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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 ) 8 5 5 0e8 5 5 6
Avai lab le at www.sc iencedi rect .com
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A novel phosphoric acid loaded quaternary 1,4-diazabicyclo-[2.2.2]-octane polysulfone membrane for intermediatetemperature fuel cells
Xu Wang a,*, Chenxi Xu a, Bernard T. Golding b, Masih Sadeghi b, Yuancheng Cao a,Keith Scott a
aSchool of Chemical Engineering and Advanced Materials, Merz Court, Newcastle upon Tyne NE1 7RU, UKb School of Chemistry, Bedson Building, Newcastle University, Newcastle upon Tyne NE1 7RU, UK
a r t i c l e i n f o
Article history:
Received 23 February 2011
Received in revised form
20 March 2011
Accepted 26 March 2011
Available online 29 April 2011
Keywords:
Phosphoric acid loaded membrane
DABCO
Polysulfone
Chloromethylation
Quaternization
Fuel cell
* Corresponding author.E-mail address: [email protected] (X. W
0360-3199/$ e see front matter Copyright ªdoi:10.1016/j.ijhydene.2011.03.143
a b s t r a c t
Phosphoric acid loaded quaternary 1,4-diazabicyclo-[2.2.2]-octane (DABCO) polysulfone
was synthesised with different degrees of substitution (DS) and the membranes were
characterized. The polymer structure was investigated using NMR and FT-IR spectra. The
effect of DS on ionic conductivity and fuel cell performance are described. Conductivities of
0.12 and 0.064 S cm�1 were achieved for the high degree of substitution membrane (DS106)
and low degree of substitution membrane (DS58), respectively. Fuel cell tests gave a high
power output of 400 mW cm�2 using H2 and O2 at 150 �C and atmospheric pressure.
Therefore, PA/QDPSU membrane has potential applications for intermediate temperature
fuel cells (ITFCs).
Copyright ª 2011, Hydrogen Energy Publications, LLC. Published by Elsevier Ltd. All rights
reserved.
1. Introduction at elevated temperature (>120 �C) offers a number of potential
Fuel cells are a key enabling technology for the future
hydrogen economy. Nafion based proton exchangemembrane
fuel cells (PEMFCs) play an important role for fuel cell devel-
opment. However, the high cost of Nafion membrane and Pt
group catalysts hinders the commercialization and further
development of PEMFC. In addition, it is sensitive to carbon
monoxide which can lead to irreversible adsorption on the
catalyst and the complex PEMFC system experiences reduced
efficiency due to water management requirements. To over-
come the shortcomings of low temperature PEMFC, operation
ang).2011, Hydrogen Energy P
advantages: a) high CO tolerance, b) faster kinetics, c) avoid-
ance of cathode flooding, d) increased system efficiency by
removing water management units [1].
Compared to aqueous phosphoric acid fuel cells (PAFCs)
operateathigher temperatures (150e200 �C) thanPEMFCs, solid
state electrolytes provide advantages such as a less corrosive
environment for catalysts and lower internal resistance losses.
Thephosphoric acid loadedpolybenzimidazole (PBI) is thebest-
known example which has produced reasonably successful
membranes for fuel cells with excellent thermal, chemical
stability and good conductivity [1]. A number of insoluble
ublications, LLC. Published by Elsevier Ltd. All rights reserved.
Fig. 1 e Synthesis scheme of quaternary DABCO
polysulfone.
Fig. 3 e FT-IR spectra of QDPSU and PA/QDPSU.
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 ) 8 5 5 0e8 5 5 6 8551
heteropolyacids (e.g.Cs2.5H0.5PMo12O40andCs-HPAs)wereused
for PBI compositemembrane to improve the ionic conductivity
of PBImembrane for high and lowphosphoric acid doping level
[2,3]. Recently, a TiO2/PBI composite membrane was prepared
by Lobato and co-workers, they found the water retention and
acid loading level were improved compared to pristine PBI
which leading toahighconductivityof (0.18Scm�1 at125 �C) [4].
Fig. 2 e 1H NMR spectra of d
Such composite membrane gave a peak power density of
800 mW cm�1 at 150 �C. Sulfonated poly (ether ether ketone)
(SPEEK) was characterized and the increase in degree of sulfo-
nation resulted in increased glassy transition temperature (Tg)
and enhanced membrane hydrophilicity which lead to
a improved proton conductivity [5]. Xing et al. synthesised
a sulfonated poly (biphenyl ether sulfone) membranes exhibi-
ted a good conductivity (0.18 S cm�1 at 25 �C) and high thermal
stability (up to 280 �C) [6]. Lately, they reported a montmoril-
lonite/sulfonated poly (phenylether sulfone)/PTFE composite
membrane with low swelling ratio and good stability at high
temperature and high strength conditions [7].
