Superalloy Dependent Stability of β-NiAl Phase in ...cecamp/NIST Sp05 Diffusion copy.pdf ·...
Transcript of Superalloy Dependent Stability of β-NiAl Phase in ...cecamp/NIST Sp05 Diffusion copy.pdf ·...
Superalloy Dependent Stability ofβ-NiAl Phase in NiCoCrAlY Coatings
Emmanuel Perez, Travis Patterson
Yong-ho Sohn
Advanced Materials Processing and Analysis Center and
Mechanical, Materials and Aerospace Engineering Department
University of Central Florida, Orlando, FL
April 19, 2005
NIST Diffusion Workshop
NiCoCrAlY Coatings in Service
NiCoCrAlY coatings are employed in gas turbine engines toprotect hot-section components such as blades and vanesagainst oxidation and hot corrosion.
These coatings possess a two-phase microstructure consistingof high Al-content β-NiAl solid solution phase and low Al-contentγ-Ni solid solution phase.
The coatings are designed to form a continuous protective Al2O3
oxide scale that protects the coating and in turn the substrate.
Combustors
Air Intake
Compressor
High Pressure Turbine
Low Pressure Turbine
Exhaust
Shaft
Lifetime of NiCoCrAlY Coatings
The Al rich β-phase in the coating isdissolved from the top and the bottompseudo interfaces:
Al is depleted on the top by formation andmaintenance of a protective oxide layer, Al2O3.Al is depleted via interdiffusion with asuperalloy substrate.
As Al depletes, the β-phase dissolves intothe γ-phase (Ni Solid Solution).
The failure of NiCoCrAlY coatings may bedefined by the complete dissolution of β-phase.
Al2O3 scale loses continuity
As Coated
Depleted
BEI: As-Coated
BEI: 5 Cycles
BEI: 50 Cycles
BEI: 100 Cycles
BEI: 314 Cycles
BEI: 400 Cycles
BEI: As-Coated
BEI: 5 Cycles
BEI: 50 Cycles
BEI: 100 Cycles
BEI: 200 Cycles
BEI: 400 Cycles
Parabolic Growth of TGOKp = 6.3 x 10-3 µm·sec1/2
Depletion Zone: Deff = 3.4 x 10-15 m2/secInterdiffusion Zone: Deff = 9.3 x 10-15 m2/sec
Oxidation and Interdiffusion: Recession of (β+γ) in NiCoCrAlY
Y.H. Sohn et al., Surf. Coat. Technol., 146-147 (2001) pp. 70-78.
Interdiffusion and Lifetimeof Oxidation Resistant Coatings
3X in Lifetime (Measured by Stability of Al-Rich β-NiAl Phase)Can be Achieved by Appropriate Selection of SubstrateComposition (Given a Coating Composition).
Isothermal Exposure Time, t 3 x Isothermal Exposure Time, 3t
E. Perez, Y.H. Sohn, Unpublished Research.
Objectives
Determine/Predict the effective interdiffusion coefficientsof Al using solid-to-solid diffusion couples of β-NiAl vs.various superalloys (γ+γ’+others) by:
Direct determination of interdiffusion fluxes fromexperimental concentration profiles in single β-NiAlphase region.Calculation of effective interdiffusion coefficientsincorporating the multicomponent diffusionalinteractions.Prediction of effective interdiffusion coefficients inmultiphase superalloys based on mass balance.
Examine the composition-dependence of Al interdiffusioncoefficients as a function of initial superalloycompositions.
Experimental Details
Solid-to-solid diffusion couples.Equiaxed NiAl vs various commerciallyavailable Ni-superalloys.Encapsulated in quartz capsule in Ar(1 atm at 1050°C) after severalhydrogen flush.Diffusion anneal for 96 hours at 1050°Cusing Lindberg/Blue 3-Zone horizontaltube furnace.Diffusion structures examined byoptical and scanning electronmicroscopyConcentration profiles determine byElectron Probe Microanalysis (EPMA)using pure standards and ZAFcorrection.
Solid-to-Solid Diffusion Couples
Excellent Diffusion Bonding Between Alloys. Particles rich in refractory elements (e.g., Ta, W, Mo, Nb, etc) are
precipitating near the interface between NiAl and superalloys.
