Degradation of High Temperature Polymer Electrolyte Fuel Cell

Transcription

Journal of The Electrochemical Society, 162 (6) F587-F595 (2015)
0013-4651/2015/162(6)/F587/9/$33.00 © The Electrochemical Society
F587
Degradation of High Temperature Polymer Electrolyte Fuel Cell
Cathode Material as Affected by Polybenzimidazole
Mikhail S. Kondratenko,a,z Marat O. Gallyamov,a,b Oksana A. Tyutyunnik,c
Irina V. Kubrakova,c Alexander V. Chertovich,a Ekaterina K. Malinkina,d
and Galina A. Tsirlinad,∗
a Faculty of Physics, M.V. Lomonosov Moscow State University, 119991 Moscow, Russia
b A. N. Nesmeyanov Institute of Organoelement Compounds RAS, 119991 Moscow, Russia
c V. I. Vernadsky Institute of Geochemistry and Analytical Chemistry RAS, 119991 Moscow, Russia
d Department of Electrochemistry, Faculty of Chemistry, M.V. Lomonosov Moscow State University,
119991 Moscow, Russia
The data of electrochemical experiments, analysis of solutions, transmission electron microscopy and scanning tunneling microscopy
are applied to separate various processes resulting in degradation of carbon supported platinum cathode material in hot concentrated
phosphoric acid in the presence of polybenzimidazole. Under these modelling HT-PEFC operation conditions, dissolution of metallic
platinum is found to play a minor role as compared to sintering of nm-size platinum crystals. Yet, polybenzimidazole significantly
affects platinum dissolution, which results in up to 2 orders of magnitude increase of integral rate of potentiostatic dissolution at
0.87 V vs RHE.
© 2015 The Electrochemical Society. [DOI: 10.1149/2.0741506jes] All rights reserved.
Manuscript submitted December 26, 2014; revised manuscript received February 20, 2015. Published March 17, 2015.
High temperature polymer electrolyte fuel cells (HT-PEFCs) based
on PBI membranes doped with orthophosphoric acid (PA) as an electrolyte are promising electrochemical current generators.1 Since PA
has reasonable conductivity in anhydrous state and low volatility up
to 200◦ C, HT-PEFC can be operated at elevated temperatures (in contrast to LT-PEFC based on polymer sulfonic acids, which require water
for reasonable proton conductivity). In its turn, temperature increase
allows to improve the tolerance of Pt catalyst to impurities (mainly
CO)2,3 and thus to use cheaper (of lower purity) hydrogen as a fuel.
Moreover, heat removal is more efficient at higher operation temperatures, so for HT-PEFC a cooling system and overall fuel cell stack
design can be simplified.
Significant improvements in power density and costs of both high
temperature and low temperature (HT and LT) polymer electrolyte fuel
cells have been achieved during the last two decades.1,4 Nevertheless,
enhancing durability and lifetime of both membrane and electrode
materials remains one of the critical issues for widespread application
of PEFC. A significant portion of the performance losses is due to the
loss of electrochemically active surface area (ESA) of Pt catalyst at
the cathode with operation time.
Various mechanisms of cathode catalyst ageing were considered in
the literature. First, ESA is lost due to the coarsening of Pt nanoparticles supported on carbon surface.5–9 There are two possible fundamental mechanisms of such coarsening:10 1) migration and coalescence
of Pt nanoparticles; 2) interparticle transport of single atoms (usually called Ostwald ripening). At potentials 0.6 V vs RHE (here and
below, the potential values are presented in RHE scale) and higher,
corrosion of carbon support may also occur,11,12 leading to the loss
of electric contact between platinum and carbon particles. It has been
shown that Pt catalyzes carbon black corrosion in hot concentrated
PA.13 At potentials higher than 0.8 V dissolution and/or oxidation of
Pt takes place.13,14 For LT-PEFC it has been shown15 that Pt nanoparticles anodically dissolve at the cathode side, then soluble products
are distributing inside the membrane-electrode assembly (MEA), and
significant amount of these products is reduced in the polymer membrane. Traces of Pt can also be found in gas diffusion layers.16 The
precipitation of Pt inside inorganic matrix has also been observed for
phosphoric acid fuel cells by means of electron probe microanalysis
(EPMA).17 To the best of our knowledge, the precipitation of Pt inside
the PBI membranes in HT-PEFC has not been reported yet. Besides
re-deposition inside the polymer membrane or inorganic matrix, the
∗
z
Electrochemical Society Active Member.
E-mail: kondratenko@polly.phys.msu.ru
dissolved Pt may also re-deposit on the surface of larger Pt nanoparticles resulting in particle growth (Ostwald ripening), which results in
overall ESA decrease.18
Experimental studies of fuel cell electrodes stability confirm that
Pt dissolution plays a significant role in cathode catalyst layer degradation. However, the roles of operating conditions and coexisting
materials in the active layers and other components of MEAs are still
not completely understood, especially for PA as electrolyte. Moreover, direct analytical data on Pt dissolution in PA are rather rare.19 A
more typical approach to estimate the amount of platinum dissolved
in PA is to measure the loss of Pt in the electrodes.13,14 Due to the
difference in experimental conditions, it is difficult to compare the
data of these works: e. g., the direct comparison of integral dissolution rates calculated using the data of Bindra et al.14 and Passalacqua
et al.13 shows discrepancy of 4–5 orders of magnitude (see Table I).
This huge difference cannot be straightforwardly assigned to the difference in experimental conditions. As one can see from the Table I,
the deviations in Pt dissolution rates at lower temperatures in other
(mostly of sulfuric acid) solutions measured under similar conditions
do not exceed one order of magnitude.
