rsf AC ThermDatabase PDF - RWTH Aachen...
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Thermodynamische Datenbanken
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1
R. Schmid-Fetzer
Contributions byJ. Klingbeil, H. Cordes, F. Goesmann, K. Zeng, K. Bhanumurthy, A. Pisch, R. Wenzel, G. Fischer,
D. Kevorkov, J. Gröbner, T. Studnitzky, B. Onderka, S.M. Schnurre, D. Mirkovic, I. Chumak
supported by the German Research Council (DFG), Volkswagenstiftung,Federal Ministry of Education & Research (BMBF), European Union (EU)
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Outline2
Thermodynamic databasesExample: Mg alloy databaseTernary parametersKey experimentsQuality problems with binary systems / software
ApplicationsDeveloping creep resistant Mg alloysSolderingAl-alloy solidification, microsegregation
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Mg database: Binary systems3
Ag-Al Ag-Ca Ag-Ce Ag-Cu Ag-Gd Ag-Li Ag-Mg Ag-Mn Ag-Nd Ag-Sc Ag-Si Ag-Sr Ag-Y Ag-Zn Ag-ZrAl-Ca Al-Ce Al-Cu Al-Gd Al-Li Al-Mg Al-Mn Al-Nd Al-Sc Al-Si Al-Sr Al-Y Al-Zn Al-ZrCa-Ce Ca-Cu Ca-Gd Ca-Li Ca-Mg Ca-Mn Ca-Nd Ca-Sc Ca-Si Ca-Sr Ca-Y Ca-Zn Ca-ZrCe-Cu Ce-Gd Ce-Li Ce-Mg Ce-Mn Ce-Nd Ce-Sc Ce-Si Ce-Sr Ce-Y Ce-Zn Ce-ZrCu-Gd Cu-Li Cu-Mg Cu-Mn Cu-Nd Cu-Sc Cu-Si Cu-Sr Cu-Y Cu-Zn Cu-ZrGd-Li Gd-Mg Gd-Mn Gd-Nd Gd-Sc Gd-Si Gd-Sr Gd-Y Gd-Zn Gd-ZrLi-Mg Li-Mn Li-Nd Li-Sc Li-Si Li-Sr Li-Y Li-Zn Li-ZrMg-Mn Mg-Nd Mg-Sc Mg-Si Mg-Sr Mg-Y Mg-Zn Mg-ZrMn-Nd Mn-Sc Mn-Si Mn-Sr Mn-Y Mn-Zn Mn-ZrNd-Sc Nd-Si Nd-Sr Nd-Y Nd-Zn Nd-ZrSc-Si Sc-Sr Sc-Y Sc-Zn Sc-ZrSi-Sr Si-Y Si-Zn Si-ZrSr-Y Sr-Zn Sr-ZrY-Zn Y-ZrZn-Zr 16 components:
120 binary systems
41 from literature + checked + adapted37 own modeling + experiments42 missing systems
120216
=⎟⎟⎠
⎞⎜⎜⎝
⎛
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Mg database: Ternary systems4
Al-Ca-Li Al-Ca-Si Al-Ce-Si Al-Ca-MgAl-Ca-Si Al-Ce-Mg Al-Cu-Li Al-Cu-Mg Al-Cu-Nd
Al-Cu-Si Al-Cu-Zn Al-Gd-Mg Al-Li-Mg Al-Li-Mn Al-Li-Si Al-Mg-Mn Al-Mg-Sc Al-Mg-Si Al-Mg-Y Al-Mg-Zn Al-Mn-Sc
Al-Mn-Si Al-Si-Y Al-Si-Zn Ca-Li-Mg Ca-Li-Si Ca-Mg-Si Ce-Li-MgCe-Mg-Mn Ce-Mg-Sc Ce-Mn-Sc Cu-Li-Mg Cu-Mg-Si Cu-Mg-Y
Cu-Mg-Zn Gd-Li-Mg Gd-Mg-Mn Gd-Mg-Sc Gd-Mn-Sc Li-Mg-Si Li-Mg-Zn Mg-Mn-Sc Mg-Mn-Y Mg-Mn-Zr Mg-Y-Zr Mn-Sc-Y Mn-Y-Zr
Exper.+Modell. Literature&Check Plausibility-Check
