Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte
It is the aim of the present work to address some of the aspects of optimized technological approach of manufacturing planar anode-bearing solid oxide fuel cells based on detailed investigation of such effects as electrolyte microcracking and degradation, taking into account weakening of its grain b...
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Інститут проблем матеріалознавства ім. І.М. Францевича НАН України
2010
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| Cite this: | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte / M.I. Lugovy, V.M. Slyunyayev, M.P. Brodnikovskyy // Электронная микроскопия и прочность материалов: Сб. научн . тр. — К.: ІПМ НАН України, 2010. — Вип. 17. — С. 82-89. — Бібліогр.: 21 назв. — англ. |
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Digital Library of Periodicals of National Academy of Sciences of Ukraine| _version_ | 1860238430912380928 |
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| author | Lugovy, M.I. Slyunyayev, V.M. Brodnikovskyy, M.P. |
| author_facet | Lugovy, M.I. Slyunyayev, V.M. Brodnikovskyy, M.P. |
| citation_txt | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte / M.I. Lugovy, V.M. Slyunyayev, M.P. Brodnikovskyy // Электронная микроскопия и прочность материалов: Сб. научн . тр. — К.: ІПМ НАН України, 2010. — Вип. 17. — С. 82-89. — Бібліогр.: 21 назв. — англ. |
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| container_title | Электронная микроскопия и прочность материалов |
| description | It is the aim of the present work to address some of the aspects of optimized technological approach of manufacturing planar anode-bearing solid oxide fuel cells based on detailed investigation of such effects as electrolyte microcracking and degradation, taking into account weakening of its grain boundaries due to impurity segregation during SOFC operation. The combination of electron microscopy research with model calculations permits both the specific energy of new surface creation in the electrolyte and critical parameters of the microcracking process to be determined. The accounting of segregation behavior features allows one to control electrolyte brittleness by using of optimal heat treatment regimes.
Розглядаються технологічні засади оптимізації виробництва пласких твердооксидних паливних комірок з несучим анодом на базі оксиду цирконію з добавками оксиду скандію. Наведено результати дослідження мікророзтріскування електроліту згаданого складу, що напилений електронно-променевим способом. При цьому береться до уваги ефект послаблення границь зерен внаслідок виникнення сегрегації домішкових атомів. Питома енергія створення нових поверхонь в електроліті та критичні параметри процесу його мікророзтріскування були визначені за допомогою комбінації електронно-мікроскопічних досліджень з модельними розрахунками. Врахування особливостей поведінки зернограничної сегрегації домішок дозволяє керувати крихкістю електроліту за допомогою використання оптимальних режимів термічної обробки.
Рассматриваются технологические основы разработки плоских твердооксидных топливных элементов с несущим анодом на основе диоксида циркония, стабилизированного оксидом скандия. Приведены результаты микрорастрескивания электролита, полученного электронно-лучевым напылением. При этом принимается во внимание эффект ослабления границ зерен вследствие сегрегации примесных атомов. С использованием комбинации электронной микроскопии с модельными расчетами определены удельная энергия образования новой поверхности в электролите и критические параметры его микрорастрескивания. Учет особенностей поведения зернограничной сегрегации примесей позволяет контролировать степень хрупкости электролита путем оптимизации режимов термической обработки.
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82
УДК 621.762:621.374:621.7.072
Technological aspects of solid oxide fuel cells
with scandia-stabilized zirconia electrolyte
M. I. Lugovy, V. M. Slyunyayev, M. P. Brodnikovskyy
It is the aim of the present work to address some of the aspects of optimized
technological approach of manufacturing planar anode-bearing solid oxide fuel cells
based on detailed investigation of such effects as electrolyte microcracking and
degradation, taking into account weakening of its grain boundaries due to impurity
segregation during SOFC operation. The combination of electron microscopy research
with model calculations permits both the specific energy of new surface creation in the
electrolyte and critical parameters of the microcracking process to be determined.
The accounting of segregation behavior features allows one to control electrolyte
brittleness by using of optimal heat treatment regimes.
Keywords: solid oxide fuel cell, electrolyte, microcracking, grain boundary, impurity.