NiAl
CM247
NiAl
GTD111
NiAl
IN738
NiAl
IN939
NiAl
Waspalloy
Phenomenology of Isothermal Interdiffusionin Multicomponent System
Onsager’s formalism* for The Interdiffusion Flux of Componenti in a Multicomponent System :
* L. Onsager, Phys. Rev., 37 (1931) 405; 38 (1932) 2265; Ann. NY Acad. Sci., 46 (1965) 241.
Requires Knowledge of (n-1) Independent Concentrations and(n-1)2 Interdiffusion Coefficients.
For a Ternary Systems:
€
˜ J 1 = − ˜ D 113 ∂C1∂x
− ˜ D 123 ∂C2
∂x and ˜ J 2 = − ˜ D 21
3 ∂C1∂x
− ˜ D 223 ∂C2
∂x
€
˜ J i = − ˜ D ijn ∂C j
∂xj=1
n−1
∑ (i = 1,2,...,n -1)
where ∂C j ∂x is the n -1( ) independent concentration gradients
˜ D ijn is the n -1( )2 interdiffusion coefficients
Determination of Ternary Interdiffusion Coefficients byExtension of Boltzmann-Matano Analysis*
* J. Kirkaldy, Can. J. Phys., 35 (1957) 435.
1
23
A B
CD
Distance, x
Co
nce
ntr
atio
n,
Ci
A
B D
C
Requires two independent diffusion couples intersecting at a commoncomposition.
Requires a significant number of diffusion couple experiment toassess compositional dependence of interdiffusion coefficients.
Determination of Interdiffusion FluxesInterdiffusion fluxes of allcomponents can be determineddirectly from their concentrationprofiles without the need of theinterdiffusion coefficients:
€
˜ J i =12t
(x - xo )dCiCi
− or Ci+
Ci x( )
∫ (i = 1,2,..,n)
where t is time
M. A. Dayananda, C. W. Kim, Metall. Trans., 10A (1979) 1333.
No Need for Interdiffusion Coefficientto Assess Diffusional Bahavior ofIndividual Components.
Profiles of experimentalconcentration and the correspondinginterdiffusion fluxes of Cu-Ni-Zncouple, α5 (Cu-43.5at.%-25.0at.%Zn)vs. α12 (Cu-17.5at.%Ni), annealed at775°C for 48 hours.
Integrated and Effective Interdiffusion
€
Di,NiAlint = ˜ J i x( )dx−∞
xo∫ and Di,SAint = ˜ J i x( )dxxo
+∞∫
€
€
˜ D i,NiAleff =
˜ D i,NiAlint
Ci− −Ci
o =
˜ J i−∞
xo∫ dx
Ci− −Ci
o and ˜ D i,SAeff =
˜ D i,SAint
Cio −Ci
+=
˜ J ixo
+∞
∫ dx
Cio −Ci
+
Integrated interdiffusion coefficients for a component iin NiAl and superalloy sides can be defined as:
Effective interdiffusion coefficients for a component iin NiAl and superalloy sides can be defined as:
Effective interdiffusion coefficients incorporatesmulticomponent diffusional interactions:
€
˜ D ieff = ˜ D ii
n +˜ D ij
n ∂C j ∂x∂Ci ∂xj
∑ (j≠ i)
M. A. Dayananda, Y.H. Sohn, Scripta Mater., 35 (1996) 683.
Correlation in Interdiffusion Coefficientswith Concentrations
€
Ci− −Ci
o
Cio −Ci
+=αi,SAαi,NiAl
˜ D i,NiAleff
˜ D i,SAeff
and Ci− −Ci
o
Cio −Ci
+=
˜ D i,NiAlapp
˜ D i,SAapp
where Diapp =
˜ D ieff
αi
Effective interdiffusion coefficients on either side ofthe analysis can be related to compositions:
Therefore, interdiffusion coefficients calculated fromsingle-phase region (e.g., NiAl) can be employed topredict those of multiphase regions (e.g., superalloys).
