demonstration of a 20 w class high-temperature polymer electrolyte fuel cell stack with novel...
TRANSCRIPT
i n t e r n a t i o n a l j o u r n a l o f h y d r o g e n en e r g y 3 6 ( 2 0 1 1 ) 5 5 2 1e5 5 2 6
Avai lab le a t www.sc iencedi rec t .com
journa l homepage : www.e lsev ier . com/ loca te /he
Demonstration of a 20 W class high-temperature polymerelectrolyte fuel cell stack with novel fabrication ofa membrane electrode assembly
Hye-Jin Lee a,1, Byoung Gak Kim b,1, Dong Hoon Lee b,1, Se Jin Park b, Yongmin Kim b,Jeung Woo Lee c, Dirk Henkensmeier b, Suk Woo Namb, Hyoung-Juhn Kim b,*,Hwayong Kim a,**, Ju-Yong Kim d,***a School of Chemical and Biological Engineering, San 56-1, Sillinm-dong Gwanak-Gu, Seoul 151-744, South Koreab Fuel Cell Center, Korea Institute of Science and Technology, 39-1 Hawolgok, Seoul 136-791, South Koreac Fuel Cell R&D Center, POSCO Power, 13-9, Jukcheonri Hunghae-eup Buk-gu, Pohang City, Gyeonbuk, South KoreadCorporate R&D Center, Samsung SDI, 428-5 Gongse, Giheung, Yongin, Gyeonggido 446-577, South Korea
a r t i c l e i n f o
Article history:
Received 12 December 2010
Received in revised form
2 February 2011
Accepted 3 February 2011
Available online 5 March 2011
Keywords:
High-temperature polymer electro-
lyte fuel cell
Phosphoric acid-doped
polybenzimidazole
Membrane electrolyte assembly
Fuel cell stack
* Corresponding author. Tel.: þ82 2 958 5299** Corresponding author. Tel.: þ82 2 880 7406*** Corresponding author. Tel.: þ82 31 288 460
E-mail addresses: [email protected] (H.-1 Equally contributed to as a first author.
0360-3199/$ e see front matter Copyright ªdoi:10.1016/j.ijhydene.2011.02.014
a b s t r a c t
Acid-doped polybenzimidazole (PBI) membrane and polytetrafluoroethylene (PTFE)-based
electrodes are used for the membrane electrode assembly (MEA) in high-temperature
polymer electrolyte fuel cells (HTPEFCs). To find the optimum PTFE content for the catalyst
layer, the PTFE ratio in the electrodes is varied from 25 to 50 wt%. To improve the
performance of the electrodes, PBI is added to the catalyst layer. With a weight ratio of
PTFE to Pt/C of 45:55 (45 wt% PTFE in the catalyst layer), the fuel cell shows good perfor-
mance at 150 �C under non-humidified conditions. When 5 wt% PBI is added to the elec-
trodes, performance is further improved (250 mA cm�2 at 0.6 V). Our 20 W class HTPEFC
stack is fabricated with a novel MEA. This MEA consists of 8 layers (1 phosphoric acid-
doped PBI membrane, 2 electrodes, 1 sub-gasket, 2 gas-diffusion media, 2 gas-sealing
gaskets). The sub-gasket mitigates the destruction of a highly acid-doped PBI membrane
and provides long-term durability to the fuel cell stack. The stack operates for 1200 h
without noticeable cell degradation.
Copyright ª 2011, Hydrogen Energy Publications, LLC. Published by Elsevier Ltd. All rights
reserved.
1. Introduction However, low-temperature PEFCs (LTPEFCs) should be oper-
Fuel cells offer several advantages for solving problems such
as environmental contamination and fossil fuel diminish-
ment. Among various kinds of fuel cells, polymer electrolyte
fuel cells (PEFCs) have been in the spotlight because of their
fast start-up, low operation temperature and high efficiency.
; fax: þ82 2 958 5199.; fax: þ82 2 889 6695.8; fax: þ82 31 288 4646.J. Kim), [email protected]
2011, Hydrogen Energy P
ated below 100 �C and water management has to be carefully
controlled to achieve high performance of this type of cell. In
addition, LTPEFCs demand CO (carbon monoxide)-free
hydrogen as a fuel. For these reasons, high-temperature PEFCs
(HTPEFCs) (operating at >120 �C) have been studied to over-
come the drawbacks of LTPEFCs [1,2].
c.kr (H. Kim), [email protected] (J.-Y. Kim).
ublications, LLC. Published by Elsevier Ltd. All rights reserved.
i n t e rn a t i o n a l j o u r n a l o f h y d r o g e n en e r g y 3 6 ( 2 0 1 1 ) 5 5 2 1e5 5 2 65522
Most HTPEFCs employ acid-doped polybenzimidazole (PBI)
derivatives in the fabrication of a fuel cell membrane [2e4].