Introduction
Promising options for future energy supply are offered by solid oxide fuel
cells (SOFC) due to the high electrical energy conversion efficiency they
display. The applications of SOFC are ranged from centralised MW scale gene-
ration through to localised applications at 100+ kW level for distributed
generation to local domestic generation on the 1 to 10 kW scale. Wide range of
other applications such as corrosion protection, uninterruptible power supply,
remote generation, and domestic appliances is also required. Commercialisation
of these applications will require even lower operating temperatures and
additional material improvements [1].
An air electrode (cathode), electrolyte, and a fuel electrode (anode) are main
constituents of a single SOFC [2] (fig. 1). The transport of oxide ions from the
electrolyte's interface with the air electrode to its interface with the fuel elec-
trode is the function of the electrolyte. The function of the cathode is to
facilitate the reduction of oxygen molecules to oxide ions transporting electrons
to the electrode/electrolyte interface to allow gas diffusion to and from this
interface. The function of the anode is to facilitate the oxidation of the fuel and
the transport of electrons from the electrolyte to the fuel electrode interface. In
addition the anode must allow diffusion of fuel gas to and exhaust gases away
from this interface.
Still, several major problems remain to be solved: degradation is too high
(between 0,5 and 2% per 1000 hours of operation, resulting in a ‘lifetime’
of around 10 000 to 30 000 operating hours); costs are too high (above
10 000 Euro/kW); intermittent operation (thermal and oxidation cycling) results
in increased degradation and/or failure; power density at temperatures below
1023 K is comparatively low [3]. These problems are a consequence of the high
temperatures, elevated pressures required for their operation, and the ceramics
materials properties [4].
High ion conductivity of scandia-stabilised-zirconia-based electrolyte offers
the potential for lowering the SOFC’s operating temperature with an ensuing
© M. I. Lugovy, V. M. Slyunyayev, M. P. Brodnikovskyy, 2010
83
Fig. 1. Planar solid oxide fuel cell
with ScSZ electrolyte.
reduction of corrosion and
degradation effects. SOFC
operating between 873 and
1073 K are generally labelled
“intermediate temperature”
SOFC (IT-SOFC). In addition,
the higher conductivity can also
be considered as a potential for
obtaining very much higher
power densities at operating temperatures above 1023 K. Using thin electrolyte
membranes with thicknesses between 5 and 50 µm is another way of
minimizing ohmic losses across the electrolyte. A promising technique to
produce thin films of electrolyte on thick anode substrates of planar geometry
is electron beam deposition (EBD). The anode supported planar SOFC cell has
become one of the most widespread SOFC types.
A challenge with the planar geometries is in obtaining mechanically stable
structures, as thin layer ceramics are inherently susceptible to failure when
subjected to moderate stress. If the anode is produced from a nickel oxide —
ScSZ composite and the electrolyte from scandia-stabilised zirconia, thermal
mismatch stresses keep the electrolyte layer under compression at room tempe-
rature and under tension at temperatures higher than the deposition temperature.
The mechanical properties of the SOFC components, including the electrolyte,
must be known in order to design an optimal SOFC structure. Typically, the
electrolyte shows microcracking due to residual stress [5].
The goal of the work is to develop an optimized technological approach of
manufacturing planar anode-bearing solid oxide fuel cells based on detailed
investigation of such effects as electrolyte microcracking and degradation,
taking into account weakening of its grain boundaries due to impurity
segregation during SOFC operation. The importance of such research is related
to the fact that SOFC’s mechanical integrity is a condition of its reliability
during long-term exploitation.
Experimental
The composition 10% (mol.) Sс2O3 — 1% (mol.) CeO2 — 89% (mol.) ZrO2
(10Sc1СеSZ) was found to be optimal for the electrolyte and as a constituent of
the anode [6]. SOFC anodes were fabricated with a traditional ceramic route.
Mixtures of 40% (wt.) NiO and 60% (wt.) 10Sc1CeSZ were ball-milled with
alcohol for 24 hours. Polyvinyl alcohol was used as pore-creating agent.
Specimens were made by uniaxial pressing using pressure ~20 MPa. These
were sintered at 1723 K for 2 hours in air. The anode substrates were found to
meet all necessary requirements concerning both strength and porosity (100—
150 MPa and 25—30%, respectively). The thickness of the anodes was 990 µm.
La0.8Sr0.2Co0.8Fe0.2O3 (LSCF) cathode material was prepared by
conventional solid-state reaction, using powders of La2O3, SrO, CoO and Fe2O3
(all 99% purity provided by Miranda-C). The ceramic route was done by ball-
milling stoichiometric quantities of the reagents with ethanol for 24 hours.
