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DICTRA and Diffusion Assessments
• Diffusion Mobility Assessment: Optimization• Simulation of Diffusion Controlled
Transformations
High Throughput Analysis of Multicomponent Multiphase Diffusion Data
March 27-28, 2003
What is needed to simulate multicomponent diffusion?
René-N4 René-N5
� �
40.370.083.022.160.055.062.081.141.562.2357.625.694.494.435.163.123.050.076.026.024.053.033.068.031.085.074.005.2427.066.025.031.045.017.036.055.057.7426.0280.033.849.225.891.993.821.367.1337.526.469.910.783.155.567.525.800.1737.1122.5351.4950.5143.4234.3483.3493.135.119
��������
��������
��������
��������
��������
��������
��������
��������
WTiTaNbMoCrCoAl
WTiTaNbMoCrCoAl
René-N4 (x10-14 m2/s) at 1293 °C
Diffusion matrix
�
Thermodynamics
����
�+L L
�+��+P+B2�+��
+P
�+��+B2
�+B2
�+B2+L
B2+L
�+P+B2
René-N4
Need efficient data storage
At each grid point for each time step for a given temperature profile.
Multicomponent Thermodynamics:Calphad Approach
Calculated phasediagram
Experimental phase diagramThermochemical data
Determine Gibbs EnergyG = f(x,T,P�
A B
TE
�
Liquid
�
Tem
pera
ture
CompositionA B
TE
�
Liquid
�
Tem
pera
ture
Composition
�
�
L
Gib
bs E
nerg
y
Composition
T<TE
G G G Gideal excess�� � �
0
Binaries Ternaries Quaternaries nth ordersystems
Diffusion Database Development� Inputs:
– Calphad Thermodynamics – Diffusion experiments (unary, binary, ternary systems)
• Tracer diffusivity, • Intrinsic diffusivity, • Interdiffusion coefficients/Marker motion
� Optimize value of mobilities, Mi , for all binaries consistent with available data– Composition and Temperature-dependent– Consistent with estimates of Metastable end members e.g., FCC W– Optimized using code, DICTRA (Parrot)
�Add terms if necessary to fit ternary data, etc. kjiijki xxxTB )(
kk RTMD �*
� � 1 and , whereexp �����
���
� �� �
�
iiiii
i MTcfQRTQ
RTMM
)()(1 1
0 TAxxTQxQn
p
n
qp
n
q
pqiqp
pipi � ��
� � �
���
Assessment of Diffusion Mobilities
Estimate MobilitySimulate diffusion processCompare experimental
and calculated D Adjust Mobility
Experimental diffusion data Mobility M=f (c,T) Calculate diffusion
Coefficients D = f(c,T)
Distance
Com
posi
tion
Diffusion profile � Diffusion Coefficient
Composition
Log
(Mob
ility)
T = 1150 °C
T = 1050 °C
T = 950 °C
Ni - Al
� � 1 and , whereexp �����
���
� �� �
�
iiiii
i MTcfQRTQ
RTMM
� �...)()( ,2,,��������ji
ijiji
ijiji
ijijij
iiii CccBccAccQcQc�
-15
-14.5
-14
-13.5
-13
-12.5
-12
0 0.05 0.1 0.15 0.2
log
D� (
m2 /s
)
Mole Fraction Al
1000°C
1050°C
1100°C
1250°C
Data from Yamamoto et. al. (1980)Assessment by Engström and Ågren (1996)
QFor a binary:
Assessment of Ni-W
-15.5
-15
-14.5
-14
-13.5
