Upload
indra-pratap-sengar
View
221
Download
3
Embed Size (px)
DESCRIPTION
ProCAST Thermodynamic Database
Citation preview
1
ProCAST
Thermodynamic Database
Release Notes
2
SUMMARY
Release Notes 2008 ........................................................................................ 3
Improvement made in the new release Ni-Database, PanNi7..................................... 4 Improvement made in the new release Fe-Database, PanFe7................................... 11
Release Notes 2007 ...................................................................................... 12 Improvement made in the new release Fe-Database, PanFe6_c............................... 13
Release Notes 2006 ...................................................................................... 16 Improvement made in the new release Ni-Database, PanNi6................................... 17 Improvement made in the new release Ti-Database, PanTi6 ................................... 18 Improvement made in the new release Mg-Database, PanMg6 ............................... 21
3
Thermodynamic Database
Release Notes 2008 for:
Nickel based alloys: PanNi7
Fe Based alloys: PanFe7
4
Improvement made in the new release Ni-Database, PanNi7:
Ni Ni
AlAl
Hf Hf
Cr Cr
C C B B
Fe Fe
Co Co
Ir Ir MoMoN N NbNb
Pt Pt Re Re
Ru Ru
Si Si
Ta Ta
Ti Ti
ZrZrW W
Three new elements: Pt, Ru and Ir are added to PanNi7, with thermodynamic descriptions developed for some key binaries and ternaries as listed in Table 1.
Table 1: Thermodynamic descriptions for key binaries and ternaries Pt Ru Ir
Ni Ni-Pt Ni-Ru Ni-Ir Al Al-Pt Al-Ru Al-Ir Cr Cr-Pt Cr-Ru
Ni-Al Ni-Al-Pt Ni-Al-Ru Ni-Al-Ir Ni-Cr Ni-Cr-Pt Ni-Cr_Ru Al-Cr Al-Cr-Pt Al-Cr-Ru
Full Description
Binary Extrapolation
5
1. Thermodynamic description for the Ni-Al-Cr-Pt system is developed and
incorporated into the PanNi7 database. Some calculated results are shown below:
0.0 0.2 0.4 0.6 0.8 1.0300
600
900
1200
1500
1800
2100
Ni 3P
t
NiP
t
-(Ni,Pt)
PtNi
33Kur 33Kur 44Esc 78Stc 53Ori
LiquidTe
mpe
ratu
re(K
)
Mole-fraction Pt
Figure 1: Comparison between calculated Ni-Pt binary phase diagram and experimentally determined phase boundary
0.0 0.2 0.4 0.6 0.8 1.0300
600
900
1200
1500
1800
2100
'-AlPt
3
Al 3P
t 5
PtAl
64Huc 70Dar 78Sch
Al 3P
t 2
Al 21
Pt 5
Al 21
Pt 8
Al 2P
t
AlP
t
-(Pt)
Liquid
Tem
pera
ture
(K)
Mole-fraction Pt Figure 2: Comparison between calculated Al-Pt binary phase diagram and
experimentally determined phase boundary
6
0.0 0.2 0.4 0.6 0.8 1.0800
1200
1600
2000
2400
L12A15
(Cr)
L12
single phase (73Wat) two phase (73Wat) phase boundary (73Wat) order transition (68Kus)
Liquid
PtCr
Tem
pera
ture
(K)
Mol. Fracn. Pt Figure 3: Comparison between calculated Cr-Pt binary phase diagram and
experimentally determined phase boundary
0.0 0.2 0.4 0.6 0.8 1.0
0.0
0.2
0.4
0.6
0.8
1.0
Liquid
05Hay
'
T = 1423K
'
Al
Ni Pt
Mol
. Fra
cn. N
i
Mol. Fracn. Pt
Figure 4: Comparison between calculated Ni-Al-Pt isothermal section and experimentally determined tie lines
7
0.00055 0.00060 0.00065 0.00070
1E-5
1E-4
1E-3
Ni-15Al-5Pt ( 06Cop PanNi7)Ni-15Al-5Pt-5Cr ( 06Cop PanNi7)Ni-15Al-5Pt-10Cr ( 06Cop PanNi7)
Act
ivity
of A
l
1/T Figure 5: Comparison between the calculated and experimentally determined activity of
Al in the Ni-Al-Pt and Ni-Al-Cr-Pt systems.
