010-01-05 21:37:24 +05:30
(output) rho_dot_sgl
constitutive_nonlocal: - read in activation energy for dislocation glide from material.config - changed naming of dDipMin/Max to dLower/dUpper - added new outputs: rho_dot, rho_dot_dip, rho_dot_gen, rho_dot_sgl2dip, rho_dot_dip2sgl, rho_dot_ann_ath, rho_dot_ann_the, rho_dot_flux, d_upper_edge, d_upper_screw, d_upper_dot_edge, d_upper_dot_screw - poisson's ratio is now calculated from elastic constants - microstrucutre has state as first argument, since this is our output variable - periodic boundary conditions are taken into account for fluxes and internal stresses. for the moment, flag has to be set in constitutive_nonlocal. - corrected calculation for dipole formation by glide - added terms for dipole formation/annihilation by stress decrease/increase constitutive: - passing of arguments is adapted for constitutive_nonlocal model crystallite: - in stiffness calculation: call to collect_dotState used wrong arguments - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults homogenization: - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults IO: - changed error message 229 material.config: - changed example for nonlocal constitution according to constitutive_nonlocal all: - added some flush statements
2009-10-20 20:06:03 +05:30
(output) rho_dot_dip
(output) rho_dot_gen
- introduction of immobile (used) single dislocation densities as new state variables - changed nomenclature (rho -> rhoSgl) to distinguish precisely between single dislocation density and total dislocation density - changed material.config accordingly
2010-01-05 21:37:24 +05:30
(output) rho_dot_gen_edge
(output) rho_dot_gen_screw
constitutive_nonlocal: - read in activation energy for dislocation glide from material.config - changed naming of dDipMin/Max to dLower/dUpper - added new outputs: rho_dot, rho_dot_dip, rho_dot_gen, rho_dot_sgl2dip, rho_dot_dip2sgl, rho_dot_ann_ath, rho_dot_ann_the, rho_dot_flux, d_upper_edge, d_upper_screw, d_upper_dot_edge, d_upper_dot_screw - poisson's ratio is now calculated from elastic constants - microstrucutre has state as first argument, since this is our output variable - periodic boundary conditions are taken into account for fluxes and internal stresses. for the moment, flag has to be set in constitutive_nonlocal. - corrected calculation for dipole formation by glide - added terms for dipole formation/annihilation by stress decrease/increase constitutive: - passing of arguments is adapted for constitutive_nonlocal model crystallite: - in stiffness calculation: call to collect_dotState used wrong arguments - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults homogenization: - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults IO: - changed error message 229 material.config: - changed example for nonlocal constitution according to constitutive_nonlocal all: - added some flush statements
2009-10-20 20:06:03 +05:30
(output) rho_dot_sgl2dip
added separate output of dipole formation rate for edge and screw
2012-08-27 21:27:22 +05:30
(output) rho_dot_sgl2dip_edge
(output) rho_dot_sgl2dip_screw
constitutive_nonlocal: - read in activation energy for dislocation glide from material.config - changed naming of dDipMin/Max to dLower/dUpper - added new outputs: rho_dot, rho_dot_dip, rho_dot_gen, rho_dot_sgl2dip, rho_dot_dip2sgl, rho_dot_ann_ath, rho_dot_ann_the, rho_dot_flux, d_upper_edge, d_upper_screw, d_upper_dot_edge, d_upper_dot_screw - poisson's ratio is now calculated from elastic constants - microstrucutre has state as first argument, since this is our output variable - periodic boundary conditions are taken into account for fluxes and internal stresses. for the moment, flag has to be set in constitutive_nonlocal. - corrected calculation for dipole formation by glide - added terms for dipole formation/annihilation by stress decrease/increase constitutive: - passing of arguments is adapted for constitutive_nonlocal model crystallite: - in stiffness calculation: call to collect_dotState used wrong arguments - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults homogenization: - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults IO: - changed error message 229 material.config: - changed example for nonlocal constitution according to constitutive_nonlocal all: - added some flush statements