Ag-Al Ag-Ca Ag-Ce Ag-Cu Ag-Gd Ag-Li Ag-Mg Ag-Mn Ag-Nd Ag-Sc Ag-Si Ag-Sr Ag-Y Ag-Zn Ag-ZrAl-Ca Al-Ce Al-Cu Al-Gd Al-Li Al-Mg Al-Mn Al-Nd Al-Sc Al-Si Al-Sr Al-Y Al-Zn Al-ZrCa-Ce Ca-Cu Ca-Gd Ca-Li Ca-Mg Ca-Mn Ca-Nd Ca-Sc Ca-Si Ca-Sr Ca-Y Ca-Zn Ca-ZrCe-Cu Ce-Gd Ce-Li Ce-Mg Ce-Mn Ce-Nd Ce-Sc Ce-Si Ce-Sr Ce-Y Ce-Zn Ce-ZrCu-Gd Cu-Li Cu-Mg Cu-Mn Cu-Nd Cu-Sc Cu-Si Cu-Sr Cu-Y Cu-Zn Cu-ZrGd-Li Gd-Mg Gd-Mn Gd-Nd Gd-Sc Gd-Si Gd-Sr Gd-Y Gd-Zn Gd-ZrLi-Mg Li-Mn Li-Nd Li-Sc Li-Si Li-Sr Li-Y Li-Zn Li-ZrMg-Mn Mg-Nd Mg-Sc Mg-Si Mg-Sr Mg-Y Mg-Zn Mg-ZrMn-Nd Mn-Sc Mn-Si Mn-Sr Mn-Y Mn-Zn Mn-ZrNd-Sc Nd-Si Nd-Sr Nd-Y Nd-Zn Nd-ZrSc-Si Sc-Sr Sc-Y Sc-Zn Sc-ZrSi-Sr Si-Y Si-Zn Si-ZrSr-Y Sr-Zn Sr-ZrY-Zn Y-ZrZn-Zr
possible ternaries
560316
=⎟⎟⎠
⎞⎜⎜⎝
⎛
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Mg database: multicomponent systems5
Ag-Al Ag-Ca Ag-Ce Ag-Cu Ag-Gd Ag-Li Ag-Mg Ag-Mn Ag-Nd Ag-Sc Ag-Si Ag-Sr Ag-Y Ag-Zn Ag-ZrAl-Ca Al-Ce Al-Cu Al-Gd Al-Li Al-Mg Al-Mn Al-Nd Al-Sc Al-Si Al-Sr Al-Y Al-Zn Al-ZrCa-Ce Ca-Cu Ca-Gd Ca-Li Ca-Mg Ca-Mn Ca-Nd Ca-Sc Ca-Si Ca-Sr Ca-Y Ca-Zn Ca-ZrCe-Cu Ce-Gd Ce-Li Ce-Mg Ce-Mn Ce-Nd Ce-Sc Ce-Si Ce-Sr Ce-Y Ce-Zn Ce-ZrCu-Gd Cu-Li Cu-Mg Cu-Mn Cu-Nd Cu-Sc Cu-Si Cu-Sr Cu-Y Cu-Zn Cu-ZrGd-Li Gd-Mg Gd-Mn Gd-Nd Gd-Sc Gd-Si Gd-Sr Gd-Y Gd-Zn Gd-ZrLi-Mg Li-Mn Li-Nd Li-Sc Li-Si Li-Sr Li-Y Li-Zn Li-ZrMg-Mn Mg-Nd Mg-Sc Mg-Si Mg-Sr Mg-Y Mg-Zn Mg-ZrMn-Nd Mn-Sc Mn-Si Mn-Sr Mn-Y Mn-Zn Mn-ZrNd-Sc Nd-Si Nd-Sr Nd-Y Nd-Zn Nd-ZrSc-Si Sc-Sr Sc-Y Sc-Zn Sc-ZrSi-Sr Si-Y Si-Zn Si-ZrSr-Y Sr-Zn Sr-ZrY-Zn Y-ZrZn-Zr
multi-component
MgMg
Mg
Si
Al
Li
RE
Ca
Si
Al
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Building of multicomponent systems6
Gibbs energy dataSystem
• ExtrapolationQuaternary& higher
• Ternary solid phases?• Extrapolation for solution phases,careful with ternary parameters
Ternary
• Thorough assessment neededBinary
• SGTE data, 1991 DinsdaleUnary
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Key experiments7
Sample selection• Calculated important reactions
Sample preparation• Levitation Melting• Arc Melting• Electron Beam Melting• Reaction Sintering
Sample analysis• Calorimetry (Calvet-DSC, drop)• Thermal Analysis (DTA, STA)• X-ray Diffractometry (XRD, 25-1500°C)• Electron Microscopy (SEM/EDX/WDX)• Metallography, Optical Microscopy
Alloysample
Ta capsule
Calorimetry
500 600 700 800-2.0
-1.5
-1.0
-0.5
0.0
0.5
1.0
1.5
primaryeutectic
Hea
t flo
w in
W/g
Temperature in °C
5
2 4 6 8400
600
800
1000
1200
Al 90Ce 0Si 10
Al 90Ce 10Si 0
U11
E1
E2
τ1 + (Al)
τ1 + τ2 + (Al)
L + τ2 + (Al)
L + (Al)
Al11Ce3 (l)+ τ1 + (Al) τ2 + (Al) + (Si)
L + τ1 +Al11Ce3(l)
L + Al11Ce3(l)
L + τ1
cooling; strong peak heating; strong peak cooling; weak peak heating; weak peak
Tem
pera
ture
, °C