-13
-12.5
5.8 10-4 6 10-4 6.2 10-4 6.4 10-4 6.6 10-4 6.8 10-4 7 10-4 7.2 10-4 7.4 10-4
x(w)=.017
x(w)=.053
x(w)=.092
Log
D* (F
CC
,Ni)
(m2 /s
)
(1/Temperature) (K)
Ni-1.7W (at.%)
Ni-5.3W (at.%)
Ni-9.2W (at.%)
1340 1290 1242 1197 1155 1116 107813941451Temperature ( oC)
-16
-15.5
-15
-14.5
-14
-13.5
6.2 10-4 6.4 10-4 6.6 10-4 6.8 10-4 7 10-4 7.2 10-4 7.4 10-4
x(w)=.017
x(w)=0.053
w(w)=.092
Log
D*
(FC
C,W
) (m
2 /s)
(1/Temperature) (K)
Ni-1.7 W
Ni-5.3 W
Ni-9.2 W
1340 1290 1242 1197 1155 1116 1078Temperature ( oC)
-18
-17
-16
-15
-14
-13
0 0.02 0.04 0.06 0.08 0.1
Log
D (I
nter
diffu
sion
) m2 /s
Mass Fraction W
900 oC
1100 oC
1000 oC
1200 oC
1300 oC
WNiNiWNi
WNiW
NiNiNiNi AxxQxQxQ ,0*
����
WNiWWNi
WWW
NiWNiW AxxQxQxQ ,0*
����
Activation energies in the fcc phase
Self activation energiesOptimized parameters
Trac
er d
iffus
ivity
dat
aInterdiffusion data
Mobility Description Ni-W
• FCC_A1: Mobility of Ni– MQ(FCC_A1,NI:VA;0) = -28700+69.8*T– MQ(FCC_A1,W:VA;0) = V1+R*T*LN(V2)– MQ(FCC_A1,NI,W:VA;0) = V3+V4*T
• FCC_A1: Mobility of W– MQ(FCC_A1,NI:VA;0) = V5+R*T*LN(V6)– MQ(FCC_A1,W:VA;0) = V7+R*T*LN(V8)– MQ(FCC_A1,NI,W:VA;0) = V9+V10*T
Ni-W : DOP file• $$ Data from Momma et al, J. Japan Inst. Metals, 28 (1964) 197-200.• $$ Measured diffusivity in Ni-W alloys with Ni-63 and W-185
• TABLE_HEAD 655• CREATE_NEW_EQ @@, 0• CHANGE_STATUS COMP Ni,W=ENT• CHANGE_STATUS PHASE FCC_A1=ENT 1• S-COND X(W)=.017• S-COND P=101325 N=1 T=@1• EXPERIMENT LOGDT(FCC,NI)=@2:.05• TABLE_VALUES
• $$Ni-5W• $$ Temp(K) Log(DT)• 1668 -12.57675413• 1623 -12.82973828• 1579 -13.07058107• 1530 -13.49485002• 1478 -13.8827287• 1433 -14.1739252• 1369 -14.74714697• TABLE_END
Ni-W Interdiffusion: DOP file• TABLE_HEAD 325• CREATE_NEW @@,0• CHANGE_STATUS COMP NI,W=ENT• CHANGE_STATUS PHASE FCC_A1=ENT 1• S-COND w(W)=@1• S-COND N=1 P=101325 T=1273• EXPERIMENT LOGDC(FCC,W,W,NI)=@2:.1• TABLE_VALUES
• $$ 1000 C• $$ w(W) logD• 0.00E+00 -16.18708664• 5.00E-03 -16.15490196• 1.00E-02 -16.09691001• 1.50E-02 -16.04575749• 2.00E-02 -16.00877392• :• 9.00E-02 -15.76955108• 9.50E-02 -15.75696195• 1.00E-01 -15.74472749• TABLE_END
Optimization= = OPTIMIZING VARIABLES = =AVAILABLE VARIABLES ARE V1 TO V50
3.15926361E+00-9.70151891E+04-9.70151891E+04-9.70248906E+4V9
1.19007328E+012.18664263E-042.18664263E-042.18664263E-04V8
1.02636444E+01-3.11392279E+05-3.11392279E+05-4.11423418E+5V7
4.48683550E-012.79975794E-052.79975794E-052.80004792E-05V6
1.95885497E-02-2.82130025E+05-2.82130025E+05-2.82130025E+05V5
1.44758232E+001.75718445E+051.75718445E+051.7573601E+05V3
6.01374702E+004.78304593E-044.78304593E-044.78352423E-04V2
3.85216307E-01-6.28250129E+05-6.28250129E+05-6.28250129E+05V1
Rel. Stand. DevScaling FactorSTART ValueValue
