-removed to long lines
-restructured f2py modules and merged make_DAMASK2Python into setup processing
-setup_code.py now sets library path in makefile and asks for compile switches for spectral code
-substituted \ in format strings with $
restructured DAMASK_spectral:
-more logical output and structure of code
-better input for spectral debug parameters
introduced parameters for selective debugging of spectral code and partly introduced the advanced divergence calculation again which is controlled by debug.config
added switch in numerics to control divergence behavior (uncorrected and corrected by phenomenological factor)
added precision directive to all values I found
restart write is on per default
restart read is switched on by using --restart or -r INT where INT gives step at which the calculation should restart
setting INT to a value <1 will turn restart write off
- removed unnecessary "return" before end of subroutine or function:
- changed undetermined array length (:) to (1:3)
To prevent problems with some code analysing tools:
- "3D oneliner loops" (with ";) only for "do" and "enddo" at the same time
- removed line continuation in OMP statements
made the makefile more flexible, removed heap-arrays switch
made convergence independent of size and resolution,
polishing output in DAMASK_spectral.f90
added function to compute eigenvalues without eigenvectors and function to convert a 3x3 logical to a 9 vector in math.f90
removed obsolete variable in numerics.f90
you have to specify the job you are restarting from in the job description (cae), if you prepare your input file by hand this is the first line after *Heading
example: if the first job was using Oldjob.inp the first entry in the job description needs to be Oldjob (without the .inp)
as for Marc restart works only from last converged increment, i.e. ther restart writing should be specified like this:
*retsart, write, frequency=1, overlay
Overlay is not essential but saves a lot of disk space and as stated before you can only restart from the last converged increment anyway
In order to keep it like that, please follow these simple rules:
DON'T use implicit array subscripts:
example: real, dimension(3,3) :: A,B
A(:,2) = B(:,1) <--- DON'T USE
A(1:3,2) = B(1:3,1) <--- BETTER USE
In many cases the use of explicit array subscripts is inevitable for parallelization. Additionally, it is an easy means to prevent memory leaks.
Enclose all write statements with the following:
!$OMP CRITICAL (write2out)
<your write statement>
!$OMP END CRITICAL (write2out)
Whenever you change something in the code and are not sure if it affects parallelization and leads to nonconforming behavior, please ask me and/or Franz to check this.
* now complaining when encountering an unknown nonlocal parameter in material.config
* use same error ID for all material parameters out of bounds
* symmetric flux calculation in side dotState can now be omitted (because of new treatment of periodicity)
* switching back to "local flux balance" (add leaving and entering fluxes at central MP, don't touch neighbor) instead of "flux distribution" (subtract leaving fluxes from central MP and add them at neighboring MP). This has the advantage that there is almost no need for CRITICAL statements in parallelization, so hopefully this results in some speed up.
removed storage of full cauchy stres field from mpie_spectral.f90, only average is stored now
added cauchy stress and von mises equivalent calculation to spectral post.
numerics: polishing
mpie_cpfem_marc: polishing
..powerlaw: aware of symmetryType function
crystallite: aware of symmetryType function, smaller leapfrog acceleration
IO: new warning 101
CPFEM: range of odd stress is now -1e15...+1e15, H_sym is used for stiffness
Major changes:
CPFEM.f90 =>
1. Moving the initialization out of CPFEM_general into a separate subroutine, which is directly called by the hypela2 (Beware, the Abaqus version must also be modified in order to adapt with this change).
2. Restore primary state variables in CPFEM_init from binary files when requested (Marc flag: restart read).
3. Writing primary state variables into binary files (Marc flag: restart write).
FEsolving.f90 =>
1. Adding functions to recognize Marc restart flags: read and write and the corresponding restart file (parent job).
2. Change the initial value of cycleCounter = -1 in conjuction with the change made the ping-pong scheme
homogenization_RGC.f90 =>
1. Just syntax polishing.
IO.f90 =>
1. Adding functions/subroutines to open binary files for writing the primary state variables for restart purpose.
mpie_cpfem_marc.f90
1. Modification of the general scheme for collection and calculation in order to accommodate the newly added restart feature.