Although PBI itself does not have proton conductivity, it
develops proton conductivity after being doped with a strong
inorganic acid, such as phosphoric acid. Acid-doped PBI can be
prepared by two different methods: post acid-doping with PBI
membrane and in situ acid-doping by directmembrane casting
from a polymerization mixture in polyphosphoric acid (PPA)
[5]. The former method produces a membrane which has
strong mechanical strength, but a limited doping level. The
latter results in a high doping level, but low mechanical
strength. In order to obtain an acid-doped PBI membrane for
effective HTPEMFC operation, the two methods are used by
carefully controlling the acid-doping level; however, there has
been no solid strategy for fabricating a PBI membrane which
has a high doping level, uses an easy membrane-casting
method and exhibits strong mechanical strength.
Previously we reported several results which addressed the
synthesis, membrane fabrication, and fabrication of the
membrane electrode assembly (MEA) for PBI membranes. For
high-temperature fuel cell operation, in situ fuel cellmembrane
was fabricated from a polymerization mixture in PPA. In this
case, high proton conductivity could be obtained, but low
mechanical strength remained a problem for MEA fabrication
and long-term stability. In this report, we use a novel MEA
fabrication method that produces a very durable HTPEFC. The
MEA has an 8-layered structure consisting of 1 phosphoric
acid-doped PBI membrane, 2 electrodes, 1 sub-gasket, 2 gas-
diffusion media, and 2 gas-sealing gaskets (Fig. 1). Most
components of this MEA are similar to those of other types for
Fig. 1 e Schematic drawing of th
low-and high-temperature PEFCs. The unique component of
this MEA is a sub-gasket. The sub-gasket ensures that the
membrane structure maintains proton conductivity and long-
term durability. Commercialized MEAs of low-temperature
PEFCs are equipped with a sub-gasket which has at least the
same thickness as that of an electrolytemembrane [6,7]. In our
case, however, the thickness of the sub-gasket is thinner than
that of the phosphoric acid-doped PBI membrane. During
single cell fabrication, the phosphoric acid-doped PBI
membrane is squeezed only as far as the thickness of the sub-
gasket.Asa result, the structuredoesnotdegrade for single cell
and stack operation, resulting in excellent durability.
In order to achieve good performance of the MEA of our
HTPEFC, the electrode was also optimized. Recently, binders
such as polytetrafluoroethylene (PTFE) and PBI for the Pt/C
catalysthavebeenstudiedtofabricate theelectrodes [8,9]. Inthis
work,weusedamixtureof PTFEandPBI as thecatalyst binder to
provide goodproton conductionandmaintainapathway for air.
Using this type of MEA, a 20 W class HTPEFC stack was fabri-
cated. In the sections which follow, we present new findings
associated with our novel MEA and 20 W class HTPEFC stack
which demonstrate their capacity for long-term durability.
2. Experimental
2.1. Materials
3,3-Diaminobenzidine (99%, Aldrich), terephthalic acid (>99%,
TCI), isophthalic acid (>99%, TCI), phosphoric acid (85%,
e 8-layered MEA structure.
Fig. 2 e Comparison of MEA shapes after MEA fabrication
without (a) and with (b) a sub-gasket. Membrane: p-PBI.
i n t e r n a t i o n a l j o u r n a l o f h y d r o g e n en e r g y 3 6 ( 2 0 1 1 ) 5 5 2 1e5 5 2 6 5523
Aldrich) and polyphosphoric acid (PPA) (115% phosphoric acid
equivalent, Aldrich) were used as received. A 46.1 wt% Pt/C
catalyst (Tanaka), gas-diffusion cloth (withmicroporous layer,
HT1410-W from E-Tek), and 60 wt% PTFE dispersion in water
(Aldrich) were used for the MEA fabrication.
2.2. Synthesis of p-PBI (poly[2,20-(p-phenylene)-5,50-bibenzimidazole]) and membrane fabrication
3,3-Diaminobenzidine (3.9 g, 0.018 mol) and terephthalic acid
(3.0 g, 0.018 mol) were polymerized with polyphosphoric acid.