0.00055 0.00060 0.00065 0.000700.1
1
Ni-15Al-5Pt ( 06Cop PanNi7)Ni-15Al-5Pt-5Cr ( 06Cop PanNi7)Ni-15Al-5Pt-10Cr ( 06Cop Panni7)
Activ
ity o
f Ni
1/T Figure 6: Comparison between the calculated and experimentally determined activity of
Ni in the Ni-Al-Pt and Ni-Al-Cr-Pt systems.
8
2. Thermodynamic description for the Ni-Al-Cr-Ru system is developed and incorporated into the PanNi7 database. Some calculated results are shown below:
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0500
1000
1500
2000
2500
3000
RuAl
FCC
This work 88Anl
Al 3R
u 2
Al 6R
u
Al 13
Ru 4
Al 2R
u
AlR
u HC
P
LiquidTe
mpe
ratu
re(K
)
X(Ru)
Figure 7: Comparison between calculated Al-Ru binary phase diagram and experimentally determined phase boundary
0.0 0.2 0.4 0.6 0.8 1.0
500
1000
1500
2000
2500
749
800
1001
1610
1580
This work [61Sav] [64Shu]
Cr 3R
u
hcpbcc
RuCr
Liquid
Tem
pera
ture
(oC
)
Mole Fraction of Ru
Figure 8: Comparison between calculated Cr-Ru binary phase diagram and experimentally determined phase boundary
9
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0400
600
800
1000
1200
1400
1600
1800
2000
2200
2400
1554
fcc
hcp
Liquid
RuNi
This Work 64Kor 64Kor X-ray 61Rau 61Rau X-ray
Tem
pera
ture
(o C)
Mole Fraction of Ru
Figure 9: Comparison between calculated Ni-Ru binary phase diagram and experimentally determined phase boundary
0.0 0.2 0.4 0.6 0.8 1.0
0.0
0.2
0.4
0.6
0.8
1.0
86ChaT = 1523K
21
'
Al
RuNi
Mol
e Fr
actio
n Ni
Mole Fraction Ru Figure 10: Comparison between calculated Ni-Al-Ru isothermal section and
experimentally determined tie lines
10
3. Thermodynamic description for the Ni-Al-Ir system is developed and incorporated into the PanNi7 database. Some calculated results are shown below:
500
1000
1500
2000
2500
3000
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0
L
(Ir)
B2
Al2.
7Ir
Al3Ir
Al 45
Ir13
Al 9I
r 2
(Al)
Al13Ir4
Al Ir
Tem
pera
ture
(K)
Mol. Fracn. Ir
Axler et al., EPMAAxler et al., Optical Pyrometry
0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1500
1000
1500
2000
2500
3000
Figure 11: Comparison between calculated Al-Ir binary phase diagram and
experimentally determined phase boundary
Figure 12: Comparison between calculated Ni-Al-Ir isothermal section and experimentally determined tie lines
11
Improvement made in the new release Fe-Database, PanFe7:
Thermodynamic description for the Fe-S is improved.
12
Thermodynamic Database
Release Notes 2007 for:
Fe Based alloys: PanFe6_c
13
Improvement made in the new release Fe-Database, PanFe6_c:
1. The thermodynamic description of the Fe-S binary system is improved. In PanFe6, the model parameters for the liquid phase and the MeS phase in the Fe-S binary are not consistent. This will cause problems in the multi-component system. These parameters are re-optimized for this reason. 2. Thermodynamic description for the Fe-Si-Sn is developed and implemented into the Fe-database. Some customers are interested in Fe alloys with small amount of Sn. Due to the time limit and alloy chemistry, the key ternary Fe-Si-Sn is the focus of this improvement. Some calculated results are shown in figures 1-4. Since this an intermediate release, this new version is named as PanFe6_c.