Despite of some quantitative contradictions and the peculiarity of
hot PA, basically experimental data available in the literature provide a solid evidence that the formation of the oxide film on the
platinum surface plays a significant role in platinum dissolution in
acids. Two main dissolution pathways of Pt in acidic media can be
outlined, i.e. electrochemical dissolution of bare Pt and chemical dissolution of Pt oxides. A vivid scientific discussion on the prevailing
mechanism is still open. The majority of PEFC degradation models
suggest that Pt dissolves via the electrochemical pathway, and the
rate of chemical dissolution of Pt-O is negligible.20–22 Rinaldo et al.
argued this statement and presented a model for chemical dissolution of Pt nanoparticles taking into account particle size effects.18 By
comparing with available degradation results they concluded that the
dominating mechanism at high potentials is chemical dissolution of Pt
oxide.
Another important issue is the influence of PBI on platinum dissolution. It is known that benzimidazoles can serve as ligands forming
coordination compounds with Pt.23–25 It is possible that such complexation may increase Pt solubility and accelerate both electrochemical
and chemical pathways of Pt dissolution. Meanwhile it is quite common to add PBI into the active layers of fuel cell electrodes,26–32
which may be crucial for the lifetime of Pt catalyst if PBI indeed
affects degradation processes. To the best of our knowledge, the possible influence of PBI on mechanisms of Pt dissolution has never been
discussed in the literature.
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Table I. Integral rates of Pt dissolution in acidic media normalized on Pt ESA.
Normalized dissolution rate, g cm−2 s−1
(2.7 ± 1,0) 10−14
(1.8 ± 0,4) 10−12
8.3 10−15
1.4 10−14
4 10−13
1.08 10−8
1.16 10−7
1.2 10−11
5.43 10−12
3.8 10−11
1.4 10−14
1.7 10−14
2.9 10−14
Pt form
Conditions
40 wt% Pt/C
0.87 V H3 PO4
40 wt% Pt/C
0.87 V 10 g/l ABPBI dissolved in H3 PO4
Platinized foil (roughness factor 140)
0.87 V H3 PO4
Platinized foil (roughness factor 140) 0.87 V 10 g/l ABPBI dissolved in H3 PO4
Smooth Pt foil (roughness factor 1.2)
0.87 V H3 PO4
Smooth Pt sheet
0.9 V H3 PO4
Smooth Pt sheet
0.95 V H3 PO4
20 wt% Pt/C
1 V 98% H3 PO4
20 wt% Pt/C
0.8 V 98% H3 PO4
Pt disk
Cycling potential 0.4 to 1.4 V 1 M H2 SO4
10 wt% Pt/C
0.9 V 0.57 M HClO4
Pt wire
0.9 V 0.57 M HClO4
Pt electrodeposited on Au
0.9 V 0.5 M H2 SO4
In this communication we present the data on Pt degradation in hot
PA and on the effect of PBI on this phenomenon. We address Pt dissolution under potentiostatic conditions taking into account morphology evolution in parallel with voltammetric features, and consider the
reasons of MEAs degradation behavior on the basis of these separately
recognized contributions.
Experimental
Cell arrangement.— Corrosion tests were performed in a conventional three electrode cell with glassy carbon counter electrode located
in the same vessel as the Pt working electrode. Hydrogen electrode
in the same solution equipped with a Luggin capillary was used as a
reference. All electrochemical measurements were performed using
Autolab PGSTAT 302 N (Eco Chemie, Netherlands) potentiostat. For
maintaining elevated temperatures the cell was put into Huber CC-K6
thermostatic bath. Reference electrode was kept outside the bath at
room temperature. This resulted in a temperature dependent potential
shift (in respect to RHE), which was estimated experimentally in a following way. Platinum working electrode in the cell filled with 85 wt%
H3 PO4 at the room temperature was bubbled with hydrogen. After the
working electrode potential reached stable zero values as referred to
the reference electrode, the cell was heated up to 160◦ C. This resulted
in establishing +80 mV potential difference between the heated and
room temperature electrodes correspondingly. This difference is assumed to result from temperature potential jump at liquid junction
and also from the temperature dependence of hydrogen equilibrium
potential. After cooling the cell the difference came back to zero. All
potentials reported below are corrected for this temperature-induced
shift and can be considered as potentials in the scale of hydrogen electrode in the same solution and at the same temperature as the working
electrode (RHE scale).
Comparative voltammetric experiments in 0.5 M H2 SO4 solutions
were arranged in a similar cell at room temperature.
The volume of solution in the cell was typically 30 ml.
Electrodes preparation.— Three types of working electrodes were
used: carbon supported Pt electrodes, platinized Pt electrodes, and Pt
foil.
Electrodes containing pure Pt supported on carbon (2×2 cm2 area)
were cut out from commercial Celtec P-1000 MEA, with Pt/C ratio
40 wt% and Pt loading 1 mg cm–2 . Since the electrodes from freshly
disassembled Celtec P-1000 MEA contain PA, they were first treated
with 40 vol.% ethanol aqueous solution at 60◦ C and then washed with
distilled water. This procedure resulted in effective PA removal. Initial
specific surface area (SSA) of Pt/C electrodes was about 50–55 m2
g−1 as determined by TEM observations.
Platinized Pt (Pt/Pt) electrodes were prepared by electrodeposition
of Pt on Pt foil sheet (2×2 cm, thickness of 0.1 mm) according to the
following procedure. Bare Pt foil was boiled in hot sulfuric acid for
Temperature, ◦ C
Ref.