Si, at.%
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Al-Ce-Si8
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Thermodynamic calculation confirms:
τ1 primary, τ2 peritectic formation (transition reaction)Al90 at.% Al
Si
Ce
τ1τ2(Al)
As-cast, 870 h at 570°C
20 40 60
400
600
800
1000
1200
1400
1600
Al 80Ce 20Si 0
Al 0Ce 20Si 80
U6
U11
P2 653°C
E2 573°C E1
L + (Si) + τ2
(Si) + τ2+ τ1
(Al) + (Si) + τ2
(Al) + τ2+ τ1
(Al) + Al11Ce3(l)+ τ1
L + Al11Ce3(h)
L + Al11Ce3(l)+ τ1
L + τ1L + (Si)+ τ1
L
cooling; strong peak heating; strong peak cooling; weak peak heating; weak peak
Tem
pera
ture
, °C
Al, at.%
20 at.% Ce constant9
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20 at.% Ce
Si
Ce
Sample 9
9
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Impact of ternary parameters10
Hg
Bi Sn
extrapolated from binaries,
no ternary parameter, L=0
Binary excess Gibbs energy:EGbin = L xA xB
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Impact of ternary parameters11
Ternary excess Gibbs energy:EGtern = L xA xB xC
aC = xC along the section xC = 0.5Because RT ln γC = L xA xB (1-2 xC)
Careful with ternary L-parameters ! Fitting tool for phase diagrams? - Check impact on activities !
Problems using first-generation software12
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• Software does not always find stable phase equilibria
• User may not know all the initial values
• Phase diagrams differ for given thermodynamic description
Reliability problem:
Global Gibbs energy minimum not found automatically
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Y. Austin Chang, Shuanglin Chen, Fan Zhang, Xinyan Yan, Fanyou Xie , Rainer Schmid-Fetzer, W. Alan Oates: Progr. Mater. Science, 49 (2004) 313-345
Problems using first-generation software13
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Software problem
Assessment problem1. Inverted miscibility gap
2. Low-T phases stable again at high-T
3. Ordered phases overlooked
Calculated constrained phase diagrams (e.g. metastable Fcc) often do not make sense.
Published assessments contain errors
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Inverted miscibility gap: Si-Ta14
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Calculated by [89Vah]Si Ta
Error detected by Pandat
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More examples:Co-Mo [99Dav], Si-W [89Vah], Al-Mo [97Sau], Al-W [98Ans], Al-N [98Ans], Fe-Si [98Ans], Sn-Zr [98Ans], Sn-Ti [98Ans]: Temp < 3000 K in most of these cases.