2009-10-20 20:06:03 +05:30
(output) rho_dot_ann_ath
(output) rho_dot_ann_the
rates in constitutive_results are taken directly from last converged step and not calculated again; added output of rates for annihilation of screws and deposition of edge jogs on collinear system
2012-08-16 16:33:22 +05:30
(output) rho_dot_ann_the_edge
(output) rho_dot_ann_the_screw
(output) rho_dot_edgejogs
added output for dislocation evolution rate associated with flux: "rho_dot_flux"
2010-03-10 15:19:40 +05:30
(output) rho_dot_flux
in nonlocal_microstructure: at the model surface the excess density is now extrapolated from opposite neighbor instead of assuming zero density; this results in better modeling of the dislocation stress at the surface restructured nonlocal_dotstate, to be able to easily switch on and off particular effects in the microstructure evolution nonlocal_dotstate now enforces a cutback when single density runs the risk of becoming negative; in the case of a state already below the relevantState dotState is set to zero introduced two new output variables: rho_dot_edge and rho_dot_screw
2010-05-21 14:21:15 +05:30
(output) rho_dot_flux_edge
(output) rho_dot_flux_screw
dislocation velocity output for each dislocation type (edge+,edge-,screw+,screw-) for fcc constitutive_nonlocal_kinetics is called only once and the result is used for each dislocation type, for all other lattice structures we have one call for each dislocation type
2012-01-26 13:13:36 +05:30
(output) velocity_edge_pos
(output) velocity_edge_neg
(output) velocity_screw_pos
(output) velocity_screw_neg
constitutive_nonlocal: - reworked contribution of immobile dislocation density for rate equations - flux is now calculated on the basis of interpolated velocities and densities at the interface; both incoming and outgoing fluxes are considered, so every material point only changes his own dotState - dislocation velocity is now globally defined and calculated by subroutine constitutive_nonlocal_kinetics; the subroutine is called inside _LpAndItsTangent as well as _microstructure; therefore, microstructure now needs Tstar_v as additional input; in the future one should perhaps create a subroutine constitutive_kinetics that calls constitutive_nonlocal_kinetics separately, to clearly distinguish between microstructural and kinetic variables - better use flux density vector as output variable instead of scalar flux values for each interface - added output variables internal and external resolved stress crystallite: - added flag to force local stiffness calculation in case of nonlocal model - misorientation angle is explicitly set to zero when no neighbor can be found debug: - added flag "selectiveDebugger" that is used when debugging statements should only affect a specific element, ip and grain; these are specified with the new variables debug_e, debug_i and debug_g - debugger can now be used in its original sense
2010-02-17 18:51:36 +05:30
(output) fluxDensity_edge_pos_x
(output) fluxDensity_edge_pos_y
(output) fluxDensity_edge_pos_z
(output) fluxDensity_edge_neg_x
(output) fluxDensity_edge_neg_y
(output) fluxDensity_edge_neg_z
(output) fluxDensity_screw_pos_x
(output) fluxDensity_screw_pos_y
(output) fluxDensity_screw_pos_z
(output) fluxDensity_screw_neg_x
(output) fluxDensity_screw_neg_y
(output) fluxDensity_screw_neg_z
Reworked kinetics. Now there is a universal law which can be used for both fcc and bcc (and probably even hcp). It mainly consists of an athermal forest cutting part , solid solution and peierls as thermally activated processes, and viscous glide. Therefore, lots of new parameters in the material.config. Not sure yet if the values make sense though. Also renamed some of the old parameters. Unknown constitutive output raises error.
2012-01-25 22:34:37 +05:30
(output) maximumDipoleHeight_edge
(output) maximumDipoleHeight_screw
new outputs "accumulatedshear", "velocity_edge", and "velocity_screw" (the latter two replace the output "dislocationvelocity")
2011-11-09 14:52:52 +05:30
(output) accumulatedshear
dislocation stress does not add to stress field anymore, but is only available as constitutive output for purposes of postprocessing. instead, we now use a backstress term (which is added to the resolved shear stress) that depends on the gradient of excess density on the same slip system.
