Presentation at nanospd 6 in metz in 2014
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Transcript of Presentation at nanospd 6 in metz in 2014
Department MTM
NANOSPD 2014 Metz
1
A subdivision model for CP Ti during the first pass
of ECAP at room temperature
Dep. of Materials Engineering, KU Leuven, Belgium
Xiaodong Guo, Marc Seefeldt
Department MTM
Content
2
Backgrounds
Modeling Strategy
Results & Discussions
Conclusion Future Plans
Department MTM
Backgrounds
3
Ti C Fe N H O
wt% Base 0.04 0.14 0.006 0.0015 0.36
Nano Titanium Implant®, produced in Timplant, Czech
∅ = 90°
𝛹 = 0°
𝑇 = 298𝐾
∆𝜀 = 1.15
𝜀 = 10−4/𝑠
ViNaT Project under FP7: Virtual NanoTitanium
Properties required for biomedical materials:
Biocompatibility
Non-Toxic
Strength
Ductility
Persistency
…
Nanosized Ti by ECAP can improve biocompatibility, strength, persistency while keeping the ductility
This subdivision model couples with VPSC, simulates a
grain’s (orientation) behavior during the first pass of
ECAP at room temperature. The effect of grain
subdivision on texture evolution will be the future work.
Department MTM
Modeling Strategy
4
Deformation Substructure
Prismatic, Basal, Pyramidal
Twins: type of reorientation bands
defect densities
Δε
microscopic mesoscopic
Deformation Texture
VPSC Model
(Simple Shear Mode)
orientations
Δε
Velocity
Gradient
Tensor
Dislocation
Elementary
Processes
macroscopicnanoscopic
)(s CRSS
)(w
Department MTM
Reorientation bands formation
5
Compression Direction
Dorothe′e Dorner, Yoshitaka Adachi, Kaneaki Tsuzaki, Scripta Materialia 57, 2007
Fe-3%Si
Compression to 36% strain
Room Temperature
Slip bands in grain A impose shear steps at grain boundary, then trigger microband groups
with periodic orientation change in grain C
How and where does the misorientation arise?
Department MTM
Reorientation bands formation
6
Prismatic slip bands in grain 1 impose shear on grain boundary, triggering twinning in grain 2
L. Wang, Y. Yang, P. Eisenlohr, T.R. Bieler, M.A. Crimp, D.E. Mason, Meta.& Mater. Trans. A, Vol 41A, 2010
Pure Titanium
Tension to 1.5% strain
Room Temperature
Department MTM
Graphical Scenario
7
∆𝛾 =𝑏
ℎ𝑐𝑟Primary dislocation slip bandsNo misorientation
Grain Boundary
Reorientation BandsHave misorientation with matrix
• Forest dislocations
• Mobile dislocations
• Slip band formation
• Excess shear at GB
• Shear transmitted into its neighbor
• Misorientation generated
• Growth of band tip by capturing
mobile dislocation
𝜔 = ∆𝛾
Department MTM
Forest Dislocations
8
• Three slip modes (Prismatic, Basal, Pyramidal) are considered;
• Edge and screw dislocations are considered;
• Vacancy assisted climb is neglected;
• Shear rates & specific Taylor factor for 3 slip modes are deduced from slip activities in VPSC
( i ) ( i )fs ( tot ) ( i )s
f s fs
dy
dt b
( i ) ( i )fe ( tot ) ( i )e
f e fe
dy
dt b
𝛽: Storage Coefficient, 𝛽 = 0.1 for current simulation
0
(i)(i)
sM
(i)
cs
c
:‘critical shear stress ratio’
Department MTM
Nucleation of Mobile Dislocations
9
‘ℎ’ : a minimum critical distance for FR source effectively generated
Slip band forms when a bunch of parallel primary slip planes undergo this process
(1) (2) (3)
Double Cross Slip event
Department MTM
Density of Mobile Dislocations
10
2
1( i ) ( i ) ( i )transfer ( j i )s s
eff eff fs
f
dnq( ) q( )
dt b b
hhCSeff cr
ffq s
w
CS
CSCSv
d
l
bPf 0
)1(
s
cr
CS
CShhv
h
l
bPf
cr 0
)2(exp
Cross-slip getting activated
Return to primary plane
𝑞(𝜏𝑒𝑓𝑓): A possibility coefficient indicating a screw dislocation undergoes a double cross slip event.