160
160
160
160
160
176
176
160
160
25
23
23
25
This work
This work
This work
This work
This work
Bindra14
Bindra14
Passalacqua13
Passalacqua13
Johnson46
Wang41
Wang41
Sugawara42
10 minutes, washed with water, boiled in hot aqua regia for 1 minute,
washed with water, polarized anodically (with 100 mA current) in
0.1 M HCl for 2 minutes, washed with water, polarized cathodically
(100 mA current) in 0.5 M H2 SO4 for 2 minutes. Then the foil was
placed in a cell with two large parallel Pt counter electrodes containing 0.02 M H2 PtCl6 + 0.01 M HCl solution. Electrodeposition was
performed potentiostatically at 100 mV versus Ag/AgCl reference
electrode. Deposition currents under steady-state conditions were 8–
10 mA. The process was stopped when the total charge reached 32 C
(ca. 1 mg cm–2 of deposited Pt assuming 100% current yield).
Platinum foil was used as received, with preliminary chemical
purification as described in the previous paragraph.
All electrodes were connected to Pt wire isolated with glass.
Electrolyte.— Acros Organics extra pure 85 wt% solution of phosphoric acid in water was used as an electrolyte without any additional
purification. When the influence of polybenzimidazoles on platinum
dissolution was studied, non-crosslinked poly(2,5 – benzimidazole)
(ABPBI) supplied by FuMA-Tech in a form of powder (average polymer molecular mass 30000 Da) was dissolved in the electrolyte preliminary heated up to 160◦ C. The electrolyte had been then stirred
with a magnetic stirrer for 2–3 hours prior to the measurements until a uniform and transparent somewhat colored and viscous polymer solution was obtained. The volume of electrolyte in the cell was
30 ml.
Transmission electron microscopy (TEM).— Samples of Pt/C catalyst were scratched from the electrode surface and placed on a formvar
film substrate. Cross sections of fuel cell MEAs were obtained as follows. Gas diffusion layers were removed. Membrane with remaining
active layers was washed from PA in 50% water/isopropanol mixture
and dried in an oven at 80◦ C for 3 hours. Then the membrane was cut
using Reihert-Jung microtome with an ultra 35◦ DiATOME diamond
knife to obtain cross sections with the thickness of below 100 nm.
These ultrathin sections were placed onto the film substrate from the
water surface of the knife reservoir.
Micrographs were obtained by means of LEO912AB (Carl Zeiss,
Germany) microscope as 2048×2048 px digital images and analyzed
using the ImageJ software.
Particle radius distributions (PRDs) for Pt/C electrodes were obtained by measuring sizes of about 500–600 particles visible in 5–10
TEM images for each electrode sample. SSAs of platinum for Pt/C
electrodes were calculated from those PRDs according to equation:
2
di
6
S = i 3 ,
[1]
ρ i di
where di is the particle diameter, and ρ is the platinum density
(21.45 g cm−3 ).
The highest possible ESA, as expected from the microscopy, was
calculated from the TEM data as SSA multiplied by the amount of
Pt in the electrodes and compared with the value calculated from CV
data.
Scanning tunneling microscopy (STM).— For STM experiments,
UMKA device (Russia) with additional spectroscopic facilities was
used. Pt–Ir tips (10% Ir) of 0.5 mm diameter were mechanically
sharpened. In topographic experiments, bias was 1.3 V (positively
polarized tip), and current was 0.3 nA.
Atomic absorption spectrometry.— Concentration of Pt in PA was
measured by electrothermal atomic absorption spectrometry (ETAAS)
(Solaar MQZ, Thermo Elemental, USA). To eliminate the influence
of PA on the detected Pt signal, all the measurements were performed
in diluted PA (1:10 PA:water). The samples containing ABPBI were
additionally diluted with 85% PA (1:2) prior to dilution with water
indicated above.
Calibration procedure was performed in the electolyte diluted as
described above (1:10) and containing known amounts of H2 PtCl6 .
The detection limit was 1 ng ml–1 (∼5 10−9 M).
Dissolution rates normalized on platinum ESA were calculated
according to the following equation:
m
,
[2]
v=
At
where m is the mass of dissolved platinum, calculated as platinum
concentration in the solution, as measured by means of ETAAS, multiplied by the volume of electrolyte; A is platinum ESA of a fresh
electrode, obtained from hydrogen desorption charge; t is exposition
time (18 h for potentiostatic experiments).
Corrosion tests.— The following sequence of experiments was
typically arranged.
1.
2.
3.
4.
5.
6.
7.
Cyclic voltammetry of the working electrode in 0.5 M H2 SO4 at
room temperature, in order to determine Pt ESA (from hydrogen
desorption charge, according to),33 scan rate of 20 mV/s, potential
limits 0.05 – 1.2 V.
Exposure of the working electrode in concentrated phosphoric
acid at 160◦ C at a constant potential (for 18 hours).
Determination of platinum concentration in resulting PA solution
by means of ETAAS, as described above.
Washing aged electrodes in pure hot PA (only for electrodes
exposed to ABPBI-containing solutions, to remove polymer from
the electrode surface).
Washing aged electrodes in hot 40 vol.% isopropanol aqueous
solution and then with pure Milli-Q water, to remove PA traces.
Cyclic voltammetry in 0.5 H2 SO4 (see point 1 above), to determine Pt ESA of aged catalyst.
Comparative microscopic characterization of the morphology of
initial (identical sample) and aged electrodes.