As an alternative method of preparing PEM for ITFCs, Li
et al. reported quaternized polymers as matrices for H3PO4
and they added that the quaternary ammonium group is
stable in the operating condition of ITFCs and it has a good
ifferent DS of CM-PSU.
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 ) 8 5 5 0e8 5 5 68552
bonding with phosphoric acid [8,9]. Our previous work on
quaternary ammonium polysulfone (QAPSU) loaded with
H3PO4 exhibited a promising fuel cell performance (700
mW cm�1 at 150 �C and 1 bar pressure) [9,10]. There are still
few reports on quaternary ammonium polymers for ITFCs
compared to the reports on PBI based composite membranes
and sulfonated polymer membranes. In this work, a quater-
nary 1,4-diazabicyclo-[2.2.2]-octane (DABCO) polysulfone
(QDPSU) was synthesised with different degrees of substitu-
tion (DS). Compared to the synthetic method for QAPSU, the
carcinogenic chloromethyl methyl ether was replaced by
a safer chloromethylation procedure (in-situ generation of
chloromethyl methyl ether).
Fig. 4 e SEM images and element maps of PA/QDPSU-DS 58, a)
e) EDX analysis.
2. Experimental
2.1. Synthesis of quaternary DABCO polysulfone
The synthesis of QDPSU was achieved by two steps as shown
in Fig. 1. First, the method for synthesis of choloromethylated
polysulfone (CM-PSU) by a FriedeleCrafts like reaction was
used, as developed by Avram and co-workers [11]. 10 g
(2.26 mmol) polysulfone (P-1700, Udel) was dissolved in
400 cm3 (mL) of 1,2-dichloroethane. 6.78 g (22.6 mmol) para-
formaldehyde and 24.6 g (22.6 mmol) trimethylchlorosilane
were added to the solution with magnetic stirring. Stannic
and b) cross-section view, c) phosphorous, d) sulphur and
Fig. 5 e Ionic conductivity of a) different degree of
substitution PA/QDPSU membrane and b) Arrhenius plot
obtained from ionic conductivity data.
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 ) 8 5 5 0e8 5 5 6 8553
chloride 1.178 (0.452 mmol) was added dropwise and the
reaction proceeded for 12e72 h at 50 �C, to produce different
degrees of substitution of CM-PSU. The white CM-PSU was
precipitated in high purity ethanol (99.9%) to remove the
excess of reactants. The product was purified by dissolving in
dimethylacetamide (DMAc), filtering and precipitating with
distilledwater several times. After that treatment, the product
was dried in high vacuum to remove any residual solvent and
kept in a vacuum before further use.
In order to obtain non-crosslinked QDPSU, the quaterni-
zation at a different degree of substitution (DS) was completed
by adding CM-PSU and DABCO in DMAc in a molar ratio of
1(eCH2Cl):5(DABCO). Themixture was stirred at 80 �C for 14 h,
whereupon the product was precipitated using diethyl ether
and dried in a vacuum.
To preparemembranes, QDPSUwas dissolved in DMAc and
the solutionwas cast onto an optical glass at 60 �C overnight to
evaporate the solvent. QDPSU membrane was immersed in
11.0 M phosphoric acid at room temperature for three days to
obtain the PA/QDPSUmembrane. All the chemicals were used
as received.
2.2. 1H NMR analysis
1H NMR (400 MHz) was performed on JEOL-ECS 400 using
deuterochloroform as the solvent and tetramethylsilane
(TMS) as the internal reference.
2.3. SEM and EDX analysis
A low vacuum environmental scanning electron microscopy
(ESEM, JSM-5300LV, Japan) incorporated with energy disper-
sive X-ray (EDX) spectroscopy was used to investigate the
morphology andmicrostructure of PA/QDPSUmembrane. The
membranewas immersed in liquid N2 for 10min andwas then
broken off to investigate the morphology of membrane cross-
section.
2.4. FT-IR analysis
Fourier transform infrared spectroscopy (FT-IR) of samples
was measured on a Varian 800 FT-IR spectrometer system
between 4000 and 400 cm�1.
2.5. Ionic conductivity measurement
A four-point probe technique was used for membrane
conductivity measurement. The membrane was contacted
with platinum foils and connected to a frequency response
analyser (FRA, Voltech TF2000, UK). All samples were cut into
1 cm wide, 5 cm long strips and placed on the platinum foil
with 0.5 cm gap between them. AC impedancemeasurements
were carried out at frequencies between 1 and 20 kHz. The
polymer membranes were held at the desired conditions of
temperature for 30 min to reach steady state.