84
The resulted mixture was dried and calcinated in air at 900 oC for 4 hours in
order to develop the perovskite phase and ground again.
EBD technique was used for producing electrolyte films deposited on the
porous, non-reduced anode substrates. Hereafter the electrolyte — anode
layered system will be termed “half-cell”. “Half-cell” is a necessary
intermediate step of producing full fuel cell. EBD is one form of physical vapor
deposition (PVD). An electron beam is directed at a target pellet, in order to
ionize and melt the target material, which is then accelerated in an electrical
field and deposits on the specimen to be coated. The process is rather slow but
results in a very precise control of layer thickness and, when applied expertly,
delivers very thin, dense coatings, as needed for intermediate temperature
electrolytes [7]. These thin layers again reduce the overall resistance of the
electrolyte and further support the trend towards higher power density/lower
operating temperatures. Powder metallurgy routes were applied to produce
ScSZ specimens to be used for further electron-beam deposition experiments.
The dimensions of the cylindrically shaped specimens were about 4 mm in
diameter and about 8 mm in height (porosity approx. 15%). The substrates were
subjected to temperatures of 873, 1023 and 1173 K (deposition temperature)
during the deposition process. The deposition time of 15 min resulted in the
formation of electrolyte films with 10 µm in thickness.
Standard techniques, scanning electron microscopy and Image-Pro Plus
Software (Version 3.0.00.00, “Media Cybernetics”), were applied to obtain
electrolyte microstructure images and to evaluate microcrack sizes as well as
the number of microcracks in the electrolyte layer. Using Image-Pro Plus
Software for all considered states of electrolyte, the length of each microcrack
observed in corresponding image was measured. The microcrack density was
calculated as:
∑
=
=
AN
i
if c
A
f
1
21 , (1)
where ic is the effective length of the i-th microcrack, and AN is the number of
microcracks on the scanned area A (in our case =A 45000 µm2).
Results and discussion
It is of top interest to know mechanical properties of EBD 10Sc1СеSZ
electrolyte in order to optimize fuel cell processing. One of the possible
approaches to characterize the mechanical properties of EBD electrolyte films is
to use heat treatment of half-cells, i. e. annealing at various temperatures above
deposition temperature followed by electron microscopy investigation of the
electrolyte surface. The annealing creates equibiaxial stress states with tensile
stress in the electrolyte, whose value depends on the difference ∆T between
annealing temperature and deposition temperature [5]. Electron microscopy
investigations of the electrolyte surface have allowed the density of microcracks
arising due to tensile residual stresses in the annealed electrolyte to be
determined (fig. 2).
The initial data for thermal stress calculation in half-cells were established
experimentally and via literature survey. The elastic modulus for the anode
material was found to be 81 GPa from four point bending tests. The elastic
modulus of an undamaged electrolyte was adopted to be 200 GPa [8]. It is
85
Fig. 2. Microstructure of EBD 10Sc1 CeSZ electrolyte film after deposition
and annealing: а — deposition at 1173 K, annealing at 1473 K; b — deposition at 873 K,
annealing at 1178 K; c — deposition at 1023 K, annealing at 1473 K; d —
deposition at 873 K, annealing at 1473 K.
known that the elastic modulus of ceramics as a rule demonstrates a dependence
on temperature. For example, the existence of such dependence for yttria-
stabilized zirconia (YSZ) is shown in [9] where a substantial scattering of
experimental data is observed. The scattering complicates the determination of a
reliable dependence of elastic modulus on temperature. To the best of our
knowledge, the temperature dependence of the elastic modulus for 10Sc1СеSZ
is not available from literature. Therefore, as a first approximation, a constant
value of the elastic modulus is used for calculation in this work. The Poisson
ratios of anode and electrolyte were adopted to be 0,3 and 0,31, respectively [9].
The coefficient of thermal expansion for the anode was found experimentally to
be 11,7⋅10-6 К-1. The coefficient of thermal expansion for the electrolyte was
adopted to be 1⋅10-5 К-1 [10]. Note that non-reduced anode substrate was used in
this work. In such a way, there are not particles of pure nickel in the anode. This
means that creep processes in the anode during annealing were negligible,
simplifying residual stress calculation.