Fuel cell tests.— In order to study degradation of Pt catalysts
in the operating fuel cells two MEAs (MEA1 and MEA2) with active (geometric) area of 25 cm2 were assembled. Poly[oxy-3,3-bis(4 benzimidazol-2 -ylphenyl)phtalide-5 (6 )-diyl] (PBI-O-PhT) membranes for both MEAs were prepared according to standard procedure
as described previously.34 Electrodes were prepared by the consecutive spraying of microporous and active layers on the surface of
280 μm thick TGP H 090 carbon paper (Carbon Fiber Department,
Toray Industries Inc.). Microporous layer preparation is described in
detail in Ref. 35. Active layer contained 84 wt% of HiSpec 3000 catalyst (20% Pt/C ratio), 8% of PTFE and 8% of Nafion was prepared
according to Ref. 36. Pt loading in the electrodes was 1 mg cm–2 .
MEA1 had been continuously held for 600 hours under open circuit
conditions at 160◦ C. Pure hydrogen was supplied to the anode at a
fixed rate of about 100 nml/min, air was fed to the cathode at a rate of
500 nml min–1 .
MEA2 was tested in start/stop mode for 1000 hours: it was operated under constant current density of 0.4 A cm–2 at 160◦ C daily (for
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9 hours per day, 250 hours under load in total) and turned off and
cooled to the room temperature overnight. Everyday startup was performed by heating MEA2 up to 160◦ C. After that the gases were
supplied to the electrodes. The shutdown procedure was consecutive
shutting off the load, shutting of the gases and then turning off heaters.
Gas flow rates for MEA2 were the same as for MEA1.
Results and Discussion
Electrochemical behavior of Pt in the media under study.— Electrochemistry of Pt in PA is scarcely studied, but at least two complications are known long ago. First, the commercial PA always contains
phosphorous acid impurities, which demonstrate oxidation on Pt in
the double layer region. This by-side process is more pronounced at
high temperatures.37–40 Second, quasireversible redox process in the
double layer region is observed, which is sometimes assigned to surface attached species (e.g. the products of PA dissociative adsorption),
which was stated for the first time in Ref. 38.
Fig. 1a demonstrates irreversible oxidation of impurity on smooth
Pt in initial cycles (current peak in the interval 0.5–0.8 V). For this
electrode, the ratio of the true and geometric surface areas is low, and
the capacitive contribution (including the response of PA adsorption)
is not too high, giving possibility to observe electrode reactions. Potential cycling results in essential (up to an order of magnitude) decrease
of impurity response (Fig. 1b). From comparison of peak currents at
curves 1, Fig. 1a and 1b, with the data available in Ref. 39 for 7.5
10−3 M phosphorous acid we conclude that concentration of phosphorous acid in our PA sample does not exceed this value (7.5 10−3 M).
The response of impurity strongly decreases with cycling (compare
Figs. 1a and 1b). Addition of polymer (curves 2 in Figs. 1a and 1b)
slightly decreases the currents of impurity oxidation, and the response
of another oxidation process appears at ca. 1.0 V, i.e. the polymer
additive also undergoes anodic oxidation. An important voltammetric
observation follows also from the comparison of curves 1 and 3 in Figs.
1a and 1b: quasi-reversible oxygen adsorption is more pronounced in
concentrated PA at high temperature as compared to sulfuric acid solution at room temperature.37 Roughly estimated charge in the oxygen
adsorption region demonstrates that oxygen coverage exceeds monolayer in the region under study, i.e. two-dimensional oxide is formed
before the onset of oxygen evolution. More easy oxygen adsorption
in PA as compared to other acids was earlier mentioned in Ref. 37.
For dispersed Pt (Fig. 1c), the interplay of PA adsorption and
diffusion-limited impurity oxidation is less pronounced because of
much higher capacitive contribution. Currents of these two processes
are comparable and result in a broad maximum at potential of ca.
0.5 V. At higher temperatures (Fig. 2a) impurity oxidation peak starts
to be more pronounced, but it is still shifted to lower potentials as
compared with the peak for smooth Pt. In polymer-containing solution, even more complex interplay of PA-related and polymer-related
processes occurs (Fig. 2b). Oxidation of polymer additive takes place
on dispersed platinum as well. Electrochemical oxidation of carbon
may also yield significant contribution to the current (see potentiostatic data of Passalacqua et al.13 for Pt/C electrodes in PA at the same
temperature).
The pronounced decrease of charge in the hydrogen region is observed even after only a few cycles, demonstrating fast ageing of
dispersed Pt (Fig. 2b). This complication gives no chance to consider
the effect of polymer in the hydrogen region. Qualitatively, we can assume that the presence of polymer decreases this charge, i.e. polymer
is adsorbed on Pt in a wide potential interval.
All further data were obtained without special PA purification to
see how real electrolyte to be used in fuel cells affects Pt degradation.
Potentiostatic dissolution of carbon supported Pt—Choice of
potentials for corrosion tests.— Since the solubility of Pt in
acidic media is negligible below 0.8 V, the present study is focused on the potentials above this value, mainly in a range of
0.87–0.95 V corresponding to cathode at open circuit of a fuel cell fed
with hydrogen and air.
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Figure 1. CVs of a smooth Pt foil (a, b) and carbon supported Pt (c) in concentrated PA or in PA with 10 g l−1 dissolved ABPBI at 160◦ C. Dashed lines correspond
to CV of the same electrode in 0.5 M H2 SO4 measured at room temperature before the experiments in PA. Scan rate 50 mV/s. For smooth Pt, initial CVs (a) and
CVs stabilized in 500 cycles (b) cycles are presented. For supported Pt, no pronounced change in CVs in subsequent cycles was observed.