Yoshinaga’s Jog Pair cross slip model: for High SFE
* Marc Seefeldt, 2004* Yoshinaga, 1964
Nucleation site density for mobile dislocations
Breeding Coefficient
Nucleation Site Density of FR source
Department MTM
Density of Mobile Dislocations
11
)(
)()(
0
)()( 2i
e
i
me
i
es
i
transferi
ms
L
vL
dt
dn
dt
d
)(
)()(
0
)()( 2i
s
i
ms
i
se
i
transferi
me
L
vL
dt
dn
dt
d
Firstly generated from DCS Later increase from Loop expansion
b ⊥⊥
evev
sv
sveL
sL
Department MTM
Transmission & Growth of Reorientation Bands
12
sLa 2
crit
b
h
Slip Band:
Localised shear, but no misorientation with respect to matrix
Excess Shear:
Width:
Misorientation Band:
Realising a similar localised shear in another slip mode
crith
bShear Transmissed:
Transmission Factor: 100% now
sLa 2Width:
Terminating boundaries grow
• End stress at the tip
• Capturing mobile dislocations
• Attaching mobile dislocations
• Shift the end of the boundary’s tip
Department MTM
Results: Dislocation Density
13
- Prismatic and Basal slip modes have a similar forest dislocation density
- Excess dislocations depend on nucleation site densities
- Experimental value of 5 × 1014/m2 after one ECAP-C pass, see Gunderov et al. MSEA, 2013
Dislocation Density Nucleation Site Density
Department MTM
Cell & Fragment Size Prediction
14
* Gunderov et al., MSEA 2013
* T.R. Cass, Oxford, 1966
Mean Cell & Fragment Size
𝑑𝑐 =𝐾𝑐𝜌𝑡𝑜𝑡
𝑑𝑓 ≈𝐾𝑓
𝜃𝑖
0.0 0.1 0.2 0.3 0.4 0.5
0
1
2
3
4
5
Cell
Fragment
True Equivalent Strain(1)Si
ze o
f C
ell &
Fra
gmen
ts (𝜇𝑚
)
Department MTM 15
Mean Misorientation
0.0 0.2 0.4 0.6 0.8 1.0 1.22.0
2.5
3.0
3.5
4.0
4.5
5.0
5.5
6.0
Mean Misorientation
Me
an
Mis
orie
nta
tio
n(o
)
True Equivalent Strain(1)
Misorientation & Hardening
0
50
100
150
200
250
300
350
400
0 0.2 0.4 0.6 0.8 1 1.2
True Equivalent Strain (1)
Tru
e Eq
uiv
alen
t S
tres
s (M
Pa)
Simulated
Experimental from Simple Shear test
- Hardening due to
• Dislocation forest hardening: ∆𝜎𝑓 = 𝑀𝛼𝜌𝐺𝑏 𝜌 𝑡𝑜𝑡
• Long-range stress hardening due to mismatch stresses around FB triple junctions: ∆𝜎𝜔 = 𝑀𝛼𝜃𝐺𝜔
• Texture hardening due to the evolving average Taylor factor 𝑀
10
14
18
Mis
mat
ch S
tres
s (M
pa)
∆𝜎𝜔
Department MTM
Conclusion & Future Plans
16
We introduced a grain subdivision model for the first pass of ECAP of CP Ti at room
temperature. The generation of reorientation bands is triggered by the stimulation
of slip bands from neighboring grain. Defect densities, cell size and fragment
spacing, hardening behavior are simulated.
One future plan is to combine this subdivision model with plasticity model in order
to study the effect of grain subdivision on texture evolution.
A simple shear test for CP Ti is in process to study more detailed parameters like
evolution of cell and fragment size, transmission factor at grain boundaries and its
orientation dependence, texture evolution etc. which can provide useful
information to the ECAP deformation of metals.