It is found that the microcrack density is negligible at ∆T = 150 K
demonstrating the practical absence of microcracking due to stresses associated
with this temperature difference. Increasing the temperature difference gives
rise to a growth of the microcrack density which promotes the significant
decrease of the electrolyte elastic modulus and Poisson ratio [11]. In turn, this
results in decreasing effective thermal stresses in the electrolyte. The effective
elastic properties of the electrolyte (Young modulus E, Poisson ratio ν) and
acting thermal stresses σ corresponding to different ∆T are listed in table. The
dependence of the tensile stresses on microcrack density can be compared with
the model calculations made in [5].
86
The effective elastic properties of 10Sc1CeSZ electrolyte film and thermal
stresses corresponding to different ∆T
∆Т, K ff E, GPa ν σ, MPa
150 0,039 194 0,30 60,6
300 0,392 147 0,23 85,6
305 0,473 138 0,21 80,6
375 1,358 69 0,11 45,0
450 2,103 38 0,06 28,9
460 2,414 30 0,05 23,0
600 3,365 14 0,02 13,9
Note that the combination of experimental observations of microcrack
density at different annealing temperatures with model calculations [5, 11—15]
allows the critical parameters of electrolyte failure, such as maximum strain
energy density and strain energy density corresponding to microcracking
initiation, as well as the corresponding stresses to be determined.The parameter
necessary for model calculations but unknown at this stage is the specific
energy of new surface creation γ. An attempt was made to determine this
parameter for the electrolyte material analyzing the experimental data. The lower
boundary γl and upper boundary γu of parameter γ were found to equal 0,035
аnd 0,037 J/m2, respectively [5]. This means the best estimation of the specific
energy of new surface creation (with accuracy of 3%) is γ = 0,036 J/m2.
The question arises to what measure the obtained value of the specific energy
of new surface creation is realistic and how it compares with literature data. It is
shown earlier that the value of the specific energy of new surface creation
(0,036 J/m2) for 10Sc1CeSZ electrolyte is reduced essentially in comparison with
specific surface energy values of zirconia-based ceramics given in literature [5].
The main reason of the reduction in our opinion can be attributed to the
intercrystalline fracture mode of electrolyte film. The energy of intergranular
fracture of polycrystalline materials is known to be decreased to some extent com-
pared to the energy of transcrystalline fracture. The decrease is widely considered to
be associated with the occurrence of impurity atoms and their segregation to grain
boundaries. The segregation is known to affect both mechanical properties and
conductivity of ceramics [16—19]. In addition to this possible impurity effect, in
our opinion, a second reason for the low specific energy of new surface creation of
electrolyte film cannot be ruled out. This is associated with an intrinsic weakness
of grain boundaries of the electrolyte film resulting from EBD processing and from
its columnar structure. Considering above arguments, it is evident that the energy of
free surfaces formed upon intercrystalline brittle failure should be used in our model
calculations instead of the surface energy.
The critical parameters of electrolyte microcracking were calculated using
the model developed in [5]. The strain energy density corresponding to micro-
cracking initiation and maximum strain energy density were established to be
0,017 MPа аnd 0,027 МPа, respectively. The stress which corresponds to micro-
cracking initiation, maximum stress and stress corresponding to localised
microcracking initiation were found to be 82, 100 аnd 95 МPа, respectively.
The microcrack density corresponding to maximum stress and to localised
microcracking initiation were found to equal 0,077 and 0,226, respectively.
87
The values for the temperature difference ∆T corresponding to
microcracking initiation, the maximum stress and the maximum strain energy
density were found taking into account the above critical parameters. The
temperature differences are 195, 257 аnd 283 К, respectively. The temperature
differences used in this work were 150, 300, 305, 375, 450, 460, аnd 600 К.
