atomic layer deposition, a rising technique for … · atomic layer deposition, a rising technique...
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Atomic Layer Deposition, a rising technique for SOFC and MCFC devices
A. Meléndez-Ceballos, D. Chery, A. Marizy, V. Albin,
A. Ringuedé, M. Cassir*
* Head Laboratoire d’Electrochimie, Chimie des Interfaces et Modélisation pour l’Energie, LECIME, UMR 7575 CNRS, ENSCP, Paris, France
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High temperature fuel cells & electrolysis
OHOH 222 21
…………+FC
SOEC
ZrO2-Y2O3
Cermet Ni-YSZ
La1-xSrxMnO3
O2- O2-
- → + 2 2
_ 2 2 1
O e O
_ 2 2 2
2 e O H O H + → + -
SOFC: 600-700°C
- e CO O H CO H 2 2 2 2 3 2
+ + → + -
CO32-
- → + + 2 3 2 2 2
2
1 CO - e CO O
Li2CO3- K2CO3
Ni + 2 à 10% Cr ou Al
NiO
MCFC: 600-650°C
↑ lifetime & performance:
Nanostruct./electrochem.
→ half-cells → single cells
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MCFC/SOFC Composite
carbonate/oxide
Nano-scaled layers for SOFC, i.e. CeO2 or ZrO2-based
* Interfacial layers – Chemical diffusion barrier (cathode/electrolyte interface) – Electronic barrier (anode/electrolyte interface) – Catalyst/electrode (at both interfaces) – Bond layer
* As SOFC electrolytes: µ-SOFC Charge transfer enhancement, resistance ↓ conductivity ↑?
* As corrosion protective layers for interconnects * As active layer at the cathode interface
Cathode (thick or thin)
Electronic barrierElectrolyte (thick or thin)
Anode (thick or thin)
Ionic diffusion barrier
Electrodecatalysts
Interconnect
Interconnect
Protective layer
Protective layer
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Atomic layer Deposition
4
Surface saturation reaction. Thickness: from few nm to µm
R. Puurunen, J. Appl. Phys., 97 (2005) 121301
Gro
wth
spe
ed
Deposition T
ALD window
- Crystaline as deposited
M. Cassir et al., J. Mater. Chem., 20 (2010) 8987
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Litterature orientations
Two main tendencies / use of ALD in SOFCs applications: Ø Low operating temperatures (<500°C) for micro systems such as portable applications. In µ-SOFCs, ultrathin electrolyte layers have a significant role and ALD presents a serious advantage.
ü The use of ultrathin catalytic or current-collector layers of Pt and Pt grid-patterned catalysts is common.
ü However, this approach supposes the direct use of hydrogen and contradicts the requirements of SOFCs in cogeneration: avoiding precious metals and using fuels as natural gas or biomass which implies a reforming process operating at around 600°C.
Ø The second tendency concerns electrolyte or catalysts interlayers
and / or cheaper electrode materials activated by ultrathin ALD-processed materials.
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State-of-the-Art Electrolyte, interfaces & current collectors: (i) Stabilized zirconia (e.g. YSZ): ZrO2, YSZ, ZrO2-In2O3 from few nm to 1 µm. on planar substrates, on porous electrodes and on pre-patterned surfaces (ii) Ceria and doped ceria (e.g. Gd0.2Ce0.8O2-d = GDC), YDC (iii) LaGaO3, which is a potential electrolyte when doped: LSGM (La0.9Sr0.1Ga0.8Mg0.2O3) (iv) BaZrO3, proton-conductor (v) Pt deposits (catalysts or/and current collectors)
Cathode: a) LaxSr1-xMnO3 (LSM) b) La1-xCaxMnO3: potential electrode c) La1-xSrxFeO3 (LSF)
Anode: LaGaO3-based materials when doped with Sr and Mg
Main teams: Prinz et al., Mc Intyre et al., Bent et al. (Standford), Niinistö et al (Helsinki), Cassir et al. (Paris), Nilsen et al. (Norway), …
Review “Input of Atomic Layer Deposition for Solid Oxide Fuel Cell Applications”, M. Cassir, A. Ringuedé, L. Ninistö, J. Mater. Chem., 20 (2010) 8987
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* Chao et al., ACS Nano, 7 (2013) 2186 ** Fan et al., Nanole:ers, 11 (2011) 2202. *** Fan et al., J. Mater. Chem., 21, 10903 (2011).