The final results were calculated using Equation (1):
s ¼ id=vA (1)
Where s is the membrane conductivity (S cm�1), i is the
response current, v is the response voltage, d is the distance
between platinum foil and A is the membrane area of cross-
section.
2.6. MEA preparation and fuel cell test
Catalyst inks were prepared by blending carbon-supported
catalysts (50 wt.% Pt/C, Alfa Aesar) and polytetrafluoro-
ethylene (PTFE) solution (60 wt.% Aldrich) in a watereethanol
mixture under ultrasonic vibration for 10 min [2,12]. Gas
diffusion electrodes (carbon paper) incorporated with wet
proofed micro-porous layer (H2315 T10AC1), obtained from
Freudenburg (FFCCT, Germany), were used as substrates to
deposit the catalyst layer for both anode and cathode. The
catalyst inks were sprayed onto the micro-porous gas diffu-
sion layer, at 100 �C, and the electrodes were held at
a temperature of 150 �C for 2 h. The Pt loading was
0.7 mg cm�2. The required amount of PA acid, which was
diluted with a water/ethanol mixture, was added to the
surface of the electrodes by means of a micropipette and
electrodes were kept in an oven, at 80 �C, for 1 h to dry
the residue of water/ethanolmixture [12]. TheMEAwas finally
obtained by hot pressing the electrodes on 4.5 mol% phos-
phoric acid loaded membranes at 150 �C for 10 min at a pres-
sure of 40 kg cm�2.
Table 1 e Membrane properties of QDPSU.
Sample Degree ofsubstitution/%
Doping level, % Conductivity/S cm�1,@150 �C
Ea/kJ mol�1 Thickness/mm
PA/QDPSU�58 58 102b 0.06 13.2 55
PA/QDPSU�106 106 193c 0.12 12.8 65
QDPSU�180a 180 e e e e
a Brittle in the presence of water.
b Equivalent to 4.6 per repeating unit (PRU).
c Equivalent to 8.6 per repeating unit (PRU).
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 ) 8 5 5 0e8 5 5 68554
The catalyst ink was prepared either by sonicating Pt/C
(50 wt.%, Alfa Aesar) and PTFE dispersion (60% wt., Aldrich) in
a watereethanol mixture, for PTFE based MEAs. The MEA was
fixed between two high-density graphite blocks (impregnated
withphenolic resin)with parallel gas flowchannels. The active
electrode area was 1 cm2. Electric cartridge heaters were
mounted at the rear of the graphite blocks to maintain the
desired temperature, which was monitored by imbedded
thermocouples and controlled with a temperature controller.
Gold-plated steel bolts were screwed into the blocks to allow
electrical contact. H2 and O2were fed to the cell at flow rates of
0.4 and 0.7 dm3 min�1, respectively. These flow rates were
some 4 times more than stoichiometric requirements corre-
sponding to themaximumcurrent obtained from the cell tests.
Fig. 6 e Fuel cell performance using different DS of
PA/QDPSU, a) DS58, b) DS106, at 150 �C, 0.7 mgPt cmL2
(50 wt.% Pt/C) for both anode and cathode, under
atmospheric pressure, dry gases.
3. Results and discussion
3.1. 1H NMR spectra
The NMR spectra for pristine PSU and CM-PSU (DS 58 and 106)
are shown in Fig. 2. In all spectra, the characteristics of poly-
sulfone backbone were found. The multi-peaks of protons (a,
b, c, d, f, g and h position) on aromatic ring are in the region
between 6.8 and 7.8 ppm. The proton peak at e position on CH3
is at 1.7 ppm. The peaks at 7.3 ppm and 1.6 ppm are attributed
by CDCl3 and H2O respectively. In the spectra of CM-PSU, the
appearance of new peak (i) at 4.6 ppm indicates the formation
of chloromethylated polysulfone (CH2Cl), based on the calcu-
lation of integrated area of the peak, the degree of substitution
(DS) was obtained using Equation (2) [13]:
DS ¼ 2AHi=AHg � 100% (2)
Where AHiand AHg are integral area of Hi (i position, proton in
�CH2Cl) and Hg (g position, proton adjacent to�SO2� group in
the aromatic ring) in the spectra of CM-PSU.
For the chloromethylation reaction time of 12 and 32 h, the
different DS of PSU were 58 and 106% (DS58 and DS106),
respectively. The 1H NMR spectra suggest the successful
synthesis of chloromethylated polysulfone with different DS.