The reaction temperature was kept at 250 �C for 24 h and the
viscous polymer solution was poured onto a glass plate and
flattened by a doctor blade to obtain a uniform thickness
(300 mm). The membrane was maintained at an ambient
condition (25 �C, 45% relative humidity) and the polyphosphoric
acid was hydrolyzed to phosphoric acid. The p-PBI membrane
was used without a further phosphoric acid-doping process.
Fig. 3 e The polarization curves of MEAs with different wt%
in the electrode. A number preceded by P refers to the wt%
of PTFE in the electrode under dry state. Test conditions:
150 �C; non-humidified; ambient pressure; flow rate of H2
100 sccm and air 300 sccm.
2.3. Preparation of m-PBI (poly[2,20-(m-phenylene)-5,50-bibenzimidazole]) solution
The m-PBI was synthesized using a similar method as
described in Section 2.2. Instead of terephthalic acid, iso-
phthalic acid was used for the synthesis of m-PBI. After the
polymerizationwas finished, the polymermixturewas poured
into water. The fibrous polymer was washed with a 10 wt%
K2CO3 solution andwater several times to obtain the de-doped
m-PBI. Then it was dried under reduced pressure for 24 h at
60 �C. The dried m-PBI (0.15 g) was dissolved in 10 g of
dimethyl acetamide (DMAc).
2.4. Preparation of electrode
Typical procedure for the electrode with 45% PTFE under dry
state: Pt/C catalyst (1 g), PTFE dispersion (2 g), iso-propanol
(100 mL), water (25 mL) and with (or without) m-PBI solution
(4.1 g) prepared as the method in the section 2.3, were mixed
by a homogenizer for 1 h. The catalyst slurry was sprayed on
carbon cloth and dried in a vacuum oven to remove residual
solvents. The catalyst-loaded electrode was sintered at 350 �Cfor 30 min under a nitrogen atmosphere.
2.5. Single cell performance test
The catalyst-loaded electrodes and phosphoric acid-doped
p-PBI membrane were assembled to make MEA using a PTFE
sub-gasket (thickness: 250 mm) with (or without) hot-pressing
processing at 140 �C under 400 kPa for 4min. The active area of
the single cell was 10 cm2. The Pt loadings of both cathode and
anode were 1 mg cm�2, respectively. Dry hydrogen and air
were used and the cell temperature was kept at 150 �C.Polarization curves and impedance spectra were obtained by
the method described by Kim et al. [5].
2.6. Fabrication of the MEA and 20 W class PEFC stack
A 20W class high-temperature PEFC was fabricated by using
the MEAs as prepared in Section 2.4. The active area of the
Fig. 4 e Polarization curves of MEAs prepared with and
without a hot-pressing method. PTFE content: 45wt% in
the electrode under dry state. Test conditions: 150 �C; non-humidified; ambient pressure; flow rate of H2 100 sccm and
air 300 sccm.
Fig. 6 e Polarization curves of MEAs which were hot-
pressed with 5 wt% or 10 wt% m-PBI and without m-PBI in
electrodes. Numbers followed by P and PBI are the wt% of
PTFE and m-PBI, respectively, in the electrode under dry
state. The MEA was hot-pressed. Test conditions: 150 �C;non-humidified; ambient pressure; flow rate of H2
100 sccm and air 300 sccm.
Fig. 5 e Impedance spectra of MEAs fabricated with and
without a hot-pressing method at 0.85 V.
i n t e rn a t i o n a l j o u r n a l o f h y d r o g e n en e r g y 3 6 ( 2 0 1 1 ) 5 5 2 1e5 5 2 65524
MEA was 25 cm2. The stack was composed of 7 cells. Each cell
had an 8-layered structure (1 phosphoric acid-doped PBI
membrane, 2 electrodes, 1 sub-gaskets, 2 gas-diffusionmedia,
2 gas-sealing gaskets) (Fig. 1). We used graphite bipolar plates
which has serpentine channels for anode and cathode.
3. Results and discussion
3.1. MEA fabrication and cell performance
Highly acid-doped p-PBI membrane has a relatively low
mechanical strength.Themembranebreakseasilyduringsingle
cell preparation or fuel cell operation. The boundary of the
Fig. 7 e 20 W class HTFC. Active ar
activeareaisparticularlysusceptibletodamage,probablydueto
the pressure difference between the electrolyte membrane
under gas-diffusion media and the gas-sealing gaskets. Fig. 2
shows the MEA with and without a sub-gasket after single cell
fabrication. Without the sub-gasket, the membrane was
destroyed by the higher pressure under the gas-sealing gaskets.