Therefore, it is evident that the temperature difference of 150 К has not caused
any microcracking, while temperature differences of 300, 305, 375, 450, 460,
аnd 600 К were more than 283 К, thus corresponding to localised
microcracking. Note also that the experimental determination of microcrack
density in the electrolyte in conditions being within the range from micro-
crack initiation to maximum stress is a complicated task due to the fact that
the corresponding microcrack densities are not far from the so-called
background value which is observed in practically non-cracked material. Thus,
it is realistic for scattered microcracking to reveal the conditions after maximum
stress, i.e., being within the range from maximum stress to maximum strain
energy density. In our case this is the range of temperature difference from 257
tо 283 К which is a narrow temperature interval of 26 К only. Accounting also
for the occurrence of statistical deviations in the microstructure of the elec-
trolyte film, it is a difficult task to fit the annealing conditions into the
temperature range of distinct scattered microcracking.
It is known that the small value of parameter γ resulting in intercrystalline
fracture of electrolyte is mainly associated with the occurrence of impurity
atoms and their segregation to grain boundaries. It was shown earlier [20, 21]
two main kinetic factors (impossibility to reach the equilibrium segregation
level in conditions of finite time of exposure as well as segregation increment
through cooling) result in the non-monotonous temperature dependence of
segregation in polycrystalline materials. The accounting of non-monotonous
temperature dependence of segregation allows temperature ranges in which
susceptibility of electrolyte material to intergranular brittleness increases to be
predicted. One of ways to use the approach is to calculate “time-temperature”
diagrams of material brittleness. Finally, it allows controlling electrolyte
brittleness by using of optimal heat treatment regimes.
Conclusions
The results obtained can be summarized as follows. The combination of
electron microscopy data with model calculations permits both the specific
energy of new surface creation of the electrolyte and critical parameters of the
microcracking process to be determined. The best estimation of the specific
energy of new surface creation (with an accuracy of 3%) is γ = 0,036 J/m2. The
strain energy density of microcracking initiation and maximal strain energy
density are 0,017 and 0,027 MPa, respectively. The mechanical stress
corresponding to microcracking initiation is 82 MPa; the maximum mechanical
stress is 100 MPa; the mechanical stress corresponding to initiation of localised
microcracking is 95 MPa. The microcrack densities which correspond to
maximal stress and to the initiation of localised microcracking are 0,077 аnd
0,226, respectively. The annealing-induced electrolyte microcracking described
here corresponds to localised microcracking, when each next structural element
fails mainly at existing microcrack tips. Detailed characterization of electrolyte
microcracking is a key issue of SOFC design to prevent electrolyte leaking.
88
The occurrence of impurity atoms and their segregation to grain boundaries
results in the small value of the specific energy of new surface creation and in
intercrystalline fracture of electrolyte. The accounting of non-monotonous
temperature dependence of segregation allows one to control electrolyte
brittleness by using of optimal heat treatment regimes.
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Технологічні засади виробництва паливних комірок
з електролітом на базі оксиду цирконію з добавками
оксиду скандію
М. І. Луговий, В. М. Слюняєв, М. П. Бродніковський
Розглядаються технологічні засади оптимізації виробництва пласких
твердооксидних паливних комірок з несучим анодом на базі оксиду цирконію з
добавками оксиду скандію. Наведено результати дослідження мікророзтріску-
вання електроліту згаданого складу, що напилений електронно-променевим
способом. При цьому береться до уваги ефект послаблення границь зерен внаслідок
виникнення сегрегації домішкових атомів. Питома енергія створення нових
поверхонь в електроліті та критичні параметри процесу його мікророзтріскування
були визначені за допомогою комбінації електронно-мікроскопічних досліджень з
модельними розрахунками. Врахування особливостей поведінки зернограничної
сегрегації домішок дозволяє керувати крихкістю електроліту за допомогою
використання оптимальних режимів термічної обробки.
Ключові слова: твердооксидні паливні комірки, електроліт, мікророзтріскування,
границя зерна, домішки.
Технологические основы разработки топливных элементов
с электролитом на основе оксида циркония
с добавками оксида скандия
Н. И. Луговой, В. Н. Слюняев, Н. П. Бродниковский
Рассматриваются технологические основы разработки плоских твердооксидных
топливных элементов с несущим анодом на основе диоксида циркония,
стабилизированного оксидом скандия. Приведены результаты микрорас-
трескивания электролита, полученного электронно-лучевым напылением. При
этом принимается во внимание эффект ослабления границ зерен вследствие
сегрегации примесных атомов. С использованием комбинации электронной
микроскопии с модельными расчетами определены удельная энергия образования
новой поверхности в электролите и критические параметры его
микрорастрескивания. Учет особенностей поведения зернограничной сегрегации
примесей позволяет контролировать степень хрупкости электролита путем
оптимизации режимов термической обработки.