3.2. FT-IR
Fig. 3 shows the infrared spectra of QDPSU and PA/QDPSU. For
both membranes, the O and S]O vibra-
tion peaks are found at 1241 and 1375 cm�1. The small peaks
at 2924 cm�1, 1617 cm�1 and the sharp peak at 1487 cm�1 are
attributed by quaternary ammonium group stretching vibra-
tion [14]. For PA/QDPSU membrane, a significant vibration
peakwas found at 966 cm�1 is attributed by the P]O vibration.
The data suggest the successful preparation of QDPSU and
PA/QDPSU membranes.
3.3. SEM and EDX
The morphology of PA/QDPSU membrane was investigated
using scanning electron microscopy (SEM) and energy
dispersive X-ray (EDX). The SEM images (Fig. 4) of the
membrane cross-section reveal a dense and non-porous
structure as shown in Fig. 4a and b. The element mapping of
P and S as shown in Fig. 4c and d, further suggest that the
homogenous structure of PA/QDPSU membrane was formed.
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 ) 8 5 5 0e8 5 5 6 8555
In Fig. 4e, the EDX analysis of PA/QDPSU shows C, S
element at 0.25 and 2.4 keV, respectively, which are contrib-
uted by polysulfone. The Al element peak was contributed by
the sample holder. The significant P element peak at 2.0 keV
suggests a complete substitution of Cl� to H2PO4� after 3 days
doping at room temperature. Thus, the degree of chlor-
omethylation is the same as the degree of substitution (DS)
after quaternization with DABCO.
3.4. Ionic conductivity
Fig.5a shows the variation of ionic conductivity with temper-
ature for the membranes prepared in this work. The conduc-
tivities of the DS106 membrane were approximately twice
those of the DS58 membrane and increased with temperature
in the range of 80e150 �C under non-humidified conditions.
Conductivities of 0.12 and 0.064 S cm�1 were achieved for
DS106 and DS58 at 150 �C, respectively. The data suggest that
the ionic conductivity of QDPSU depended upon the DS of PSU.
Higher DS of QDPSU was synthesised, however, DS180
membrane is too brittle in the presence of water and thus is
not suitable for fuel cell applications.
Fig. 5b shows Arrhenius plots of the conductivity data and
the calculated activation energies of ion transport were 13.2
and 12.8 kJ mol�1, respectively for DS58 and DS106
Fig. 7 e a) IR corrected polarization curves of DS58 and
DS106, b) Tafel plots obtained from polarization curves in
Fig. 7a.
membranes. The data indicate that the ionic conductivity of
PA/QDPSU was related to the number of function groups
(degree of substitution) andwas independent of the activation
energy for ion transport. The properties of themembranes are
listed in Table 1.
3.5. Fuel cell performance
Fig. 6 shows the polarization and power density curves of fuel
cells using hydrogen and oxygen at different temperatures.
Both MEAs with different DS of QDPSU showed increased fuel
cell performancewith increasing temperature. The open circuit
potentials at temperatures of 150 �Cwere 0.97 and 0.90 V for the
DS58 and DS106 membranes, respectively. The high DS of PA/
QDPSU led to a superior fuel cell performance (400 mW cm�2)
than the low DS PA/QDPSU (323 mW cm�2). The fuel cell
performance was similar to the result published using greater
catalyst loading (0.81 mgPt cm�2) and a thinner membrane
(20 mm) [9].
The internal cell conductivities estimated from the linear
region of the polarization curves obtained at 150 �C were
0.015Scm�1 and0.023Scm�1 for theDS58andDS106membrane
basedMEAs respectively. These values aremuch lower than the
membrane conductivities indicating significant voltage losses
due to electrode polarization and electrode layer resistances.
Fig. 7 shows IR corrected polarization curves of the fuel cells
operated at 150 �C. From the plot of the IR correct voltage vs ln
( j ), the slope (Tafel type) of the lines were 120 and 103 mV per
decade. Ignoring the contribution associatedwith thehydrogen
oxidation reaction, these values are close to literature reported
values for phosphoric acid loaded PBI fuel cells [15].
4. Conclusions
A novel PA/QDPSU was synthesised via a FriedeleCrafts like
reaction followed by quaternization with DABCO, which is safe
and easy to handle. Different degrees of substitution (DS) can be
achieved by this method. The ionic conductivity and fuel cell
performance are related to the DS. The higher DS of QDPSU
results in significantly better ionic conductivity and fuel cell
power density. However, too high of the DS (such as DS180) will
compromise themembranemechanicalpropertywhich leads to
the unfavourable results for fuel cell applications. A high power
density output of 400mW cm�2 can be achieved using DS106 of
PA/QDPSUmembrane at 150 �C and atmospheric pressure.
Acknowledgement
The authors thank the UK EPSRC for financial support.
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