In the case of single cell fabricationwith a sub-gasket, however,
destruction of the membrane was not observed.
The 8-layered MEA, which has a sub-gasket, was used for
the fuel cell operation at 150 �C under non-humidified
ea of MEA: 25 cm2; 7 cell stack.
Fig. 8 e Cell performance of 20 W class HTPEFC at 150 �C under non-humidified and ambient pressure. The MEA were
fabricated using hot-pressing method with 5 wt% m-PBI in electrodes. Active area of MEA: 25 cm2; 7 cell stack. (a) Constant
current operation at 5 A with 750 sccm of H2 and 2500 sccm of air; (b) IV curves initial, 600, 1200 h operation.
i n t e r n a t i o n a l j o u r n a l o f h y d r o g e n en e r g y 3 6 ( 2 0 1 1 ) 5 5 2 1e5 5 2 6 5525
conditions and ambient pressure. To determine the ideal PTFE
amount in the electrodes, we carried out experiments by
varying the weight ratio of PTFE from 25 to 50% in the elec-
trodes under dry state. As shown in Fig. 3, cell performance
improved when PTFE content increased, although there was
a limit after which cell performance was compromised. At
a PTFE weight percentage of 50, performance declined
precipitously. These results may occur because as the amount
of PTFE is enhanced, binding ability may improve, resulting in
Fig. 9 e Cell performance of 7 cells of a 20 W class HTPEFC at 1
a function of time at 5 Awith 750 sccm of H2 and 2500 sccm of air
difference between the best and the worst cell of the stack at 0
high cell performance, but with too much PTFE in the elec-
trodes, hydrogen and oxygen may be blocked and the resis-
tance of the electrode layer may increase.
In preparing the 8-layered MEA, we fabricated it both with
and without a hot-pressing method. To mitigate the resis-
tance between the membrane, the electrodes and the gas-
diffusion layers, we pressed theMEA at 140 �Cunder 40 KPa for
4 min. A performance comparison of cells containing MEAs
which were fabricated with and without a hot-pressing
50 �C under non-humidified and ambient pressure as
. (a) Initial; (b) 600 operation; (c) 1200 h operation (d) Current
.6 V in initial, 600 and 1200 h operations.
i n t e rn a t i o n a l j o u r n a l o f h y d r o g e n en e r g y 3 6 ( 2 0 1 1 ) 5 5 2 1e5 5 2 65526
method is shown in Fig. 4. The hot-pressed MEA resulted in
higher cell performance than with a pristine MEA. This was
confirmed by examining the impedance spectra (Fig. 5) which
showed that the Ohmic resistance of the hot-pressedMEAwas
smaller than that of the pristine one.
Catalyst binders, such as PBI and PTFE, were used for MEA
fabrication. PBI binder is excellent for three-phase boundary
formation. Previously we clarified the role of PBI and phos-
phoric acid in an electrode [10,11]. J. Lobato et al. [12] have also
reported on the importance of the ratio of PBI and phosphoric
acid in electrodes. PTFE binder, which has generally been used
in phosphoric acid fuel cells (PAFCs) [13], has the advantage of
promoting good transfer of fuel and air. In this reported work,
we used amixture of PTFE andm-PBI for the catalyst binder to
provide a good pathway for gases as well as proper proton
conduction. We fixed PTFE content at 45 wt% and varied the
content ofm-PBI to 5 and 10wt%. Fig. 6 shows the dependence
on cell performance of m-PBI content. When 5 wt%m-PBI was
added in the electrode, the cell performance of the MEA was
higher than that of pristine MEA without m-PBI in the elec-
trode. However, cell performance decreased when the 10 wt%
m-PBI was added in the electrode. Cell performance was very
dependent on them-PBI content in the electrode. Theremight
be an optimum combination for m-PBI and PTFE, so this shall
be the subject of our next experiment in an effort to improve
cell performance.
3.2. 20 W class high-temperature PEFC stack operation
Seven 8-layered MEAs, which were hot-pressed with 5 wt%
m-PBI in the electrodes, were used to fabricate a 20 W class
HTPEFC stack (Fig. 7). Fig. 8 presents the cell performance of
the stack as a function of time. Constant current operation at 5
A did not cause deterioration of the stack in 1200 h. IV curves
also indicated that after 600 and 1200 h of operation, perfor-
mance of the cells in the stack was not compromised.