NUMBER OF OPTIMIZING VARIABLES: 8ALL OTHER VARIABLES ARE FIX WITH THE VALUE ZEROTHE SUM OF SQUARES HAS CHANGED FROM 5.19453290E+02 TO 5.1944291E+02DEGREES OF FREEDOM 109. REDUCED SUM OF SQUARES 4.76554396E+00
Optimization Results: Tracer Diffusivity
Difference/ Error
DifferenceAcceptable error
Optimized Value
Experimental Quantity
0.94404.72E-25.0E-02-14.70LOGDT(FCC_A1,NI)=-14.75
-0.642-3.2E-25.0E-02-14.21LOGDT(FCC_A1,NI)=-14.17
-3.2E-2-1.59E-35.0E-02-13.88LOGDT(FCC_A1,NI)=-13.88
-0.826-4.13E-25.0E-02-13.54LOGDT(FCC_A1,NI)=-13.49
-3.170-0.15855.0E-02-13.23LOGDT(FCC_A1,NI)=-13.07
-2.788-0.13945.0E-02-12.97LOGDT(FCC_A1,NI)=-12.83
-2.814-0.14075.0E-02-12.72LOGDT(FCC_A1,NI)=-12.57
Extrapolation to Higher Order Systems
AlAlAlCr
CrAlNi
NiAlAl
AlAlCrCr
CrCrNi
NiCrCr
AlCrNiNiCrAlNiCrNi
NiCrNiAl
AlNiCr
CrNiNi
NiNiNi
AlAlAlCr
CrAlAl
AlAlCrCr
CrCrCr
AlAlAlNi
NiAlAl
AlAlNiNi
NiNiNi
CrCrCrNi
NiCrCr
CrNiNiCrNiCr
CrNiNi
NiNiNi
xQxQxQQ
xQxQxQQ
xxxBxxAxQxQxQQ
xQxQQ
xQxQQ
xQxQQ
xQxQQ
xQxQQ
xxAxQxQQ
����
����
������
���
���
���
���
���
����
Ternaryinteraction
Binaryinteraction
Ni-Cr
Ni-Al
Cr-Al
Ni-Cr-Al
Examples of Fits for Binary InteractionsNi-Al-Cr-Co-Hf-Nb-Mo-Re-Ta-Ti-W
-17.5
-17
-16.5
-16
-15.5
-15
-14.5
-14
0 0.02 0.04 0.06 0.08 0.1
Ti
Ta
W
Re
-14.5
-14
-13.5
-13
-12.5
-12
0 20 40 60 80 100
Atomic Percent Ni
1400 oC
1325 oC
1250 oC
1200 oC
1160 oC
Ni-Co Interdiffusion
Log
(D) m
2 /s
Data from Ustad and Sorum, Phys. Stat. Sol. A 285 (1973) 285.Calculated
Log
(D) m
2 /sWeight Fraction
Interdiffusion with Ni
Data from Karunaratne et al., Mater. Sci. Eng., A281 (2000) 229.Data from Komai et al., Acta. Mater., 46, (1998) 4443.
T = 1000 oC
Previous assessments: Ni-Al-Cr Engström and Ågren, Z. Metallkd. 87 (1996) 92.
Ni-Al-Ti Matan et al., Acta mater., 46 (1998) 4587.
Current assessments: Ni-Co, Ni-Hf,Ni-Mo, Ni-Nb,Ni-Re, Ni-Ta, Ni-Ti,Ni-W, Co-Cr, Co-MoC. E. Campbell, W. J. Boettinger, U. R. Kattner, Acta Mat, 50 (2002) 775
Diffusion Correlation at Melting Temperature
18�
�
MRTQ
� For a pure metal
13.614.5-235350207619522504hcpHf
16.816.8-311420223022293695bccW
21.734.3-25690014219001946hcpTi
20.922.8-268253154014163296bccTa
16.314.9-382950283030843459hcpRe
28.225.4-274328117013002468bccNb
20.017.6-254975153017402895bccMo
19.519.5-286175176817681770hcpCo
32.919.2-23500086014752133bccCr
18.418.3-142000931933.5933.5fccAl
20.020.0-287000172517281728fccNi
-Q/RTM (fcc) (Kaufman)
-Q/RTM(fcc)
(SGTE)
ActivationEnergy (J/mole)
TM, K (fcc)(Kaufman)
TM, K (fcc)
TM, KCrystal Structure
Element
Comparison with Ni-Co-Cr-Mo Data at 1300 oC*
Diffusion coefficients calculated using the different thermodynamic databases and a fixed diffusion mobility database.