Ключевые слова: твердооксидные топливные элементы, электролит, микрорас-
трескивание, граница зерна, примесь.
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| id | nasplib_isofts_kiev_ua-123456789-63518 |
| institution | Digital Library of Periodicals of National Academy of Sciences of Ukraine |
| issn | XXXX-0048 |
| language | English |
| last_indexed | 2025-12-07T18:27:01Z |
| publishDate | 2010 |
| publisher | Інститут проблем матеріалознавства ім. І.М. Францевича НАН України |
| record_format | dspace |
| spelling | Lugovy, M.I. Slyunyayev, V.M. Brodnikovskyy, M.P. 2014-06-02T20:59:26Z 2014-06-02T20:59:26Z 2010 Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte / M.I. Lugovy, V.M. Slyunyayev, M.P. Brodnikovskyy // Электронная микроскопия и прочность материалов: Сб. научн . тр. — К.: ІПМ НАН України, 2010. — Вип. 17. — С. 82-89. — Бібліогр.: 21 назв. — англ. XXXX-0048 https://nasplib.isofts.kiev.ua/handle/123456789/63518 621.762:621.374:621.7.072 It is the aim of the present work to address some of the aspects of optimized technological approach of manufacturing planar anode-bearing solid oxide fuel cells based on detailed investigation of such effects as electrolyte microcracking and degradation, taking into account weakening of its grain boundaries due to impurity segregation during SOFC operation. The combination of electron microscopy research with model calculations permits both the specific energy of new surface creation in the electrolyte and critical parameters of the microcracking process to be determined. The accounting of segregation behavior features allows one to control electrolyte brittleness by using of optimal heat treatment regimes. Розглядаються технологічні засади оптимізації виробництва пласких твердооксидних паливних комірок з несучим анодом на базі оксиду цирконію з добавками оксиду скандію. Наведено результати дослідження мікророзтріскування електроліту згаданого складу, що напилений електронно-променевим способом. При цьому береться до уваги ефект послаблення границь зерен внаслідок виникнення сегрегації домішкових атомів. Питома енергія створення нових поверхонь в електроліті та критичні параметри процесу його мікророзтріскування були визначені за допомогою комбінації електронно-мікроскопічних досліджень з модельними розрахунками. Врахування особливостей поведінки зернограничної сегрегації домішок дозволяє керувати крихкістю електроліту за допомогою використання оптимальних режимів термічної обробки. Рассматриваются технологические основы разработки плоских твердооксидных топливных элементов с несущим анодом на основе диоксида циркония, стабилизированного оксидом скандия. Приведены результаты микрорастрескивания электролита, полученного электронно-лучевым напылением. При этом принимается во внимание эффект ослабления границ зерен вследствие сегрегации примесных атомов. С использованием комбинации электронной микроскопии с модельными расчетами определены удельная энергия образования новой поверхности в электролите и критические параметры его микрорастрескивания. Учет особенностей поведения зернограничной сегрегации примесей позволяет контролировать степень хрупкости электролита путем оптимизации режимов термической обработки. en Інститут проблем матеріалознавства ім. І.М. Францевича НАН України Электронная микроскопия и прочность материалов Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte Технологічні засади виробництва паливних комірок з електролітом на базі оксиду цирконію з добавками оксиду скандію Технологические основы разработки топливных элементов с электролитом на основе оксида циркония с добавками оксида скандия Article published earlier |
| spellingShingle | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte Lugovy, M.I. Slyunyayev, V.M. Brodnikovskyy, M.P. |
| title | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte |
| title_alt | Технологічні засади виробництва паливних комірок з електролітом на базі оксиду цирконію з добавками оксиду скандію Технологические основы разработки топливных элементов с электролитом на основе оксида циркония с добавками оксида скандия |
| title_full | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte |
| title_fullStr | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte |
| title_full_unstemmed | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte |
| title_short | Technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte |
| title_sort | technological aspects of solid oxide fuel cells with scandia-stabilized zirconia electrolyte |
| url | https://nasplib.isofts.kiev.ua/handle/123456789/63518 |
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