Ø Enhancing O2-‐ incorpora/on kine/cs by nanoscaled interlayers**,*** • 17.5 nm of YDC (14.1 mol. % Y) between YSZ and a porous Pt cathode
enhances the performance of LT-‐SOFC • ↓ cathode/electrolyte R while increasing the exchange j0 by a factor of
4 at 300-‐500 °C • Enhancement of the performance of the cell x 3
Ø Enhanced oxygen exchange on surface-‐engineered YSZ* • 10 nm of ALD-‐processed YSZ (14 mol. % Y) on YSZ single-‐crystal YSZ ↓ O2
surface exchange coefficient 5 fold increase (Isotopic oxygen exchange tests + SIMS)
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Grain sizes of 20-‐30 nm result in a high density of grain boundaries, which together with the OH-‐ incorpora?on tend to provoke the proton conduc?vity of the YSZ thin film (200 nm) 10 mW/cm² at 450°C
* Prinz et al., Chem. of Mater. 21, 3290 (2009) ** J. S. Park et al. , Chem. Of Mater., 22, 5366 (2010)
Ø Y-‐doped BaZrO3 proton conduc/ng membranes (BYZ) of 100 nm used in a single cell with Pt porous electrodes*
100 nm thin films: ü ALD-‐processed: 136 mW/cm² at 400°C ü PLD (pulsed laser deposi?on)-‐ processed : 120 mW/cm² at 450°C
Ø Proton conduc/on-‐based fuel cell with YSZ electrolyte by ALD**
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ZrO2-Y2O3 (YSZ) 8 mol% / LSM at 300°C .
990 nm nm 990 nm
990 nm 540 nm 280 nm
-6.5
-6
-5.5
-5
-4.5
-4
-3.5
-315 17 19 21 23 25 27
10000/T(K-1)
Log(σ(S.m-1))
E=0.33eV
E=0.34eV
E=0.40eVж Sample AΔ Sample BÅSample C
100°CT(°C)
200°C300°C
activation energies < 1 eV (bulk YSZ)
σi(280)<σi(540)≈σi(990)
Sl
Rmeas1=σ
C. Brahim, Appl.. Surf. Sci. 253 (2007) 3962 M. Cassir et al. Appl. Surf. Sci., 193 (2002) 120 M. Cassir et al., Patent WO02053798 (2002)
-4.00E+02
-2.00E+02
0.00E+00
2.00E+02
4.00E+02
6.00E+02
0.00E+00 2.00E+02 4.00E+02 6.00E+02 8.00E+02 1.00E+03 1.20E+03 1.40E+03
Z'/Ohm
-Z''/Ohm 6
54
3
210 -1
-2
6
54
3210
-1
-2
65 4 3
ж Sample AΔ Sample BÅ Sample C
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Alternative electrolyte, yttria-doped ceria YDC (10/20 mol%)
400 nm, 6 mol% / ss
342 nm, 7 mol% / La0.8Sr0.2FeO3
300°C
342 nm, 7 mol% / La0.8Sr0.2FeO3
0.E+00
2.E+05
4.E+05
6.E+05
8.E+05
1.E+06
0.E+00 2.E+05 4.E+05 6.E+05 8.E+05 1.E+06 1.E+06 1.E+06Z' (Ohms)
Z" (O
hms)
0.05V0.1V0.15V0.2V0.25V
3
4
5
YDC
laye
r
Electrode reaction
-7
-6
-5
-4
-3
-2
-1
010 15 20 25 30
(10000/T) / K -1
log (s
igma /
S.m
-1)
YSZ 20at% [7,10]
YDC 16at%
400°C 300°C500°C 200°C-7
-6
-5
-4
-3
-2
-1
010 15 20 25 30
(10000/T) / K -1
log (s
igma /
S.m
-1)
YSZ 20at% [7,10]
YDC 16at%
400°C 300°C500°C 200°C
- T > 420°C, σYDC > σYSZ - εr 10 x lower / bulk YDC: thin layer better dielectric material
E. Ballée et al., Chem. Mater., 2009, 21, 4614-4619 EFC 2013 Rome
• In3+ size close to Zr4+ – r(In3+)=0.80 A° – r(Zr4+)=0.84 A°
Ø Ionic & electronic conductivity = f(In3+ ratio)
ZrO2-In2O3 system
••Ο
ΧΟ ++→ VOInOIn Zr
ZrO
32 '2
32
2
-4
-3.5
-3
-2.5
-2
-1.5
-1
-0.5
00% 20% 40% 60% 80% 100%
In mol%
log σ
(S/c
m)
Ionic conductivity Electronic conductivity
-4
-3.5
-3
-2.5
-2
-1.5
-1
-0.5
00% 20% 40% 60% 80% 100%
In mol%
log σ
(S/c
m)
Ionic conductivity Electronic conductivity
A. Ringuedé, P. Mourot, C. Alvarez Lugano, J-C. Badot and M. Cassir, J. New Mat. for Electrochem. Syst. 9 (2006) 201-208
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30 40 50 60 70 802θ (°)
Inte
nsité
(u.a
)
¿
¿
¿ ¿
Þ
Þ
Þ
Þ
Þ
¿ZrO2 ÞLSM
(a)
(b)
(111
)
(200
)
(220
)
(311
)
Þ
IDZ ionic conductor