2012-01-17 15:56:57 +05:30
(output) dislocationstress
constitutive_nonlocal: - read in activation energy for dislocation glide from material.config - changed naming of dDipMin/Max to dLower/dUpper - added new outputs: rho_dot, rho_dot_dip, rho_dot_gen, rho_dot_sgl2dip, rho_dot_dip2sgl, rho_dot_ann_ath, rho_dot_ann_the, rho_dot_flux, d_upper_edge, d_upper_screw, d_upper_dot_edge, d_upper_dot_screw - poisson's ratio is now calculated from elastic constants - microstrucutre has state as first argument, since this is our output variable - periodic boundary conditions are taken into account for fluxes and internal stresses. for the moment, flag has to be set in constitutive_nonlocal. - corrected calculation for dipole formation by glide - added terms for dipole formation/annihilation by stress decrease/increase constitutive: - passing of arguments is adapted for constitutive_nonlocal model crystallite: - in stiffness calculation: call to collect_dotState used wrong arguments - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults homogenization: - crystallite_postResults uses own Tstar_v and temperature, no need for passing them from materialpoint_postResults IO: - changed error message 229 material.config: - changed example for nonlocal constitution according to constitutive_nonlocal all: - added some flush statements
2009-10-20 20:06:03 +05:30
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
lattice_structure fcc
* comments are now recognized by IO even when they do not appear at the beginning of the line * no need for the zero entries in the material.config anymore
2011-05-30 14:39:19 +05:30
Nslip 12 # number of slip systems
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
update of nonlocal material parameters
2011-05-20 13:41:22 +05:30
c11 106.75e9 # elastic constants
now with first draft of nonlocal constitutive law debugging memory leak closed debugging counters corrected center of gravity stored in mesh state updated is now split into a collecting loop and an execution updateState and updateTemperature fill sequentially separate logicals and evaluate afterwards to converged added 3x3 transposition function, norm for 3x1 matrix and 33x3 matrix multiplication in math non-converged crystallite triggers materialpoint cutback (used to respond elastically) non-converged materialpoint raises terminal illness which in turn renders whole FE increment useless by means of odd stress/stiffness and thus waits for FE cutback
2009-08-11 22:01:57 +05:30
c12 60.41e9
c44 28.34e9
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
* comments are now recognized by IO even when they do not appear at the beginning of the line * no need for the zero entries in the material.config anymore
2011-05-30 14:39:19 +05:30
burgers 2.86e-10 # Burgers vector in m
Reworked kinetics. Now there is a universal law which can be used for both fcc and bcc (and probably even hcp). It mainly consists of an athermal forest cutting part , solid solution and peierls as thermally activated processes, and viscous glide. Therefore, lots of new parameters in the material.config. Not sure yet if the values make sense though. Also renamed some of the old parameters. Unknown constitutive output raises error.
2012-01-25 22:34:37 +05:30
rhoSglEdgePos0 0.25e10 # Initial positive edge single dislocation density in m/m**3 (per slip family)
rhoSglEdgeNeg0 0.25e10 # Initial negative edge single dislocation density in m/m**3 (per slip family)
rhoSglScrewPos0 0.25e10 # Initial positive screw single dislocation density in m/m**3 (per slip family)
rhoSglScrewNeg0 0.25e10 # Initial negative screw single dislocation density in m/m**3 (per slip family)
rhoDipEdge0 1e8 # Initial edge dipole dislocation density in m/m**3 (per slip family)
rhoDipScrew0 1e8 # Initial screw dipole dislocation density in m/m**3 (per slip family)
* now able to introduce some scatter in the initial single dislocation density (only for nonlocal model!) ; setting the parameter "rhoSglScatter" to a positive value generates a gauss distribution for the dislocation density with standard deviation equal to "rhoSglScatter" * dislocation stress calculation is only done for nonlocal constitution ("/nonlocal/" keyword is present in material.config)
2011-02-04 21:11:32 +05:30
rhoSglScatter 0 # standard deviation of scatter in initial single dislocation density
Reworked kinetics. Now there is a universal law which can be used for both fcc and bcc (and probably even hcp). It mainly consists of an athermal forest cutting part , solid solution and peierls as thermally activated processes, and viscous glide. Therefore, lots of new parameters in the material.config. Not sure yet if the values make sense though. Also renamed some of the old parameters. Unknown constitutive output raises error.