As one can see from the previous section, at these potentials the observations of Pt dissolution is complicated by
irreversible anodic oxidation of both impurities in electrolyte and
the polymer additive. Under potentiostatic conditions currents decayed from ∼1 mA to ∼0.1 mA. Corresponding charges increase
monotonously with time, and steady-state values are still not achieved
in 18 h. Contributions of concomitant processes give no chance
to associate the charge in the course of potentiostatic polarization with the quantity of dissolved Pt and/or formed platinum oxide. The currents and charge increase monotonously with potential, in a good agreement with cyclic voltammetry data presented in
Fig. 1c.
Figure 2. Cyclic voltammogramms of Pt/C working electrodes in pure concentrated PA (a) or in PA with 10 g l−1 dissolved ABPBI (b) at various temperatures.
Scan rate 50 mV/s. Initial cycles.
Figure 3. Concentrations (left axis) of Pt in PA after 18 h potentiostatic dissolution of carbon supported platinum (circles), platinized (stars) and smooth
(square) platinum electrodes in pure concentrated PA or in PA with 10 g l−1
dissolved ABPBI at 160◦ C measured by means of atomic absorption spectroscopy. Integral dissolution rates (right axis) are presented only for Pt/C
electrodes (circles).
Pt dissolution.—According to the ETAAS data, the amount of Pt
dissolving in pure PA at 0.87 V from Pt/C electrodes is about 3 μg. If
the dissolution follows the reaction 3
Pt → Pt 2+ + 2e− ,
[3]
this amount should correspond to the charge of about 3 μC while
significantly higher charges are registered during potentiostatic experiments (18 C for Pt/C electrodes in pure PA at 0.87 V). The difference
was expected from our data for oxidation of carbon, impurities in the
electrolyte and (in experiments with the polymer additive) polymer
molecules.
Concentrations of Pt in the electrolyte measured by means of
ETAAS after 18 h corrosion tests of carbon supported platinum and
platinized platinum in hot phosphoric acid are presented in Fig. 3.
Regarding hot phosphoric acid, there are only two works (by
Bindra et al.14 and Passalacqua et al.13 ) in which potentiostatic platinum dissolution in hot PA was addressed experimentally (but less
directly, on the basis of weight loss). The dissolution of Pt in phosphoric acid at elevated temperature was also studied by Tarasevich
et al. by means of ETAAS.19 Their data correspond to accelerated
corrosion tests of commercial E-TEK catalysts (20% Pt) at 90◦ C in a
mixture of 85% PA with 10% H2 O2 , not to electrochemical polarization.
Taking into account the differences in experimental conditions,
Pt concentrations observed after corrosion tests of Pt/C electrodes at
0.87 and 0.92 V in the present work are comparable to the results
of Bindra et al.14 (potentiostatic exposition of bare Pt foil at 176◦ C)
and Tarasevich et al.19 This fact indicates that saturation of solution
with Pt species is reached during the exposition of Pt/C electrodes
at the mentioned potentials. For higher potentials the dissolution
is limited by Pt oxides formation. Oxide formation results in a decreased amount of dissolving Pt starting from a certain potential value
(Fig. 3) which has been reported previously by Wang et al.41 for
HClO4 solutions and Sugawara et al.42 for H2 SO4 solutions. According to quartz crystal nanobalance studies in aqueous H2 SO4 solutions
at room temperature,43 oxide formation occurs in several steps. Half
monolayer of chemisorbed oxygen atoms is formed first in the potential region of 0.85–1.15 V, and the formation of the second half monolayer is accompanied by strong dipole-dipole lateral repulsive interactions. In order to minimize these repulsions, the initial half-monolayer
of oxygen adatoms undergoes an interfacial place-exchange process
with the Pt surface atoms with formation of a quasi-3D surface lattice
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comprising Pt2+ and O2− moieties. The resulting coverage depends
on potential and may exceed one monolayer.
Growing oxide layer limits the electrochemical pathway of Pt dissolution, and chemical dissolution of Pt oxide becomes the dominating mechanism. This is why Nernstian behavior observed by Bindra14
is not observed at higher potentials in the present study and other
works.41,42
Integral dissolution rates of Pt in hot PA at 0.87 V calculated from
ETAAS data are presented in Table I. Assignment of dissolution rate
to a certain surface area is a sort of a trick, as the true surface area
continues to decrease in the course of experiments. However since
the initial and resulting ESA are of the same order of magnitude, this
uncertainty does not affect the order of magnitude of the calculated
dissolution rate. For pure PA, the values are close to the results of
Wang et al.41 and Sugawara et al.42 obtained by measuring concentration of Pt dissolving in aqueous solutions of HClO4 and H2 SO4
at room temperature by means of inductively coupled plasma mass
spectrometry (see Table I for comparison). Regarding hot phosphoric acid, unfortunately, the data from the work of Tarasevich et al.19
are insufficient to calculate the dissolution rate for comparison. As
for the data of Bindra et al.14 and Passalacqua et al.,13 if saturation was achieved indeed, it would be rather risky to use the weight
loss for calculation of platinum concentrations and dissolution rates
because weight loss should start to depend on redeposition of Pt
from saturated medium, and forming deposit can find itself somewhere at the walls of the cell, etc. This would contribute to weight
loss, but not to increase of Pt ions concentration. To illustrate this
problem, just the close concentrations obtained in Ref. 14 and 19
(despite of dramatic difference of the true surface areas) are good
examples.
