Merge branch 'Dislotwin-climb2' into 'development'
Dislotwin climb2 See merge request damask/DAMASK!94
This commit is contained in:
Franz Roters
commit
2aaa5ff8e7
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@ -390,7 +390,6 @@ Phenopowerlaw_singleSlip:
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- master
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- release
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###################################################################################################
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Marc_compileIfort2018_1:
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stage: compileMarc
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@ -402,7 +401,6 @@ Marc_compileIfort2018_1:
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- master
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- release
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###################################################################################################
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Hex_elastic:
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stage: marc
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@ -440,11 +438,13 @@ J2_plasticBehavior:
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- master
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- release
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###################################################################################################
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grid_all_example:
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stage: example
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script: grid_all_example/test.py
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except:
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- master
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- release
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###################################################################################################
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SpectralRuntime:
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@ -53,12 +53,13 @@ module plastic_dislotwin
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nu, &
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D0, & !< prefactor for self-diffusion coefficient
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Qsd, & !< activation energy for dislocation climb
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D, & !<grain size
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omega, & !< frequency factor for dislocation climb
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D, & !< grain size
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p_sb, & !< p-exponent in shear band velocity
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q_sb, & !< q-exponent in shear band velocity
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CEdgeDipMinDistance, & !<
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i_tw, & !<
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tau_0, & !<strength due to elements in solid solution
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tau_0, & !< strength due to elements in solid solution
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L_tw, & !< Length of twin nuclei in Burgers vectors
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L_tr, & !< Length of trans nuclei in Burgers vectors
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xc_twin, & !< critical distance for formation of twin nucleus
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@ -104,6 +105,7 @@ module plastic_dislotwin
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integer, dimension(:,:), allocatable :: &
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fcc_twinNucleationSlipPair ! ToDo: Better name? Is also use for trans
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real(pReal), dimension(:,:), allocatable :: &
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n0_sl, & !< slip system normal
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forestProjection, &
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C66
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real(pReal), dimension(:,:,:), allocatable :: &
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@ -123,6 +125,7 @@ module plastic_dislotwin
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integer(kind(undefined_ID)), dimension(:), allocatable :: &
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outputID !< ID of each post result output
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logical :: &
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ExtendedDislocations, & !< consider split into partials for climb calculation
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fccTwinTransNucleation, & !< twinning and transformation models are for fcc
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dipoleFormation !< flag indicating consideration of dipole formation
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end type !< container type for internal constitutive parameters
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@ -251,6 +254,8 @@ subroutine plastic_dislotwin_init
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prm%forestProjection = lattice_forestProjection (prm%N_sl,config%getString('lattice_structure'),&
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config%getFloat('c/a',defaultVal=0.0_pReal))
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prm%n0_sl = lattice_slip_normal(prm%N_sl,config%getString('lattice_structure'),&
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config%getFloat('c/a',defaultVal=0.0_pReal))
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prm%fccTwinTransNucleation = merge(.true., .false., lattice_structure(p) == LATTICE_FCC_ID) &
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.and. (prm%N_sl(1) == 12)
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if(prm%fccTwinTransNucleation) &
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@ -272,6 +277,19 @@ subroutine plastic_dislotwin_init
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prm%D0 = config%getFloat('d0')
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prm%Qsd = config%getFloat('qsd')
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prm%atomicVolume = config%getFloat('catomicvolume') * prm%b_sl**3.0_pReal
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prm%ExtendedDislocations = config%keyExists('/extend_dislocations/')
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if (prm%ExtendedDislocations) then
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prm%SFE_0K = config%getFloat('sfe_0k')
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prm%dSFE_dT = config%getFloat('dsfe_dt')
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endif
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! multiplication factor according to crystal structure (nearest neighbors bcc vs fcc/hex)
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!@details: Refer: Argon & Moffat, Acta Metallurgica, Vol. 29, pg 293 to 299, 1981
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prm%omega = config%getFloat('omega', defaultVal = 1000.0_pReal) &
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* merge(12.0_pReal, &
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8.0_pReal, &
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lattice_structure(p) == LATTICE_FCC_ID .or. lattice_structure(p) == LATTICE_HEX_ID)
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! expand: family => system
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prm%rho_mob_0 = math_expand(prm%rho_mob_0, prm%N_sl)
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@ -740,8 +758,11 @@ subroutine plastic_dislotwin_dotState(Mp,T,instance,of)
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f_unrotated, &
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VacancyDiffusion, &
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rho_dip_distance, &
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v_cl, &
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tau
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v_cl, & !< climb velocity
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Gamma, & !< stacking fault energy
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tau, &
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sigma_cl, & !< climb stress
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b_d !< ratio of burgers vector to stacking fault width
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real(pReal), dimension(param(instance)%sum_N_sl) :: &
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dot_rho_dip_formation, &
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dot_rho_dip_climb, &
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@ -786,8 +807,17 @@ subroutine plastic_dislotwin_dotState(Mp,T,instance,of)
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if (dEq0(rho_dip_distance-rho_dip_distance_min(i))) then
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dot_rho_dip_climb(i) = 0.0_pReal
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else
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v_cl = 3.0_pReal*prm%mu*VacancyDiffusion*prm%atomicVolume(i) &
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/ (2.0_pReal*PI*kB*T*(rho_dip_distance+rho_dip_distance_min(i)))
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!@details: Refer: Argon & Moffat, Acta Metallurgica, Vol. 29, pg 293 to 299, 1981
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sigma_cl = dot_product(prm%n0_sl(1:3,i),matmul(Mp,prm%n0_sl(1:3,i)))
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if (prm%ExtendedDislocations) then
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Gamma = prm%SFE_0K + prm%dSFE_dT * T
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b_d = 24.0_pReal*PI*(1.0_pReal - prm%nu)/(2.0_pReal + prm%nu)* Gamma/(prm%mu*prm%b_sl(i))
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else
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b_d = 1.0_pReal
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endif
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v_cl = 2.0_pReal*prm%omega*b_d**2.0_pReal*exp(-prm%Qsd/(kB*T)) &
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* (exp(abs(sigma_cl)*prm%b_sl(i)**3.0_pReal/(kB*T)) - 1.0_pReal)
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dot_rho_dip_climb(i) = 4.0_pReal*v_cl*stt%rho_dip(i,of) &
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/ (rho_dip_distance-rho_dip_distance_min(i))
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endif
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