2012-01-25 22:34:37 +05:30
minimumDipoleHeightEdge 2e-9 # minimum distance for stable edge dipoles in m (per slip family)
minimumDipoleHeightScrew 2e-9 # minimum distance for stable screw dipoles in m (per slip family)
* comments are now recognized by IO even when they do not appear at the beginning of the line * no need for the zero entries in the material.config anymore
2011-05-30 14:39:19 +05:30
lambda0 80 # prefactor for mean free path
* kinetics now according to Mohles; enables solid solution hardening * changed example in material.config accordingly
2011-01-26 15:47:42 +05:30
atomicVolume 1.7e-29 # atomic volume in m**3
Reworked kinetics. Now there is a universal law which can be used for both fcc and bcc (and probably even hcp). It mainly consists of an athermal forest cutting part , solid solution and peierls as thermally activated processes, and viscous glide. Therefore, lots of new parameters in the material.config. Not sure yet if the values make sense though. Also renamed some of the old parameters. Unknown constitutive output raises error.
2012-01-25 22:34:37 +05:30
selfdiffusionPrefactor 1e-4 # prefactor for self-diffusion coefficient in m**2/s
selfdiffusionEnergy 2.3e-19 # activation enthalpy for seld-diffusion in J
corrected kinetics law and changed parameters. For solid solution hardening there are 3 parameters: the activation energy, the concentration of obstacles that determines the activation length and meanfreepath, and the obstacle size that determines the activation volume. For the Peierls mechanism there is: the width of doublekinks that determines the activation volume and the Peierls stress for edge and screw. Still testing needed to check whether the current formulation makes sense or not.
2012-02-03 18:20:54 +05:30
solidSolutionEnergy 2e-19 # activation energy of solid solution particles in J
changed Peierls stress to more realistic values for fcc
2012-02-03 18:42:45 +05:30
solidSolutionConcentration 1e-5 # concentration of solid solution in parts per b^3
corrected kinetics law and changed parameters. For solid solution hardening there are 3 parameters: the activation energy, the concentration of obstacles that determines the activation length and meanfreepath, and the obstacle size that determines the activation volume. For the Peierls mechanism there is: the width of doublekinks that determines the activation volume and the Peierls stress for edge and screw. Still testing needed to check whether the current formulation makes sense or not.
2012-02-03 18:20:54 +05:30
solidSolutionSize 2 # size of solid solution obstacles in multiples of burgers vector length
changed Peierls stress to more realistic values for fcc
2012-02-03 18:42:45 +05:30
peierlsStressEdge 1e5 # Peierls stress for edges in Pa (per slip family)
peierlsStressScrew 1e5 # Peierls stress for screws in Pa (per slip family)
corrected kinetics law and changed parameters. For solid solution hardening there are 3 parameters: the activation energy, the concentration of obstacles that determines the activation length and meanfreepath, and the obstacle size that determines the activation volume. For the Peierls mechanism there is: the width of doublekinks that determines the activation volume and the Peierls stress for edge and screw. Still testing needed to check whether the current formulation makes sense or not.
2012-02-03 18:20:54 +05:30
doublekinkWidth 10 # width of double kinks in multiples of burgers vector length b
viscosity 1e-4 # viscosity for dislocation glide in Pa s
Reworked kinetics. Now there is a universal law which can be used for both fcc and bcc (and probably even hcp). It mainly consists of an athermal forest cutting part , solid solution and peierls as thermally activated processes, and viscous glide. Therefore, lots of new parameters in the material.config. Not sure yet if the values make sense though. Also renamed some of the old parameters. Unknown constitutive output raises error.
2012-01-25 22:34:37 +05:30
p 1 # exponent for thermal barrier profile
q 1 # exponent for thermal barrier profile
attackFrequency 50e9 # attack frequency in Hz
added relativistic correction of velocity (maximum velocity given by parameter in material.config); probability of thermal activation in velocity law not allowed to be greater than one. output of creation rate for edge jogs now for own system, not collinear. check for negative densities in dotState now uses absoluteToleranceRho instead of significantRho.