T[C
]
w%(SN)
0
200
400
600
800
1000
1200
1400
1600
0 10 20 30 40 50 60 70 80 90 100
w%(SN)
T[C
]
FE SN
BCC_
A2
FCC_
A1
Fe5S
n3Fe
3Sn2
FeSn
FeSn
2
1134
895
807768 761
609
512
232
0 10 20 30 40 50 60 70 80 90 1000
200
400
600
800
1000
1200
1400
1600
Figure 1: Fe-Sn Binary Phase Diagram
14
x(SI)
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(SI)
x(SN
)
FE
SN
SI
FeSi FeSi2_L Diamond
BCT
FeSn2
FeSn
Bcc
Bcc+FeSnBcc+FeSn+FeSi
Figure 2: Isothermal Section of Fe-Si-Sn at 25oC. (a) Calculated. (b) Assessed According to Experimental Measurements.
Wsn
0
300
600
900
1200
1500
0.0 0.1 0.2 0.3
Bcc+FeSnFeSi+FeSn+Bcc
L2+FeSi+Bcc
L2+FeSi+Fe5Si3
L2+Bcc+Fe5Si3
L2+Bcc
L2+Fe2Si+FeSi L1+L2+Bcc
L1+L2LL
L1+L2+FeSi
L+FeSn+Bcc
Wsn
0
300
600
900
1200
1500
0.0 0.1 0.2 0.3
Bcc+FeSnFeSi+FeSn+Bcc
L2+FeSi+Bcc
L2+FeSi+Fe5Si3
L2+Bcc+Fe5Si3
L2+Bcc
L2+Fe2Si+FeSi L1+L2+Bcc
L1+L2LL
L1+L2+FeSi
L+FeSn+Bcc
Bcc+FeSnFeSi+FeSn+Bcc
L2+FeSi+Bcc
L2+FeSi+Fe5Si3
L2+Bcc+Fe5Si3
L2+Bcc
L2+Fe2Si+FeSi L1+L2+Bcc
L1+L2LL
L1+L2+FeSi
L+FeSn+Bcc
Figure 3: Isopleth Parallel to Si-Sn with 70 wt% Fe
15
Wsi
200
400
600
800
1000
1200
1400
1600
0.00 0.05 0.10 0.15 0.20 0.25 0.30 0.35
Bcc+FeSnFeSi+FeSn+Bcc
L2+FeSi+Bcc
L2+FeSi+Fe5Si3
L2+Bcc
L2+Fe2Si+FeSi
L1+L2
Bcc
L
L1+L2+FeSi
L1+L2+Bcc
L1+Bcc
L2+Bcc+Fe5Si3
L2+FeSi+FeSi2_H
L2+FeSi+FeSi2_L
Wsi
200
400
600
800
1000
1200
1400
1600
0.00 0.05 0.10 0.15 0.20 0.25 0.30 0.35
Bcc+FeSnFeSi+FeSn+Bcc
L2+FeSi+Bcc
L2+FeSi+Fe5Si3
L2+Bcc
L2+Fe2Si+FeSi
L1+L2
Bcc
L
L1+L2+FeSi
L1+L2+Bcc
L1+Bcc
L2+Bcc+Fe5Si3
L2+FeSi+FeSi2_H
L2+FeSi+FeSi2_L
Figure 4: Isopleth From Pure Fe Along the Fix Ratio of Si/Sn=35/65 (wt%)
Fe 35Si65Sn
16
Thermodynamic Database
Release Notes 2006 for:
Ni based alloys: PanNickel6
Titanium Alloys: PanTitanium6
Magnesium Alloys: PanMagnesium6
17
Improvement made in the new release Ni-Database, PanNi6:
1. Thermodynamic description for the phase is developed in PanNi6. This is based on the work of M. K. Miller and S. S. Babu Atomic Level Characterization of Precipitation in Alloy 718 published on (Edited by E. A. Loria, 2001) and other available experimental data. Since is a metastable phase and will transfer to stable phase after long time exposure at high temperature, must be suspended to reveal phase during thermodynamic calculation. However, this is not the case for kinetic simulation in which their stabilities are determined by the kinetic parameters and heat treatment conditions in addition to the thermodynamic stability. Introduce of phase enable the simulation of 718 alloys. Fractions of phases as function of temperature for one Ni718 alloy is shown in Figure 1.
0.0
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
1.0
600 700 800 900 1000 1100
f()f(')f('')f()(exp)''(exp)'(exp)(exp)
Phas
e Fr
actio
ns
Temperatur e [oC]600 700 800 900 1000 11000
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
1
Figure 1: Fraction of phase as a function of temperature for nickel alloy 718
2. Many ternary systems, such as Ni-Al-Co, Ni-Co-Cr, Ni-Al-Ta, Ni-Al-W, Ni-Co-
Re, and Ni-Co-Ta, are modified so that the properties, such as densities, liquidus, solidus, and solvus can be reasonably predicted.