M. A. Dayananda, Y.H. Sohn, Scripta Mater., 35 (1996) 683.
IN93
9 C
on
cen
trat
ion
(at
%)
Ni
Co
Cr
Al
Ti
0
10
20
30
40
50
60
0 50 100 150 200 250 300 350
Position (µm)
Matano plane X0=154µm
IN93
9 C
on
cen
trat
ion
(at
%)
Ni
Co
Cr
Al
Ti
0
10
20
30
40
50
60
0 50 100 150 200 250 300 350
Position (µm)
Matano plane X0=154µm
IN939
-1.0
-0.5
0
0.5
1.0
1.5
2.0
50 100 150Position (µm)
Al
Co
Cr
Ni
Ti
Matano plane: 154µm
Inte
rdif
fusi
on
Flu
x Ji
(10- 1
1m
/sec
)
IN939
-1.0
-0.5
0
0.5
1.0
1.5
2.0
50 100 150Position (µm)
Al
Co
Cr
Ni
Ti
Matano plane: 154µm
Inte
rdif
fusi
on
Flu
x Ji
(10- 1
1m
/sec
)
Profiles of Concentration and Interdiffusion Flux(NiAl vs. IN939 Annealed at 1050°C for 96 Hours)
The interdiffusion flux was calculated only on the NiAl side (i.e.,single-phase region) of the couple using estimated mass-balanceframe of reference (e.g., Matano plane determined byconcentration profiles and microscopy).
0
10
20
30
40
50
60
70
0 100 200 300 400
Position (µm)
IN73
8 C
on
cen
trat
ion
(at
%)
Al
Co
Cr
Ni
TiMatano plane X0=187µm
0
10
20
30
40
50
60
70
0 100 200 300 400
Position (µm)
IN73
8 C
on
cen
trat
ion
(at
%)
Al
Co
Cr
Ni
TiMatano plane X0=187µm
-1.0
-0.5
0
0.5
1.0
1.5
2.0
0 100 200Position (µm)
Inte
rdif
fusi
on
Flu
x Ji
(10-1
1m
/sec
)
IN738
Al
CoCr
Ni
Ti
Matano plane: 187µm
-1.0
-0.5
0
0.5
1.0
1.5
2.0
0 100 200Position (µm)
Inte
rdif
fusi
on
Flu
x Ji
(10-1
1m
/sec
)In
terd
iffu
sio
n F
lux
Ji(1
0-11
m/s
ec)
IN738
Al
CoCr
Ni
Ti
Matano plane: 187µm
Profiles of Concentration and Interdiffusion Flux(NiAl vs. IN738 Annealed at 1050°C for 96 Hours)
The interdiffusion flux was calculated only on the NiAl side (i.e.,single-phase region) of the couple using estimated mass-balanceframe of reference (e.g., Matano plane determined byconcentration profiles and microscopy).
0
10
20
30
40
50
60
70
0 100 200 300Position (µm)
CM
247
Co
nce
ntr
atio
n (
at%
)
Al
Ni
Co
Cr
TiMatano plane X0=214µm
0
10
20
30
40
50
60
70
0 100 200 300Position (µm)
CM
247
Co
nce
ntr
atio
n (
at%
)
Al
Ni
Co
Cr
TiMatano plane X0=214µm
CM247Al
Co
Cr
Ni
Ti
-1.0
-0.5
0
0.5
1.0
1.5
100 200
Position (µm)In
terd
iffu
sio
n F
lux
Ji(1
0- 11
m/s
ec)
Matano plane: 214µm
CM247Al
Co
Cr
Ni
Ti
-1.0
-0.5
0
0.5
1.0
1.5
100 200
Position (µm)In
terd
iffu
sio
n F
lux
Ji(1
0- 11
m/s
ec)
Matano plane: 214µm
Profiles of Concentration and Interdiffusion Flux(NiAl vs. CM247 Annealed at 1050°C for 96 Hours)
The interdiffusion flux was calculated only on the NiAl side (i.e.,single-phase region) of the couple using estimated mass-balanceframe of reference (e.g., Matano plane determined byconcentration profiles and microscopy).