2012-08-30 13:03:13 +05:30
maximumVelocity 3600 # maximum allowed velocity
update of nonlocal material parameters
2011-05-20 13:41:22 +05:30
surfaceTransmissivity 1.0 # transmissivity of free surfaces for dislocation flux
corrected debug output of evolution rates; added possibility to change the safety factor for the CFL flux condition via the material.config file; updated the example material.config due to recent changes in nonlocal constitutive
2012-08-16 14:43:38 +05:30
grainboundaryTransmissivity 0.0 # transmissivity of grain boundaries for dislocation flux (grain bundaries are identified as interfaces with different textures on both sides); if not set or set to negative number, the subroutine automatically determines the transmissivity at the grain boundary
interaction_SlipSlip 0 0 0.625 0.07 0.137 0.122 # Dislocation interaction coefficient
new parameter "significantRho" for nonlocal constitutive law ; density below this value will hardly contribute to dislocation glide or any dislocation reaction ; old parameter "absoluteToleranceRho" is now used only for its initial purpose, namely the absolute tolerance in the state integration
2012-08-23 11:18:21 +05:30
shortRangeStressCorrection 0 # switch for use of short range correction stress
cutoffRadius 1e-3 # cutoff radius for dislocation stress in m
corrected debug output of evolution rates; added possibility to change the safety factor for the CFL flux condition via the material.config file; updated the example material.config due to recent changes in nonlocal constitutive
2012-08-16 14:43:38 +05:30
CFLfactor 2.0 # safety factor for CFL flux check (numerical parameter)
new parameter "significantRho" for nonlocal constitutive law ; density below this value will hardly contribute to dislocation glide or any dislocation reaction ; old parameter "absoluteToleranceRho" is now used only for its initial purpose, namely the absolute tolerance in the state integration
2012-08-23 11:18:21 +05:30
significantRho 1e6 # minimum dislocation density considered relevant in m/m**3
absoluteToleranceRho 1e4 # absolute tolerance for dislocation density in m/m**3
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
update of nonlocal material parameters
2011-05-20 13:41:22 +05:30
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
[BCC_Ferrite]
i think it's elasticity not elaticity, right?
2012-03-15 14:16:51 +05:30
elasticity hooke
replaced keyword constitution with plasticity in preparation of upcomming generalized elasticity
2012-03-12 19:39:37 +05:30
plasticity phenopowerlaw
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
lattice_structure bcc
Nslip 12 0 0 0 # per family
Ntwin 0 0 0 0 # per family
c11 233.3e9
c12 135.5e9
c44 118.0e9
gdot0_slip 0.001
n_slip 20
tau0_slip 88.0e6 0 0 0 # per family
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
tausat_slip 205.0e6 0 0 0 # per family
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
gdot0_twin 0.001
n_twin 20
tau0_twin 31.0e6 0 0 0 # per family
s_pr 0 # push-up factor for slip saturation due to twinning
twin_b 0
twin_c 0
twin_d 0
twin_e 0
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
h0_slipslip 495.0e6
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
h0_sliptwin 0
h0_twinslip 0
h0_twintwin 0
interaction_slipslip 1 1 1.4 1.4 1.4 1.4
interaction_sliptwin 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
interaction_twinslip 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
interaction_twintwin 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
renamed w0 and w0_slip to a and a_slip
2011-11-23 20:18:39 +05:30
a_slip 1.0
* former "relevantRho" and "relevantResistance" is renamed to "atol_rho" and "atol_resistance" and now used as an absolute tolerance for the state residuum. before it was used rather as significant state, so whenever the state dropped below that value it was considered converged. (In dislotwin and titanmod constitutive law there is only one value atol_rho which is used for all the states, though the state array consists not only of densities. We need further parameters here!) * somewhat simplified convergence check for adaptive euler and runge-kutta
2010-10-26 18:46:37 +05:30
atol_resistance 1
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
[BCC_Martensite]
replaced keyword constitution with plasticity in preparation of upcomming generalized elasticity
2012-03-12 19:39:37 +05:30
plasticity phenopowerlaw
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
lattice_structure bcc
Nslip 12 0 0 0 # per family
Ntwin 0 0 0 0 # per family
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
c11 417.4e9
c12 242.4e9
c44 211.1e9
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
gdot0_slip 0.001
n_slip 20
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
tau0_slip 575.00e6 0 0 0 # 460.0e6 # per family
tausat_slip 1280.0e6 0 0 0 # 1020.0e6 # per family
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
gdot0_twin 0.001
n_twin 20
tau0_twin 31.0e6 0 0 0 # per family
s_pr 0 # push-up factor for slip saturation due to twinning
twin_b 0
twin_c 0
twin_d 0
twin_e 0
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
h0_slipslip 53500.0e6 # 35000.0e6
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
h0_sliptwin 0
h0_twinslip 0
h0_twintwin 0
interaction_slipslip 1 1 1.4 1.4 1.4 1.4
interaction_sliptwin 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
interaction_twinslip 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
interaction_twintwin 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1 1
renamed w0 and w0_slip to a and a_slip
2011-11-23 20:18:39 +05:30
a_slip 2.0
* former "relevantRho" and "relevantResistance" is renamed to "atol_rho" and "atol_resistance" and now used as an absolute tolerance for the state residuum. before it was used rather as significant state, so whenever the state dropped below that value it was considered converged. (In dislotwin and titanmod constitutive law there is only one value atol_rho which is used for all the states, though the state array consists not only of densities. We need further parameters here!) * somewhat simplified convergence check for adaptive euler and runge-kutta
2010-10-26 18:46:37 +05:30
atol_resistance 1
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
The new dislocation model is now implemented in constitutive_dislotwin.f90 (seems to run fine, but still under investigation)
2009-10-10 01:58:23 +05:30
[TWIP steel FeMnC]
i think it's elasticity not elaticity, right?