To consider the observed difference of dissolution rates obtained in
various experiments, one should also take into account slow diffusion
in phosphoric acid. If the dissolution rate is limited by diffusion of
dissolved platinum species from metal surface, the rate of dissolution
(in g s−1 ) should depend more on electrode geometrical area than on
the ESA of platinum. We checked this assumption experimentally and
compared dissolution of smooth Pt foil and platinized Pt foil with
the same geometrical area and different ESA. According to cyclic
voltammetry data the roughness factor was about 1.2 for smooth foil
and about 140 for fresh platinized foil. Pt concentrations appeared to
be 5 10−8 and 1 10−7 M correspondingly. Since the measured platinum concentrations are far from equilibrium (see Fig. 3), dissolution
rates (in g s−1 ) for smooth and platinized foil are of the same order
of magnitude (4 10−12 g s−1 and 9 10−12 g s−1 , correspondingly)
and are almost independent from ESA (10 cm2 and 1100 cm2 , correspondingly). This fact confirms that at least at low concentrations (in
large volumes of PA) the rate of platinum dissolution is controlled by
the slow diffusion of dissolved platinum species from the electrode
surface.
Considering the contradictions of independently measured dissolution rates (Table I), we surely should account for the difference of
applied mode (potentiostatic or potentiodynamic), which affect contributions of pure and oxide-covered platinum surface to the measured
value of dissolution rate. However, as follows from the discussion
above, to clarify this complex process one should arrange the experiments far from PA saturation with oxidized platinum species.
Potential dependence of Pt/C integral dissolution rates is shown
in Fig. 3 (right axis). The maximum of dissolution rate is observed
at ∼0.9 V in pure PA and at ∼1.0 V in PA containing dissolved
ABPBI. At higher potentials dissolution rates decrease due to the formation of oxide film on the platinum surface, in agreement with the
previously mentioned over monolayer oxygen coverage. Increased Pt
concentration detected at 1.12 V in pure PA is likely due to the degradation of carbon support resulting in delamination of Pt nanoparticles as confirmed by TEM observations (Fig. 4). One can see that
the morphology of carbon support is significantly changed, and the
density of supported nanoparticles is reduced dramatically after the
electrode exposure at 1.12 V (Fig. 4d). According to PRD obtained
from TEM data, the relative amount of large particles is decreased
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Figure 4. TEM images of fresh Pt/C electrodes (a) and electrodes after 18 h potentiostatic exposition in PA at 160◦ C at 0.87 V (b), 0.92 V (c) and 1.12 V (d) vs
RHE. Particle size distributions are obtained using 5–10 TEM images of various parts of the electrode surface.
indicating that the delamination is more pronounced for larger
nanoparticles.
Due to delamination, the electrolyte should contain Pt nanoparticles besides really dissolved Pt molecular species. One can estimate
the diffusion coefficient of these nanoparticles using Stokes-Einstein
equation:
D=
kT
,
6πηr
[4]
where k is Boltzmann constant, T is the absolute temperature, η
is dynamic viscosity, r is particle radius. For spherical particles of
10 nm diameter in concentrated PA at 160◦ C the equation 4 yields
diffusion coefficient D ∼ 10−11 m2 s−1 . During the potentiostatic exposure time of 18 h the average distance of diffusion will be ca. 1 mm.
According to this estimate, most of the delaminated nanoparticles
should be located in the pores and near the surface of the electrode
and can be removed from the electrolyte with the removal of the
electrode prior to collecting the electrolyte out of the cell. The residual Pt particles influence the measurements of Pt concentration by
means of ETAAS. This influence is less pronounced in the presence of
ABPBI due to higher solution viscosity slowing down the diffusion of
nanoparticles.
Morphology and ESA loss.—According to CV data, significant decrease of Pt ESA after 18 hour potentiostatic exposition in hot PA
for both Pt/C and platinized Pt electrodes is observed (Fig. 5a and
5b). Relative ESA losses calculated from CV data and independently
from TEM data are presented in Fig. 6. In the absence of ABPBI Pt
dissolution contributes weakly to ESA loss since very low amounts
(several μg) of Pt are dissolved. In pure PA at potentials 0.87–1.02 V
relative ESA loss calculated from PRD and ETAAS data (Fig. 6) is
in a good agreement with relative ESA loss obtained from CV data,
indicating that ESA loss results mainly from particle coarsening. The
discrepancy between PRD and CV calculated ESA is observed at
1.12 V. As mentioned before, at this potential delamination of Pt
Figure 5. Cyclic voltammogramms of Pt/Pt (a) and Pt/C (b) working electrodes taken in 0,5 M H2 SO4 at 23◦ C before and after corrosion tests. Scan rate
20 mV s−1 .
Figure 6. Relative ESA losses for Pt/Pt and Pt/C working electrodes after
18 h potentiostatic exposition at 160◦ C in pure concentrated PA or in PA
with dissolved ABPBI (10 g l−1 ). ESA losses were calculated from three
types of experimental values: 1) from hydrogen desorption peak charges (CV
data); 2) from atomic absorption spectroscopy data (dissolution loss); 3) from
atomic absorption spectroscopy data and PRD, obtained from TEM images
(dissolution and coarsening loss).
particles from the surface of carbon support is observed in TEM
images (Fig. 4). Delamination influences PRD: larger particles are
removed from the support. This results in increased SSA calculated
from PRD and negative area loss calculated from PRD (since platinum
loss in the electrodes determined by means of the ETAAS is underestimated in case of nanoparticle delamination, as described above). On
the other hand, according to CV data relative ESA loss at 1.12 V is
more than 70% for pure PA. Taking this and also a sharp decrease of
particle density in TEM images into account one may conclude that
delamination of Pt nanoparticles from carbon support is a dominating
mechanism of the distinct ESA loss at 1.12 V.
The ESA loss is more pronounced for platinized Pt electrodes
(Fig. 6). This is likely due to the fact that electrodeposited Pt crystallites are located close to each other at distances between the crystallite
centers of about ∼10 nm, which is comparable with the crystallites
average size, while average distances between neighboring Pt particles supported on carbon are significantly higher (see Fig. 4). This
results in accelerated particle coalescence. Since the redeposition of
Pt from solution is unlikely to occur at the potentials under discussion, migration and coalescence of nanoparticles is likely to be the
dominating mechanism of particle coarsening.