added some parameters for spectral method to numerics.f90 (tolerance)
changed error message concerning spectral method in IO.f90
corrected calculation of stress BC in mpie_spectral.f90
* now remembering stiffness similar to how we do it for Lp etc.; avoids undefined stiffness values for nonconverged stiffness calculation
* non-local stuff:
* changed non-local kinetics (Gilman2002)
* enforce zero shearrate for overall carrrier density below relevant density
* enforce zero density for those states that become negative and were below relevant density before
* dislocation velocity is not limited by V^(1/3) / dt anymore
mesh:
elemType identification based on lower case
Abaqus now reports more errors
IO:
new function to inquire whether inputfile contains "parts"
new function to assemble multiply included inputfile into a flat one
awareness of range generation in element numbers
error reporting
--> 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.
- corrected flux term
- multiplication is now aware of dislocation type
- corrected change rate for "dipole size" dupper
- corrected term for dipole dissociation by stress change
- added transmissivity term in fluxes which accounts for misorientation between two neighboring grains (yet hardcoded transmissivity according to misorientation angle)
- added more output variables
constitutive:
- 2 additional variables "previousDotState" and "previousDotState2", which are used to store the previous and second previous dotState (used in crystallite for acceleration/stabilization of state integration)
- timer for dotState now measures the time for calls to constitutive_ collectState (used to reside in crystallite_updateState, which is not critical in terms of calculation time anymore)
crystallite:
- convergence check for nonlocal elments is now done at end of crystallite loop, not at the beginning; we simple set all elements to not converged if there is at least one nonlocal element that did not converge
- need call to microstructure before first call to collect dotState for dependent states
- stiffness calculation (jacobian): if there are nonlocal elements, we also have to consider changes in our neighborhood's states; so for every perturbed component in a single ip, we have to loop over all elements; since this is extremely time-consuming, we just perturb one component per cycle, starting with the one that changes the most during regular time step.
- updateState gets a damping prefactor for our dotState that helps to improve convergence; prefactor is calculated according to change of dotState
IO:
- additional warning message for unknown crystal symmetry
(1) subStepSizeHomog and subStepSizeCryst := size of substep when cut-back is applied (initially was hard-coded).
(2) stepIncreaseHomog and stepIncreaseCryst := step increase when calculation for substep converge (was also hardcoded).
introduced a possibility to choose different finite difference scheme, i.e., forward-, backward- and central-difference, for computing grain numerical tangent. note that central-difference scheme will slow down the computation significantly. please use it only if necessary.
parameters to set these new features have been included in numerics.f90 and numerics.config, whereas corresponding error messages have been introduced in the IO.f90
- 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
# IO has some additional functionality for Abaqus parsing
# ping pong scheme in FE interface now similar (and more human understandable) in both versions
# mesh has better splitting of different tasks, plus operation on database whenever possible
# FEsolver as new global var to indicate FEM solver type
# computation mode reshuffling: 6 is now Marc special case of recycling...
(state < relevant state) or (residuum < relative tolerance * state)
since the relevant value for the state variables depend on their nature and can vary by large scales (e.g. volume fraction: 1e-10, dislocation density: 1e5) it is not possible to set a unique value. instead the constitutive law has to decide what is relevant. therefore, all constitutive laws now read in parameters from the material.config that determine the values for relevantState [@luc: in dislobased law relevant State is for the moment generally set to 1e-200, so no additional parameters necessary in material.config. if you also want this feature, we can still implement it, no big deal]
- added sanity checks in constitutive_nonlocal.f90
- corrected coordinate transformation for backstress calculation in constitutive_nonlocal.f90
- corrected equations for evolution of dipole dislocation densities (athermal annihilation and formation by glide)
IO.f90 >>> adding "inRad" instead of using inRad from math.f90 module, since math.f90 module is now below IO.f90.
numerics.f90 >>> now can read the parameter "fixed_seed" from numerics.config. this parameter is used to set a pseudo-random number generator/fixed seeding. default value is 0 (zero), which will give fully random number.
math.f90 >> adding a possibility to fix the seeding (i.e., pseudo random number)
numerics.config >>> add a new parameter: "fixed_seed"
formerly, if the number of orientations requested was (far) less than the number of nonzero bins in the texture representation, you only got a subset of low phi1 values..! (that is the top corner in Euler space -- Hi Bing ;-) )
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
# 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
Martin Diehl