2012-03-15 14:16:51 +05:30
elasticity hooke
replaced keyword constitution with plasticity in preparation of upcomming generalized elasticity
2012-03-12 19:39:37 +05:30
plasticity dislotwin
updated section with dislotwin paramters
2010-05-06 14:31:54 +05:30
#(output) edge_density
#(output) dipole_density
#(output) shear_rate_slip
#(output) mfp_slip
#(output) resolved_stress_slip
#(output) threshold_stress_slip
#(output) twin_fraction
#(output) shear_rate_twin
#(output) mfp_twin
#(output) resolved_stress_twin
#(output) threshold_stress_twin
added parameters for shear band model
2011-09-14 19:05:28 +05:30
#(output) shear_rate_shearband
#(output) resolved_stress_shearband
#(output) schmid_factor_shearband
#(output) sb_eigenvalues
#(output) sb_eigenvectors
The new dislocation model is now implemented in constitutive_dislotwin.f90 (seems to run fine, but still under investigation)
2009-10-10 01:58:23 +05:30
### Material parameters ###
lattice_structure fcc
some modifications in line with Davids analytical model input some additional variables via material.config
2010-08-17 19:53:55 +05:30
C11 175.0e9 # From Music et al. Applied Physics Letters 91, 191904 (2007)
C12 115.0e9
C44 135.0e9
grainsize 2.0e-5 # Average grain size [m]
SolidSolutionStrength 1.5e8 # Strength due to elements in solid solution
updated section with dislotwin paramters
2010-05-06 14:31:54 +05:30
### Dislocation glide parameters ###
Nslip 12 0 0 0
slipburgers 2.56e-10 0 0 0 # Burgers vector of slip system [m]
rhoedge0 1.0e12 0 0 0 # Initial dislocation density [m/m**3]
rhoedgedip0 1.0 0 0 0 # Initial dislocation density [m/m**3]
Qedge 3.7e-19 0 0 0 # Activation energy for dislocation glide [J]
v0 1.0e-4 0 0 0 # Initial glide velocity [m/s]
CLambdaSlip 10.0 0 0 0 # Adj. parameter controlling dislocation mean free path
D0 4.0e-5 # Vacancy diffusion prefactor [m**2/s]
Qsd 4.5e-19 # Activation energy for climb [J]
removed special characters from twip steel section in material.config changed crirtical twin stress in constitutive_dislotwin.f90
2010-03-24 13:47:27 +05:30
pexponent 1.0 # p-exponent in glide velocity
qexponent 1.0 # q-exponent in glide velocity
updated section with dislotwin paramters
2010-05-06 14:31:54 +05:30
Catomicvolume 1.0 # Adj. parameter controlling the atomic volume [in b]
Cedgedipmindistance 1.0 # Adj. parameter controlling the minimum dipole distance [in b]
* former "relevantRho" and "relevantResistance" is renamed to "atol_rho" and "atol_resistance" and now used as an absolute tolerance for the state residuum. before it was used rather as significant state, so whenever the state dropped below that value it was considered converged. (In dislotwin and titanmod constitutive law there is only one value atol_rho which is used for all the states, though the state array consists not only of densities. We need further parameters here!) * somewhat simplified convergence check for adaptive euler and runge-kutta
2010-10-26 18:46:37 +05:30
atol_rho 1.0e-200
updated section with dislotwin paramters
2010-05-06 14:31:54 +05:30
interactionSlipSlip 0.122 0.122 0.625 0.07 0.137 0.122 # Interaction coefficients (Kubin et al. 2008)
added parameters for shear band model
2011-09-14 19:05:28 +05:30
### Shearband parameters ###
shearbandresistance 180e6
shearbandvelocity 1e-4
Input parameter 'QedgePerSbSystem' which denotes activation energy for each shear band system is added
2012-05-22 21:40:28 +05:30
QedgePerSbSystem 3.7e-19 # Activation energy for shear banding [J]
added parameters for shear band model
2011-09-14 19:05:28 +05:30
updated section with dislotwin paramters
2010-05-06 14:31:54 +05:30
### Twinning parameters ###
Ntwin 12