DeffNiAlDappNiAlDIntNiAlAluminum
14.45.452.16Waspalloy
8.473.021.50IN939
11.24.061.58IN738
10.23.651.56GTD111
11.24.151.31CM247
10-15(m2/sec)10-15(m2/sec)at%Alloy
DeffSADappSADIntSAAluminum
3.541.130.98Waspalloy
3.591.140.92IN939
3.491.110.83IN738
3.481.110.86GTD111
2.890.920.62CM247
10-15(m2/sec)10-15(m2/sec)at%Alloy
Interdiffusion Coefficients of AlCalculated for NiAl and Predicted* for Superalloy
NiAl Side Calculatedwith Concentration Profiles
Superalloy Side Predicted withCorrelations* in Interdiffusion Coefficients
€
Ci− −Ci
o
Cio −Ci
+=αi,SAαi,NiAl
˜ D i,NiAleff
˜ D i,SAeff
and Ci− −Ci
o
Cio −Ci
+=
˜ D i,NiAlapp
˜ D i,SAapp
Correlations* Integrated, apparent and effectiveinterdiffusion coefficients formultiphase region (i.e.,superalloys and precipitates) canbe predicted.
Deff determined based on
€
αi = π
DeffSADappSADIntSAAluminum
2.971.130.98Waspalloy
2.951.140.85IN939
3.572.150.96IN738
2.301.110.64GTD111
2.080.920.52CM247
10-15(m2/sec)10-15(m2/sec)at%Alloy
DeffSADappSADIntSAAluminum
3.541.130.98Waspalloy
3.591.140.92IN939
3.491.110.83IN738
3.481.110.86GTD111
2.890.920.62CM247
10-15(m2/sec)10-15(m2/sec)at%Alloy
Interdiffusion Coefficients of AlPredicted and Estimated* for Superalloy
Predicted InterdiffusionCoefficients for Superalloys
Estimated* InterdiffusionCoefficients for Superalloys
*Estimation using spline-fittedconcentration profile through thescatter in multiphase region insuperalloys
Predicted using correlations ininterdiffusion coefficients.
Deff determined based on
€
αi = π
Integrated Diffusion Coefficient (i.e., TotalInterdiffusion Flux) of Al in Various Superalloys
Aluminum
3.14Waspalloy
2.34IN939
2.54IN738
2.20GTD111
1.83CM247
10-15(m2/sec)at%Alloy
€
˜ D Al, TotalInt The integrated interdiffusion
coefficient for the entireprofile employs thatcalculated from the NiAlside (i.e., single-phaseregion) of the couple andthat predicted for thesuperalloy side (i.e.,multiphase-region).
The integrated interdiffusioncoefficient indicates theoverall interdiffusion flux foreach diffusion couples.
Variation of Apparent Diffusion Coefficientswith Initial Superalloy Composition
0.80
1.00
1.20
0 5 10 15 20 25 300.80
1.00
1.20
0 5 10 15 20 25 30
Cr (at%)
0.80
1.00
1.20
0 1 2 3 4 5 6 70.80
1.00
1.20
0 1 2 3 4 5 6 70.80
1.00
1.20
0 1 2 3 4 5 6 7
˜ D A
l, SA
App
x10
15(
) m
2se
c
Ti (at%)
˜ D A
l, SA
App
x10
15(
) m
2se
c
0.80
1.00
1.20
0 2 4 6 8 10 12 14
Al (at%)
˜ D A
l, SA
App
x10
15(
) m
2se
c
Variation of Apparent Diffusion Coefficientswith Initial Superalloy Composition
0.80
1.00
1.20
0.0 0.5 1.0 1.50.80
1.00
1.20
0.0 0.5 1.0 1.5
Ta (at%)
˜ D A
l, SA
App
x10
15(
) m
2se
c
0.80
1.00
1.20
0.0 1.0 2.0 3.0 4.00.80
1.00
1.20
0.0 1.0 2.0 3.0 4.0
W (at%)
˜ D A
l, SA
App
x10
15(
) m
2se
cApparent Al interdiffusion coefficients in superalloysincreased with increases in Cr and Ti concentrations,but decreased with increases in Al, Ta and Wconcentrations in the superalloys.
Summary
Solid-to-solid diffusion couples studies using β-NiAl vs.CM247, GTD111, IN738, IN939 and Waspalloy were carriedout.Integrated, effective and apparent interdiffusioncoefficients from single-phase region (β-NiAl) werecalculated based on concentration profiles determined byEPMA.Integrated, effective and apparent interdiffusioncoefficients in the multiphase phase region (superalloys)were predicted.Apparent Al interdiffusion coefficients in superalloysincreased with increases in Cr and Ti concentrations, butdecreased with increases in Al, Ta and W concentrationsin superalloys.Experimental work is in progress to determine themagnitude of compositional dependence (I.e., crossinterdiffusion coefficients).