-2.27
-4.69
7.93
7.58
7.53
9.22
9.78
10.3
5.03
8.59
9.25
9.74
10.0
10.3
10.6
10.7
-2.37-1.7 ± 0.37.623.96.5
-2.26-2.0 ± 0.46.23.722.2
7.473.3 ± 0.77.116.225.9
6.834.2 ± 0.87.121.425.8
7.013.7 ±0.77.119.825.8
8.964.8 ±1.06.67.426.3
9.616.0 ± 1.26.44.426.5
10.38.9 ± 1.86.61.726.8
4.946.8 ± 1.4 7.747.93.2
8.46.4 ± 1.3 7.727.16.4
8.956.9 ± 1.47.426.210.8
9.358.2 ± 1.67.425.815.2
9.5610.1 ± 2.07.225.618.4
9.859.9 ± 2.07.425.020.8
10.19.7 ± 1.97.424.522.7
10.27.5±1.57.424.124.2
CalculatedNIST Thermotech
Measured Mo CoCr
Composition (Atomic Percent)Ni = balance
NiCrCrD~
NiCoCoD~
CoNiCrD~
smDNiij
21410�
~
†Heaney and Dayananda Metall. Trans. A, 1986, 17A, 983.
Co-Nb at 1100 C for 1000 h
0
0.01
0.02
0.03
0.04
0.05
-400 -350 -300 -250 -200 -150 -100 -50 0
GE Data (Nb)
DICTRA 1
DICTRA 2
Mol
e Fr
actio
n N
b
Distance (�m)
T = 1100 oC
Mobility of Nb in fcc Co not evaluated in diffusion database
0
0.2
0.4
0.6
0.8
1
-400 -300 -200 -100 0 100 200 300 400
Nb: GE Data
DICTRA: FCC phase
Mol
e Fr
actio
n N
b
Distance (�m)
T = 1100 oC
A+B*erf[(x-C)/(4Dt)^0.5]A = 0.026B = 0.025C = -47 �m
D = 2.13 x10-15 m2/s
FCC
smNbxDFCCCoMo
2141026.1]1.)([~�
���
Based on this result re-evaluate mobility parameter(MQ(FCC_A1&Nb,Co:V;0)] = -275333+R*T*LN(7.6071E-05)
smNbxDFCCCoMo
2151023.2]1.)([~�
���
smNbxDFCCCoMo
2141026.1]1.)([~�
���
(MQ(FCC_A1&Nb,Co:V;0) =-255333+R*T*LN(7.6071E-05)
DICTRA*Diffusion Controlled Transformations
• 1-D finite difference solution to diffusion equations• Variable self-adjusting mesh• Volume fixed reference frame• Vacancy and interstitial diffusion• Can solve problems with planar layers of
– single phase material – multiphase material (matrix and dispersed phase)
• describes suitable average concentration of multiphase mixture• assumes diffusion only in the matrix phase• assumes phase fraction of dispersed phase is small• assumes the composition of the dispersed phase is given by
local equilibrium for average concentration* from the Division of Physical Metallurgy, The Royal Institute of Technology, Stockholm, Sweden.
René-N4/René-N5 at 1293 °C for 100 h
0
0.02
0.04
0.06
0.08
0.1
0.12
-1000 -500 0 500 1000
Mas
s Fr
actio
n
Distance (�m)
Cr
Co
W
Ta
Al
TiMo
Re
HfNb
� Databases used– Thermodynamics:
Thermotech– Diffusion mobilities:
NIST Ni-mob
René-N4 René-N5
� �
6.35 mm 6.35 mm
Double geometric grid: 200 points
Experimental work performed by T. Hansen, P. Merewether, B. Mueller, Howmet Corporation, Whitehall, MI.
Porosity Prediction
-0.1
-0.05
0
0.05
0.1
-0.0004 -0.0002 0 0.0002 0.0004
Distance (m)
� �zJVa�
��
10 h
100 h
Rene-N4 Rene-N5
200 �m
N4 N5
Back scatter image; 100 h
0- +Predicted position for
maximum pore formationMaximum gives location of pore formation.