3. Thermodynamic description of phase is modified based on the available
experimental data. The phase, originated from Ni3Ti, can be described as Ni3(Al, Nb, Ti, ) which is essentially the same as those of the , , and but with different levels of Al, Nb and Ti. The relative stability of these phases is therefore determined by the alloy composition and kinetic parameters.
18
Improvement made in the new release Ti-Database, PanTi6:
1. Ternary systems, such as Ti-Al-V, Ti-Al-Mo, Ti-Al-Sn, Ti-Al-Cr, Ti-Al-Nb, Ti-
Cr-Nb, Ti-Al-O, and so on are modified to better describe the commercial titanium alloys. The modified database is thoroughly tested by commercial titanium alloys, such as Ti64, Ti6242, Ti6246, Ti17, and so on. As an example, the calculated fraction of phase as a function of temperature is compared with the experimental data for one Ti6242 alloy as shown in Figure 2.
0.0
0.2
0.4
0.6
0.8
1.0
1300 1400 1500 1600 1700 1800 1900
Temperature (F)
Volu
me
Frac
tion
Bet
a
[2005Sem]Calculated
Figure 2: Fraction of phase as a function of temperature for Ti6242,
experimental data is from L. Semiatin [2005Sem] (private communication)
Figure 3 and 4 show the comparison between calculated and experimental determined phase composition for the same Ti6242 alloy, very good agreement are obtained.
2. Thermodynamic description for the Ti-Si-Zr system is developed with the ternary S2 phase included. Calculated isotherm and isopleth are compared with experimental data as shown in Figures 5 and 6.
19
0.0
5.0
10.0
15.0
20.0
25.0
1300 1400 1500 1600 1700 1800 1900Temperature (F)
Com
posi
tions
(wt %
)
Al AlphaAl BetaMo AlphaMo BetaPandat Al BetaPandat Mo BetaPandat Al AlphaPandat Mo Alpha
Al
Mo
Al
Mo
Figure 3: Comparison between calculated and experimental determined phase
composition (Al and Mo) for the same Ti6242 alloy as in Figure 2.
70.0
75.0
80.0
85.0
90.0
95.0
1300 1400 1500 1600 1700 1800 1900
Temperature (F)
Com
posi
tions
(wt %
)
Ti AlphaTi BetaPandat Ti AlphaPandat Ti Beta
Ti
Ti
Figure 4: Comparison between calculated and experimental determined phase
composition (Ti) for the same Ti6242 alloy as in Figure 2.
20
Figure 5: Comparison between calculated and experimental determined isothermal section of the Ti-Si-Zr system at 1200oC
Figure 6: Comparison between calculated and experimental determined isopleth section of the Ti-Si-Zr system.
0.0
0.2
0.3
0.5
0.7
0.9
0.0 0.2 0.4 0.6 0.8 1.0
CalculateOutlined by
Ti Z
Si
X(Zr)
600
800
1000
1200
1400
1600
1800
0.0 0.1 0.2 0.3
CalExp
80Ti 0Zr 20Si
50Ti 30Zr 20Si
21
Improvement made in the new release Mg-Database, PanMg6: 17 Components: Ag, Al, Ca, Ce, Cu, Fe, Gd, Li, Mg, Mn, Nd, Sc, Si, Sr, Y, Zn, Zr 285 Phases Simplified Composition Limits: > 75 wt.%: Mg < 10 wt.%: Al, Ca, Li, Mn, Si, Zn, but not in combinations Ca+Mn, Ca+Zn, Mn+Si or Si+Zn < 1 wt.%: Ag, Ce, Gd, Nd, Sc, Sr, Y, Zr, Fe, Cu
Many element combinations can be used well beyond these limits or even in the entire composition range. Details are given below.