Sn-Zr
Low-T phases stable again at High-T: Co-Si15
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More examples:Nb-C [97Hua], Mo-C[88Ans], Fe-C [85Gus], Ni-C [87Gab], Al-Co [98Dup], Cr-Ta [93Cup], Ni-Ti [96Bel].
Calculated diagram by [92Cho] Error detected by Pandat
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Error detected by Pandat
Ordered phases overlooked: Al-Nb16
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Other example: Fe-Ta [93Coe]
Calculated diagram by [98Ans]
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Terminal solution reappears: Mg-Sn17
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Calculated diagram [1993Frie]J. Chim. Phys. (1993) 90, 181-187
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Error detected by PandatT[
C]
X[SN]
0
100
200
300
400
500
600
700
800
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0SNMG
0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 10
100
200
300
400
500
600
700
800
X[SN]
T[C
]
hcp
Mg Sn
L
hcp
hcp : regular solution
L°Mg,Sn= - 43007.6 - 4.05666*T;
L-parameter is too negative.
hcp
L
Mg Sn
Calculated by [93Dup]
500
1500
2500
3500
0 0.2 0.4 0.6 0.8 1
Mol. fracn. Ta
Tem
p. /
K
Liquid
Bcc BccCr2Ta_HT
Cr2Ta_LT
Constrained Phase diagram:Metastable diagram (no Liquid)calculated by Pandat using the same parameters of [93Dup]
500
1500
2500
3500
0 0.2 0.4 0.6 0.8 1
Mol. fracn. Ta
Tem
p. /
K
Cr2Ta_LT
Cr2Ta_LT
Cr2
Ta_H
T
Bcc
Bcc
Improbable Constrained Phase Diagram: Cr-Ta18
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Ordered LT stable at high T
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500
1500
2500
3500
0 0.2 0.4 0.6 0.8 1
Mol. fracn. Ta
Tem
p. /
K
Liquid
Cr2Ta_HT
Cr2Ta_LT
BccBcc
Constrained Phase Diagram: Cr-Ta19
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Calculated by [2001Zha]
Improved modeling: C15 (LT) & C14 (HT) phases using
Cluster Site Approximation (CSA) with fewer parameters [2001Zha]
Metstable diagram (no Liquid)calculated by [2001Zha]
500
1500
2500
3500
0 0.2 0.4 0.6 0.8 1Mol. fracn. Ta
Tem
p. /
K
Bcc
Cr2Ta_HT
Cr2Ta_LT
[2001Zha] F. Zhang, S.-L. Chen, Y. A. Chang and W. A. Oates, “An Improved Approach for Obtaining Thermodynamic Descriptions of Intermetallic Phases: Application to the Cr-Ta System”, Intermetallics, 2001, 9, 1079-1083.
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Problems using first-generation software20
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These mistakes have been made when the desired answers are known (the experimental binary phase diagrams).
How can we rely on calculations carried out this way when the answer is not known(multicomponent phase diagrams)?
351 binaries
2925 ternaries
17550 quaternaries….
Example:
27 elements
(COST database)
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Second-generation: Pandat21
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No user knowledge on demixing or ordering required.
No initial values required.
Finds automatically the correct phase diagram given a thermodynamic description.