René-88/IN-718; 1000 h at 1150 °C
0
0.05
0.1
0.15
0.2
-500 0 500 1000
Mas
s Fr
actio
n
Distance (�m)
Cr
Co
Fe
Nb
Mo
TiAl
W
At 1150 °C equilibrium phase fractions
• René-88: f�
= 1• IN-718: f
�= 1
René-88 IN-100
4 mm 4 mm
Experimental data from J. C. Zhao, GE-CRD, Schenectady, NY
Applications of Diffusion Database
• Prediction of �� precipitation: GE-AIM program: – Composition and volume of ��� is key to predicting many of mechanical properties
• Back diffusion during solidification: Howmet
• Protective coatings: Howmet• B2/Rene-N5 diffusion simulations
•B2 layer dissolves, forms �� layer
• Heat treatment optimization: avoiding incipient melting.
Transient Liquid Phase Bonding
T = 1315 °C; Time 900 sNi-10.3Al/Ni-10B/Ni-10.3Al
0.00 0.04 0.08 0.120.00
0.05
0.10
0.15
0.20
LL ��������
L��� �����
L ���
Mole Fraction Al
T = 1315 °C
50 �m
Ni-Al Ni-Al
�
L� ���� ���
Thermodynamics &Diffusion mobilities
Mol
e Fr
actio
n B
microstructureevolution
0
10
20
30
40
50
60
0 10 20 30 40 50 60
Rapid quench experimentsSlow cooled experimentsPrediction after isothermal holdPrediction with cooling
�Time (s)
Join
t wid
th (�
m)
0.00 0.02 0.04 0.06 0.08 0.10 0.120.000
0.002
0.004
0.006
0.008
0.010
Mole Fraction Al
Mol
e Fr
actio
n B
L + �
���
�
t = 1 st = 900 s
t = 1800 s
t = 3600 s
L ���� �
L �
L �
� ��� �
Time = 0 s
Time = 1 s
Time = 900 s
Time = 3600 s
C. E. Campbell and W. J. Boettinger, Metall. Materials Trans., 31A, 2000, 2835.
Heat Treatment Optimization:Solidification of Ni-11Al-4.5Ta (at.%)
L
L�
�����’9.5�m
t = 0 s
0 s < t < 4 s
t > 4 s
• Microstructure evolution
Solidification assumptions
• Cooling rate = 8K/s; • �/2 = 9.5 �m
0
0.05
0.1
0.15
0.2
0.25
0 0.05 0.1 0.15 0.2
Mol
e Fr
actio
n Al
Mole Fraction Ta
�'
B2
�
Ni3Ta�
DICTRA solidification path�' is a dispersed phase in �
T�= 8 K/s
Solidification Path
Thermodynamics: Ni-Data, ThermotechDiffusion: Ni-Mob, NIST
Incipient Melting Temperature
1635
1640
1645
1650
1655
1660
1665
0.0001 0.001 0.01 0.1 1 10 100 1000
(K/s)-1
Inci
pien
t Mel
ting
Tem
pera
ture
(K)
1000 (K/s) 100 (K/s)
1 (K/s) 0.01 (K/s)
Ni-11Al-4.5Ta (at.%)
Simulation Setup• Used composition and phase fractions from solidification calculation.
• Assume linear heating rates beginning at 800 K
• Assume �’ fraction is in equilibrium with � matrix at each grid point.
• Assume incipient melting occurs at the center between dendrites.
��
10 (K/s)
T�1
TE
TSolidus
Tsolvus (�/�’)
Heating Rate 100 K/s, TIM= 1655 K
Optimized Heat Treatment
0
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0 2 4 6 8
Distance (�m)
Phas
e Fr
actio
n �’
t = 0 s
800 s
855 s
1000 s
1200 s800
1000
1200
1400
1600
0 200 400 600 800 1000 1200
Tem
pera
ture
(K)
Time (s)
For Ni-11Al-4.5Ta alloy solidified at 8 K/s
� Heat from 800 K to 1655 K at 1 K/s
� Hold at 1655 K until t = 1325 s (t = 470 s)
Homogenous microstructure
Next step: Multicomponent simulation, optimization, experimental verification