twinburgers 1.47e-10 # Burgers vector of twin system [m]
twinsize 5.0e-8 # Twin stack mean thickness [m]
some modifications in line with Davids analytical model input some additional variables via material.config
2010-08-17 19:53:55 +05:30
L0 442.0 # Length of twin nuclei in Burgers vectors
updated section with dislotwin paramters
2010-05-06 14:31:54 +05:30
maxtwinfraction 1.0 # Maximum admissible twin volume fraction
Ndot0 0.0 # Number of potential sources per volume per time [1/m**3.s]
rexponent 10.0 # r-exponent in twin formation probability
Cmfptwin 1.0 # Adj. parameter controlling twin mean free path
Cthresholdtwin 1.0 # Adj. parameter controlling twin threshold stress
interactionSlipTwin 0.0 1.0 # Dislocation-Twin interaction coefficients
interactionTwinTwin 0.0 1.0 # Twin-Twin interaction coefficients
corrected error messages you can now switch of shear banding by seting sb_velocity to zero stacking fault energy parameters are now read from material.config
2011-09-26 15:25:08 +05:30
SFE_0K -0.0396 # stacking fault energy at zero K; TWIP steel: -0.0526; Cu: -0.0396
dSFE_dT 0.0002 # temperature dependance of stacking fault energy
The new dislocation model is now implemented in constitutive_dislotwin.f90 (seems to run fine, but still under investigation)
2009-10-10 01:58:23 +05:30
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
<texture>
reworked crystallite part to allow for flexible user output --> new "crystallite" part in config file --> new "crystallite" option for microstructures --> new output file "...job.outputCrystallite" to be used in conjunction with marc_addUserOutput for meaningful naming of User Defined Vars.
2010-02-25 23:09:11 +05:30
#-------------------#
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
[Rolling]
hybridIA DP_EBSD.linearODF
added some examples
2009-12-08 21:01:50 +05:30
symmetry orthotropic # or monoclinic
CPFEM.f90 >>> A very small, not important thing. homogenization.f90 and crystallite.f90 >>> Correction in the algorithm to count the iteration distribution (for better statistics). material.config and numerics.config >>> more collection of parameters.
2009-08-28 20:35:14 +05:30
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
[random]
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
[001]
(gauss) phi1 0.000 Phi 0.000 phi2 0.000 scatter 0.000 fraction 1.000
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
[101]
(gauss) phi1 0.000 Phi 45.000 phi2 90.000 scatter 0.000 fraction 1.000
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
[111]
(gauss) phi1 0.000 Phi 54.7356 phi2 45.000 scatter 0.000 fraction 1.000
overhaul to allow for multiphase/homogenization setup.
2009-03-04 17:18:54 +05:30
Example of material.config, delivering the required information for the new version of constitutive_dislobased
2009-07-14 17:01:06 +05:30
[123]
(gauss) phi1 209.805 Phi 29.206 phi2 63.435 scatter 0.000 fraction 1.000
added some examples
2009-12-08 21:01:50 +05:30
[fiber example]
# fiber axis in spherical coordinates: alpha crystal system, beta sample system
forgotten: the change in the input config
2010-03-24 18:58:46 +05:30
(fiber) alpha1 123 alpha2 123 beta1 12 beta2 45 scatter 15 fraction 0.333
reworked restarting for compatibility with abaqus (not yet fully working) added new orientation feature for direct simulation: component type (random) asigns random orientation to an entire grain
2011-05-28 15:14:43 +05:30
[random single crystals]
* comments are now recognized by IO even when they do not appear at the beginning of the line * no need for the zero entries in the material.config anymore
2011-05-30 14:39:19 +05:30
(random) scatter 0.000 fraction 1.000