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T[C]
X[ZN]
0
100
200
300
400
500
600
700
800
900
1000
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8
Al-Mg-Cu-Zn-Mn-Si with xMg = xCu = xMn = xSi = 0.0522
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L
L+β-AlMnSi
L+Mn11Si19
fcc1+fcc2+(Si)+σ+τ+Al4Mn
L+β-AlMnSi+δ-AlMnSi
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Outline23
Calphad method
Thermodynamic databasesExample: Mg alloy databaseTernary parametersKey experimentsQuality problems with binary systems
ApplicationsDeveloping creep resistant Mg alloysSolderingAl-alloy solidification, microsegregation
ADAMIS24
Elements: Ag, Bi, Cu, In, Sb, Sn, Zn, Pb
Thermodynamic Assessment
Surface tension and viscosity
Alloy Database for Micro-Solders
X. J. Liu, I. Ohnuma, R.Kainuma, K. Ishida: Tohoku University, Japan
S. L. Chen and Y. A. Chang: CompuTherm & University of Wisconsin, USA
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ADAMIS - - - - - - - - - - PandatPanEngine
25
Phase diagram calculation
Liquidus projection ($ 3 components)
Solidification simulationScheil, equilibrium
Surface tension and viscosity calculation(ternary contours)
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Surface Tension and Viscosityat Constant Composition
26
Sn-X Candidate Solders (mostly eutectic composition)
Surface Tension Viscosity
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Viscosity Contour27
Liquid Sn-Sb-BiAlloys at 900 K
X[SB]
X[BI]
0.0
0.2
0.3
0.5
0.7
0.9
0.0 0.2 0.4 0.6 0.8 1.00 0.2 0.4 0.6 0.8 10
0.2
0.4
0.6
0.8
1
X[BI]
X[SB
]
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
0.85mPas
0.9
0.95
1.0
1.051.11.151.21.251.3
Sb
BiSn
0.951.0
0.9
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Surface Tension and Viscosity Contours28
Liquid Sn-Cu-Ag alloys at 1000 °C
X[CU]
X[AG]
0.00
0.09
0.17
0.26
0.35
0.43
0.52
0.61
0.69
0.78
0.87
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.00 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 10
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
1
X[AG]
X[CU
]
0.8
1.0
1.21.4
1.6
Sn Ag
Cu
X[CU]
X[AG]
0.00
0.09
0.17
0.26
0.35
0.43
0.52
0.61
0.69
0.78
0.87
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.00 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 10
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
1
X[AG]
X[CU
]
550
600650
700750
800850
900950
1000
1050
1100
Sn Ag
Cu
550
600650
700750
800850
900950
1000
1050
1100
Sn Ag
Cu
550
600650
700750
800850
900950
1000
1050
1100
Sn Ag
Cu
Surface Tension Viscosity
mN/m mPa.s
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Surface Tension σ29
J. A. V. Butler, Proc. Roy. Soc.A, A135 (1935) 348-375
K. S. Yeum, R. Speiser and D. R. Poirier, Metall. Trans.B, 20B(1989) 693-703
T. Tanaka and I. Iida, Steel Research, 65 (1994)p. 21.
Extrapolation by knowledge of excess Gibbs energy Gxs
b = 1.091 for close-packed lattice
β = 0.83 for liquid metalsxsi
xsi GG β=*
3/23/1ii VbNS =
Partial excess Gibbs energies:
σi surface tension of pure liquid (i),
Si molar surface area in a monolayer of pure liquid (i)
ai activity of (i) in bulk alloy
ai* activity of (i) in "surface phase * " i
i
ii a
aSRT *
ln+=σσ
i = 1…c components
11
* =∑=
c
iix
( i = 1...c )
Solve these c+1 equations for the c+1 unknowns σ and xi*
( )),(),(1ln **
ixs
iixs
iii
i
ii xTGxTG
Sxx
SRT
−++= βσσ
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Viscosity η30
H. Eyring, J. Chem. Phys., 4 (1936) 283-291
S. Seetharaman and D. Sichen, Metall. Mater. Trans. B, 25B (1993) 589-595
⎟⎟⎠
⎞⎜⎜⎝
⎛ ∆=
RTG
MhN #
expρηhN = 3.99 . 10-10 Js/mol
∑= ii MxM∑= iix ρρ ρi density of pure (i)
Mi atomic mass of pure (i)∆G# Gibbs energy of activation
Extrapolation by knowledge of excess Gibbs energy Gxs
∆Gi# = f(T) Gibbs energy of activation of pure (i)
( )∑∑ ∑ +++∆=∆<
ixs
iiji
jiii xTGxxRTxxRTGxG ,ln3##
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User-Friendly Interface 31
plus extra buttonsSame as Pandat
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wwwwww.imet.tu.imet.tu--clausthalclausthal.de/.de/agrsfagrsf
Conclusion32
ApplicationsAlloy developmentProcess optimization
Thermodynamic databasesQuality of data is vital - scrutinizing published datasets Link key experiments to modeling
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