During the stack operation, we tested the cell performance
of 7 cells of the stack (Fig. 9). Initially the 7 cells showed
different cell performance. The performance difference
between the best cell and the worst cell was 63 mA cm�2.
Surprisingly, as operation time increased, the difference
decreased. In addition, stack performancewas not affected, as
shown in Fig. 8. It is not clear why this phenomenon occurred.
One possible answer is that the phosphoric acid distribution
evened out in each cell because each MEA was equipped with
a sub-gasket whichmade the thickness of eachmembrane the
same. This could account for the similar performance of each
cell as operation time increased.
4. Conclusions
In order to improve HTPEFC performance, PTFE and m-PBI
were combined to make catalyst binder in the electrode. In
addition, a hot-pressing method was shown to be very effec-
tive for the mitigation of Ohmic resistance, resulting in high
cell performance. A novel MEA fabrication method was
developed for the acid-doped PBI membrane. It involved the
insertion of a sub-gasket to avoid deterioration of the PBI
membrane during cell fabrication and operation. We
fabricated a 20 W class HTPEFC stack using 7 MEAs. The stack
was operated for 1200 h without noticeable performance
degradation. We also found out that the 7 cells composing the
stack demonstrated similar performance, an outcome which
is not fully understood at this time. Electrochemical and
physical analysis of our MEA will be carried out to understand
the driving force behind these performance results.
Acknowledgements
This work was supported by the New and Renewable Energy
R&D Program (2008-N-FC12-J-01-2-100), and a grant
(M2009010025) from the Fundamental R&D Program for Core
Technology of Materials funded by the Ministry of Knowledge
Economy (MKE), Republic of Korea.
r e f e r e n c e s
[1] Wainright JS, Wang JT, Weng D, Savinell RF, Litt M. Acid-doped polybenzimidazoles: a new polymer electrolyte. JElectrochem Soc 1995;142:L121e3.
[2] Li Q, He R, Jensen JO, Bjerrum NJ. PBI-based polymermembranes for high temperature fuel cells-preparation,characterization and fuel cell demonstration. Fuel Cells 2004;4:147e59.
[3] Yu S, Xiao L, Benicewicz BC. Durability studies of PBI-basedhigh temperature PEMFCs. Fuel Cells 2008;8:165e74.
[4] Li M, Scott K. A polymer electrolyte membrane for hightemperature fuel cells to fit vehicle applications.Electrochimica Acta 2010;55:2123e8.
[5] Lee JW, Lee DY, Kim HJ, Nam SY, Choi JJ, Kim JY, et al.Synthesis and characterization of acid-dopedpolybenzimidazole membranes. J Membr Sci 2010;357:130e3.
[6] Numao Y, Oma A. JP2007e95669A.[7] Murthy M, Esayian M, Hobson A, MacKenzie S, Lee W, Van
Zee JW. Performance of a polymer electrolyte membrane fuelcell exposed to transient CO concentrations. J ElectrochemSoc 2001;148:A1141e7.
[8] Wannek C, Lehnert W, Mergel J. Membrane electrodeassemblies for high temperature polymer electrolyte fuelcells based on poly(2,5-benzimidazole) membrane withphosphoric acid impregnation via the catalyst layers. J PowerSources 2009;192:258e66.
[9] Pan C, Li Q, Jensen JO, He R, Cleemann LN, Nilsson MS, et al.Preparation and operation of gas diffusion electrodes forhigh-temperature proton exchange membrane fuel cells. JPower Sources 2007;172:278e86.
[10] Kim HJ, An JA, Kim JY, Eun YC, Cho SY, Yoon HK, et al.Polybenzimidazoles for high temperature fuel cellapplications. Macromol Rapid Commun 2004;25:1410e3.
[11] Kim JH, Kim HJ, Lim TH, Lee HI. Dependence of theperformance of a hightemperature polymer electrolyte fuelcell on phosphoric acid-doped polybenzimidazole ionomercontent in cathode layer. J Power Sources 2007;170:275e80.
[12] Lobaco J, Canizares P, Rodrigo MA, Linares JJ, Pinar FJ. Studyof the influence of the amount of PBI-H3PO4 in the catalystlayer of high temperature PEMFC. Int J Hydrogen Energy2010;35:1347e55.
[13] Song RH, Shin DR, Kim CS. New method of electrodefabrication for phosphoric acid fuel cell. Int J HydrogenEnergy 1998;23:1049e53.