Composition Limits for Advanced Users: 1. Binary Mg-X: 0 - 100 wt.%, X = all components 2. Binary X1-X2: see Table 1: Binary systems 3. Ternary Mg-X1-X2 see Table 2: Ternary and multicomponent systems Mg-X1-X2-X3 4. Multicomponent systems see Table 2: Ternary and multicomponent systems Mg-X1-X2-X3
Table 1: Binary systems
Ag Al Ca Ce Cu Fe Gd Li Mg Mn Nd Sc Si Sr Y Zn Zr Ag 95Lim 02Yin 97Lim 97Lim 01RSF 88Che 01RSF 98Gom 01RSF Al A 00RSF 98Cac 91Sau 91Sei 00RSF 89Sau 98Lia 04RSF 03Cac 99Gro 92Luk 04Zho 95Gro 93Mey 01Wan Ca ! A 99RSF 96Ris 94Ang 99RSF 00RSF 95Aga 03RSF 03RSF 00RSF 02RSF 03Zho 00RSF 01Bru Ce A A C 96Zhu 00RSF 94Cac 99RSF 03Cac 99RSF 03RSF 03Pis 03RSF Cu A A A A 93Ans 91Sau 91Cou 03Mie 96Zhu 01RSF 91Jac 96Ris 97Jan 93Kow 93Zhe Fe 0 CC B ! A 00Zin 91Tib 91Hua 93Hen 91Lac 00Reu 01Jia Gd ! A C 0 ? C 00RSF 99Cac 00RSF 00RSF 00RSF Li 0 A A D CC 0 B 90Sau 97RSF 97RSF 95Bra 01RSF 00RSF 91Sau Mg B A B C A B C A 04RSF 01RSF 98Pis1 01Zha 00Li 01Luk 92Luk 91Ham Mn 0 B B C B A B D B 00RSF 98Pis2 91Tib 00RSF 01Mie 97Gro Nd C B C B A B 0 0 C C 01RSF Sc ! A D C C ! C D A A ? 00RSF Si A A A C A B ! B B CC ! ! 92Luk 93Jac 94Gue Sr ! A B ? A 0 ? ! B 0 0 0 ! 03Zho Y C A C 0 A ! C C B A C C CC 0 97Gro Zn A A B B A A ! C B C ! ! CC B ! Zr C A ? C A B 0 ? C B 0 0 B ? C !
22
Modeling status Rating of modeling quality
A = excellent fitting to sufficient experimental data (enthalpies of formation, enthalpies of mixing, phase diagram data, solubilities)
Complete binary modeling, Reliable description
B = satisfactory fitting or/and less experimental data (cannot be improved based on present experimental data) C = quick + dirty (could be improved with more modeling effort on existing data) D = dirty (unreliable or missing experimental data estimation only)
Complete binary modeling, Less reliable description
CC = from Database (cost, ), no publication available 0 = noncritical system (no stable binary phases) Produces very crude (ideal solution) binary system ? = No information available (no phase diagram, no known
compounds)
No binary modeling, extrapolation of terminal solutions only
! = critical system (known high melting compounds, ) Danger: do not use for binary calculations, compounds will not appear
Table 2: Ternary and multicomponent systems Mg-X1-X2-X3 Complete
assessment Assessment checked for Mg-corner
Extrapolation not checked - Element combination is not critical
Extrapolation not checked - criticala) combination
Suggested composition limit for (X1+X2)
0 - 100 wt.%
< 20 wt.%
< 5 wt.% < 1 wt.%
Ternary systems Mg-X1-X2 -Al-Ca -Ag-Al -Ag-Fe -Cu-Fe -Li-Nd -Ag-Ca -Al-Ce -Ag-Ce -Ag-Li -Cu-Gd -Li-Sc -Ag-Gd -Al-Cu -Ag-Cu -Ag-Mn -Cu-Mn -Li-Y -Ag-Sc -Al-Gd -Ag-Nd -Ca-Cu -Cu-Nd -Li-Zr -Ag-Sr -Al-Li -Ag-Y -Ca-Fe -Cu-Sc -Mn-Nd -Ce-Fe -Al-Mn -Ag-Zr -Ca-Gd -Cu-Zr -Mn-Si -Ce-Zn -Al-Sc -Al-Y -Ca-Mn -Fe-Gd -Mn-Sr -Ce-Zr