320 nm of IDZ (34 mol%) /LSM 480 nm of IDZ (26 mol% ) / LSM 380 nm of IDZ (22 mol%) / NiO-YSZ Well-covering, dense and uniform cubic-structured deposits
λKαCo= 1.78897 Å
(a) 320 nm IDZ; 34 mol% (b) 480 nm IDZ; 26 mol%
• Deposition at 300 °C
⇒ no annealing treatment
2 µm 1 µm 1 µm 2 µm
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Gradient Gradient 1 µm 1 µm
1,06 µm
ZrO2-In2O3 (gradient) / YSZ
Epaisseur désirée (nm)
Composition en InO1,5 désirée (mol%)
200 90 200 60 200 45 500 25
YSZ
IDZ
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Electrical behaviour of the gradient
7
8
9
10
11
12
13
14
15
11 12 13 14 15 16 17 18 19 20 21
10000/T /K-1
Log
((R
/e)/(Ω
/m))
YSZ30%50%65%90%gradient HT
300°C400°C500°C
% In ≤ 65 % ⇒ R with % In
65%
50% 30%
90%
% In = 90 % ⇒ R
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Theoretical/experimental approach of CeO2-based catalysts at the SOFC (or MCFC) anode
(Ph.D of T. Désaunay, sept. 2012) Ø Oxygen source at SOFC anode: enhancement of hydrogen oxidation /
would allow the direct oxidation of CH4 without carbon deposit Ø State of the surface: fundamental role / reactivity
Ø Understanding mechanisms at the molecular level: higher performance
Ø Theoretical approach of the behaviour of ceria and its interface reactivity by DFT
Ø Nanoparticles of CeO2 synthesised by hydrothermal route Ø
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Ø Reactivity: T-programmed reduction (TPR): T order: nanocubes (100) < nanowires (110) < nanooctahedra (111)
> > Ea (kJ/mol) : 70 < 130 < 430
Ø Thin-layered CeO2 / NiO-YSZ by ALD
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Al2O3 (102)
Y:ZrO2 (100)
SrTiO3 (100)
Non oriented
Thin layers for MCFC by ALD
H2 + CO2 + H2O ↓
Anode"Ni + 3% Cr"Li2CO3-Na2CO3/LiAlO2
Ni2+ → Ni (short-circuit)
LixNi1-xO → ↑"Cathode "O2 + CO2 ↑
!
Ni + 3% Cr"
Li2CO3-Na2CO3/LiAlO2
Thin layer < 1 µm"Ni/NiO
Protection of MCFC separator plates
Protection of the cathode cathode
Current collector Anticorrosion layer MCrAlY bond layer
Stainless steel
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Coatings
CeO2 TiO2 Nb2O5 Co3O4
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TiO2 + 2Li+ +CO32− → Li2TiO3 +CO2
LixTiyNiO3.59 ± 0.06 (x ≤ 0.5 and y ≤ 0.36): crystal structure similar to NiO
TiO2 coating (300 nm) / Ni in molten Li2CO3-K2CO3 at 650°C Before After 230 h Mapping: well-distributed mixed phase Ti-Ni-O
Sol. /
wt.ppm
Ni TiO2 / Ni (50 nm)
TiO2 / Ni (150 nm)
TiO2 /Ni (300 nm)
Ni 15 8.2 6.5 10
Ti 1.3 1.2 < 1
OCP evolution vs. time in Li2CO3-K2CO3 at 650OC, 230 h. a) Ni, b) TiO2 (50 nm), c) CeO2 (27 nm), d) Co3O4 (50 nm)
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Sample Ni Porous TiO2
50 nm CeO2
20 nm Co3O4 50 nm
Measured Value
(wt. ppm) 15 8 10 12
Conclusions Ø ALD deposits
– Crystalline at low T without annealing – Dense, conformal – Good composition and thickness control – Production of thin layers with composition gradient – Speed growth relatively low (15 nm/h IDZ)
Ø Pellets ≠ µ or nano-structured thin layers Ø Modification of the electrochemical properties with composition gradient Ø Correlation between nanostructures and electrochemical properties?
- More active area (surface kinetics enhanced) - Reduced interfacial electrode-electrolyte reactions
- Thermal constraints control (rapid ageing of the fuel cell materials) Ø Modelling effort required for complex materials surface organization Ø Use of thin layers in new high-temperature electrochemical devices
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