The shift of PRD to larger particle sizes is the same trend as reported previously in the literature.6,7,44 There are two possible fundamental mechanisms for coarsening of supported particles: interparticle
transport of single atoms (usually called Ostwald ripening) and migration and further coalescence of the whole particles (Smolukhovky
mechanism). According to Granqvist and Buhrman,10 an asymptotic
tail on a large diameter side and a cutoff at smaller particles sizes are
predicted in PRD for migration-coalescence mechanism. On the other
hand, for the interparticle transport mechanism there is a substantial
tail on the smaller-particle side, and the distribution is zero above certain finite diameter. Since in our experiments we observe decreasing
fraction of smaller particles and increasing tail on the larger-particle
side, it is reasonable to assume that the dominating mechanism for
F593
particle coarsening is migration-coalescence, which is consistent with
the conclusions of Gruver et al.7 and Aindow et al.44 on degradation
of carbon supported platinum in phosphoric acid. Using TEM Gruver
et al. have provided good experimental evidence of particle migration: after potentiostatic exposure to hot PA platinum nanoparticles
on carbon film have been found in the regions initially shielded from
Pt deposition.
Particle coarsening results in 20% decrease of ESA after 18 hours at
0.87 V (Fig. 6) which is lower than 45% observed by Passalacqua et al.
(1000 min at 0.8 V, 160◦ C, 20% Pt/C catalyst)13 and ∼40% observed
by Gruver al. (1380 min, at 0.8 V, 160◦ C, 20% Pt/C catalyst).7 We consider two possible reasons for these differences. First, the difference in
potential may influence the state of carbon support, catalyst-support
interaction and therefore the mobility of particles. The second reason
may be the difference in initial states of the catalytic materials: Passalacqua et al. and Gruver et al. used freshly prepared electrodes with
SSA of about 135 m2 g−1 and 70 m2 g−1 , correspondingly, while we
used commercial MEA Celtec P-1000, which had been in prolonged
contact with PA and had lower initial SSA of about 50–55 m2 g−1 .
Polybenzimidazole influence.—The presence of ABPBI dissolved in
PA results in a noticeable increase of dissolved platinum concentration and the rate of platinum dissolution for both carbon supported
platinum and platinized platinum electrocatalysts (Fig. 3, Table I). We
suppose that the presence of PBI in the solution affects both electrochemical and chemical pathways of Pt dissolution. The formation of
complexes of ABPBI with Pt likely shifts the equilibrium potential
of the Pt/Pt(II) system to lower values which results in accelerated
electrochemical dissolution of bare Pt at certain potential. It is also
possible that the chemical dissolution of Pt oxides is accelerated due
to the increased solubility of Pt oxide species in PA in the presence of
PBI.
The effect of ABPBI is more pronounced for carbon supported
platinum (2 orders of magnitude increase in dissolution rate at
0.87 V) than for platinized platinum (70% increase at 0.87 V). This difference may be explained by lower contact area of polymer with metal
for platinized platinum since macromolecules cannot diffuse into the
layer of electrodeposited Pt crystallites because of small distances
between them. Indeed, an estimate of polymer coil size according to
1
the equation R = (Lb) 2 (b is Kuhn segment, L is a contour length)
yields R ∼ 40 nm (b = 8.79 nm for ABPBI and L = Nl, where l =
0.59 nm45 is the virtual bond length, N is the number of repeating
units, calculated from average polymer molecular mass, 30000 Da).
Distances between crystallites are somewhat smaller than crystallite
sizes ∼10 nm according to STM data. That means a possibility for the
polymer to reach only the top layer of the platinized Pt surface.
Although dissolution rates are increased significantly, the presence
of dissolved ABPBI does not influence particle coarsening. According to TEM data, PRD of Pt/C catalysts after potentiostatic exposure
to pure PA or PA with dissolved polymer are identical for potentials 0.87–1.02 V. SSAs determined by TEM are the same in both
cases. Nevertheless, the amount of Pt in the electrodes is reduced
faster in the presence of APPBI due to the increased dissolution rate
(Fig. 3). This results in more pronounced ESA losses calculated from
PRD and ETAAS data than in pure PA. ESA losses in the presence
of ABPBI determined by CV (Fig. 6) are even higher than the losses
calculated from PRD. This fact may be attributed to residual polymer
on Pt surface since it is impossible to remove polymer completely
during washing procedure prior to measuring ESA in 0.5 M H2 SO4
solution.
At higher potential (1.12 V) delamination of Pt nanoparticles from
the carbon support takes place. The presence of the polymer is likely
to affect this process. The PRD of Pt/C electrodes exposed to pure
PA at 1.12 V differs from PRD of the same electrodes exposed to
ABPBI solution at the same potential. In the presence of ABPBI
larger particles are presented in the PRD. The increased viscosity
of the electrolyte in the presence of polymer probably reduces the
mobility of nanoparticles and the delamination rate. On the other
hand, the overall ESA loss is higher in the presence of polymer in the
whole potential range.
F594
Figure 7. TEM images of the cross section of the fuel cell MEA after
600 h test under open circuit conditions at 160◦ C (a) and (b), electron diffraction pattern of the area in panel b (c).