Mg +
-Al-Si -Ca-Ce -Ca-Nd -Fe-Li -Mn-Zn -Fe-Sc
23
-Al-Zn -Gd-Mn -Ca-Sc -Fe-Mn -Mn-Zr -Fe-Y -Ca-Li -Gd-Y -Ca-Sr -Fe-Nd -Nd-Sc -Gd-Si -Ca-Si -Li-Zn -Ca-Y -Fe-Si -Nd-Sr -Gd-Zn -Cu-Li -Mn-Y -Ca-Zn -Fe-Sr -Nd-Zr -Li-Sr -Cu-Si -Nd-Y -Ca-Zr -Fe-Zn -Sc-Sr -Nd-Si -Cu-Y -Sc-Y -Ce-Cu -Fe-Zr -Sc-Zr -Nd-Zn -Cu-Zn -Ce-Gd -Gd-Mn -Si-Y -Sc-Si -Gd-Li -Ce-Mn -Gd-Nd -Si-Zn -Sc-Zn -Li-Si -Ce-Sc -Gd-Sc -Si-Zr -Si-Sr -Mn-Sc -Ce-Sr -Gd-Sr -Sr-Y -Sr-Zn -Mn-Zr -Ce-Si -Gd-Zr -Sr-Zn -Y-Zn
-Y-Zr -Ce-Y -Li-Mn -Sr-Zr -Zn-Zr Multicomponent systems Mg-X1-X2-X3
-Al-Ca-Li -Al-Ca-Ce -Al-Ca-Si -Al-Gd-Li -Al-Cu-Zn -Mn-Y-Zr -Al-Li-Si -Ce-Mn-Sc -Gd-Mn-Sc
Mg +
-Mn-Sc-Y
Non Mg systems Al-Ca-Fe Ag-Al-Cu Al-Ca-Si Al-Ca-Ce Al-Ce-Nd Al-Ca-Li Al-Ce-Si Al-Ce-Gd Al-Cu-Li Al-Ce-Y Al-Cu-Si Al-Cu-Mn Al-Cu-Zn Al-Cu-Nd Al-Fe-Mn Al-Gd-Nd Al-Fe-Si Al-Gd-Y Al-Li-Si Al-Li-Mn Al-Mn-Si Al-Mn-Sc Al-Si-Zn Al-Nd-Y Ca-Fe-Si Al-Si-Y Ca-Li-Si Ca-Sr-Zn Cu-Fe-Si Fe-Mn-Si
24
a) Combination is critical either because - Critical binary system(s) involved, e.g. Ag-Ca - Ternary extrapolation does not take known ternary solubilities (or phases) into
account, even though all binary systems are assessed, e.g. Mg-Ce-Zn Note:
A simple fixed composition limit ( % of additive elements to Mg) is not adequate for two reasons:
1. Modeling of binary and ternary systems was generally performed for full composition range. That is, the Mg-database may be used for many other systems as well.
2. Even a small (a few %) joint addition of elements X and Y might in worst case form a stable XY precipitate in Mg-matrix. For 16 components we have 120 binary systems and the combination of X and Y must be checked. All binary Mg-X systems are fully modeled.
Table 3: Notes to Validity limits
Safety level Determination of safety level for system Mg-X1-X2-X3
Potential risks Recommended composition limits
1. Very safe System is listed in Table 2, green code
assessed at least for main components.
Implies assessment of all binaries.
none
none (proximity to
assessed ternaries is most safe)
2. Safe All binary systems (X1-X2, X1-X3, X2-X3) are
assessed, see green or yellow code in Table 1
Unknown stable ternary phases or
solutions might be overlooked.
(Often for Al + RE)
none (proximity to
assessed binaries is most safe)
3. Reasonably
safe
Some binary systems (X1-X2) are not assessed but
uncritical, see "0" in Table 1
Same as level 2 plus (maybe)
binary XY phases overlooked at high joint composition
> 75 wt.% Mg and (X1+X2) < 20
wt.%
4. Partially unsafe
Some binary systems (X-Y) are not assessed and
critical, see "!" in Table 1
Same as level 3 plus binary XY phases
overlooked, possibly even at low joint
composition
> 75 wt.% Mg and (X1+X2) < 1
wt.%
ProCASTThermodynamic DatabaseRelease NotesThermodynamic DatabaseThermodynamic DatabaseThermodynamic DatabaseAg95Lim97Lim
CC
91Ham?Non Mg systems