Degradation in operating fuel cells.—Open circuit conditions.—
On the TEM images of PBI-O-PhT membranes cross-sections (Fig. 7a
and 7b) obtained from MEA 1 after 600 h operation under open circuit
conditions one can see a layer of nanoparticles of a cubic shape at the
distance of about 3.5 μm (indicated with an arrow in Fig. 7a) from the
cathode surface. Electron diffraction helps to identify the crystalline
structure of the nanoparticles (Fig. 7c). Usual rings of face-centered
cubic structure are observed indicating that nanoparticles consist of Pt
re-deposited inside polymer membrane. This effect of Pt re-deposition
has been observed previously in the literature for LT-PEFC15 and is
explained by the chemical reduction of Pt dissolving at the cathode
and migrating into the membrane by hydrogen counterflow diffusing
through the membrane from the anode side. Using TEM images one
can estimate the amount of redeposited Pt and obtain lower estimate
of Pt dissolution rate (assuming all the dissolved Pt redeposits inside
the membrane). The thickness of a membrane cross section is 100 nm,
geometrical size of the membrane active area is 5 × 5 cm2 . Measuring
particle sizes and calculating their mass for TEM images of several
MEA cross-sections of known volume one may estimate the total
amount of Pt redeposited in the membrane as ∼2.5 mg (about 10% of
Pt loading in the 25 cm2 cathode). Since initial Pt SSA in the cathode
is about 50 m2 g−1 (determined by means of CV for an identical MEA;
CV measurements for MEAs 1 and 2 were not performed in order not
to affect Pt dissolution) and overall Pt loading in the cathode is ∼25
mg, the cathode ESA is ∼104 cm2 . Using equation 2 one may obtain
lower estimate of Pt dissolution rate of ∼10−13 g cm−2 s−1 .
The obtained estimate of Pt dissolution rate is in a good agreement
with potentiostatic experiments in our corrosion cell with reference
electrode. Indeed, Pt dissolution rate in a fuel cell under open circuit without externally applied potential is one order of magnitude
higher than the rate of carbon supported Pt dissolution in pure PA at
0.87 V, and one order of magnitude lower than the rate of dissolution of Pt in the presence of ABPBI dissolved in PA (see Table
I). We assume that chemical dissolution of Pt oxide species contributes significantly to the overall dissolution rate. Indeed, according to CV data (Fig. 2a) the formation of the oxide layer starts at
0.8 V which is somewhat lower than the potential of HT-PEFC cathode under open circuit conditions (about 0.9 V). Therefore under
Figure 8. TEM images of the cross section of the fuel cell MEA after 1000 h
of mixed operation: under constant load of 0.4 A cm2 for 9 h daily at 160◦ C
and without gas supply at room temperature overnight (a) and (b), particle
radius distribution (c), electron diffraction pattern of the area in panel b (d).
open circuit conditions Pt at the cathode is partially covered with
oxide which undergoes chemical dissolution.
Start/stop operation.—In reality operating fuel cells are never held at
OCV for so prolonged periods of time. Nevertheless, current interrupts
are inevitable, especially in mobile applications. MEA 2 was tested
under constant current load daily, and the current and gas supply were
turned off at night. In Figs. 8a and 8b one can see that after 1000 h
of functioning under this mode (250 h under constant load in total)
the amount of Pt redeposited in the membrane is also significant.
The observed electron diffraction pattern for the area presented in
Fig. 8b is typical for face-centered cubic structure of Pt (Fig. 8d).
The layer of Pt nanoparticles is broader and is located closer to the
surface of the membrane than for MEA 1. It is worth noticing that
size distribution of redeposited Pt particles is bimodal reflecting two
modes of operation: under current load at 160◦ C daily and in the
absence of current load cooled down to room temperature at night.
The shape of particles is close to spherical. According to TEM images,
the amount of Pt redeposited in the membrane is ∼0.5 mg (about 2%
of the initial loading in 25 cm2 cathode). This yield low estimate of Pt
integral dissolution rate of ∼10−14 g cm−2 s−1 . It is the same order of
magnitude as the rate of carbon supported Pt dissolution in pure PA
at 0.87 V.
Conclusions
Particle coarsening is the dominating mechanism of ESA loss of
carbon supported Pt in the potential range of 0.87–1.02 V. The coarsening is most likely due to migration and coalescence of nanoparticles.
At higher potential of 1.12 V Pt nanoparticle delamination starts to be
a key reason of dramatic decrease of ESA. The presence of ABPBI dissolved in PA does not affect particle coarsening in the potential range
0.87–1.02 V and probably slows down delamination of nanoparticles
at 1.12 V.
Yet, the distinct influence of polybenzimidazole (ABPBI) on the
dissolution rate of carbon supported and platinized platinum in PA
at 160◦ C at potentials corresponding to fuel cell OCV is confirmed
directly. The presence of ABPBI in the electrolyte results in significant (up to 2 orders of magnitude, for Pt/C at 0.87 V) increase
of dissolution rate. The accelerated dissolution in the presence of
polymer slightly accelerates ESA loss. It is worth noticing than the
effect of accelerated dissolution on the ESA loss is weaker than the
effect of particle coarsening. Nevertheless direct addition of PBI and
other polymers containing benzimidazole rings into the active layers
of fuel cell electrodes appears to be detrimental for the lifetime of
platinum based electrocatalysts.
Chemical dissolution of Pt oxide species contributes significantly
to overall dissolution rate under open circuit conditions and at high
anodic potentials.
Acknowledgments
The part of the research performed by M.S.K., M.O.G., and
A.V.Ch. as reported in this publication was supported by Skolkovo
Institute of Science and Technology. M.S.K. and M.O.G. also acknowledge the support from Russian Academy of Sciences within the
Basic Research Program of the Division of Chemistry and Materials
Sciences (Program No OKh-3).
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Degradation of High Temperature Polymer Electrolyte Fuel Cell

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