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Shuhui Sun, Gaixia Zhang, Xueliang Sun, Mei Cai, Martin Ruthkosky, "Highly Stable and Active Pt/Nb-TiO2 Carbon-Free Electrocatalyst for Proton Exchange Membrane Fuel Cells", Journal of Nanotechnology, vol. 2012, Article ID 389505, 8 pages, 2012. https://doi.org/10.1155/2012/389505
Highly Stable and Active Pt/Nb-TiO2 Carbon-Free Electrocatalyst for Proton Exchange Membrane Fuel Cells
The current materials used in proton exchange membrane fuel cells (PEMFCs) are not sufficiently durable for commercial deployment. One of the major challenges lies in the development of an inexpensive, efficient, and highly durable and active electrocatalyst. Here a new type of carbon-free Pt/Nb-TiO2 electrocatalyst has been reported. Mesoporous Nb-TiO2 hollow spheres were synthesized by the sol-gel method using polystyrene (PS) sphere templates. Pt nanoparticles (NPs) were then deposited onto mesoporous Nb-TiO2 hollow spheres via a simple wet-chemical route in aqueous solution, without the need for surfactants or potentiostats. The growth densities of Pt NPs on Nb-TiO2 supports could be easily modulated by simply adjusting the experimental parameters. Electrochemical studies of Pt/Nb-TiO2 show much enhanced activity and stability than commercial E-TEK Pt/C catalyst. PtNP/Nb-TiO2 is a promising new cathode catalyst for PEMFC applications.
Proton exchange membrane fuel cells (PEMFCs) have been attracting much attention as an alternative clean energy source because of their high efficiency, high power density, and low pollution . However, there are still challenges, such as, low catalytic activity, low durability, and high cost, which are hindering the commercialization of PEMFCs . For automotive applications, PEMFCs must be durable enough for ~5,000 driving hours (i.e., 10 years) in vehicles . The loss of platinum (Pt) electrochemical surface area (ECSA) over time due to carbon support corrosion and Pt dissolution/aggregation/Oswald ripening is considered one of the major contributors to the degradation of fuel cell performance . Usually, carbon black (Vulcan XC-72) is used as Pt catalyst support in PEMFCs. However, carbon black is known to undergo electrochemical oxidation under a fuel cell operating environment, especially at potentials above 0.9 V (1), leading to a loss of Pt and fuel cell performance degradation [4, 5]: Therefore, it is necessary to explore noncarbon catalyst support materials with the current fuel cell operating strategy. Some metal oxides have been studied by different research groups as alternative catalyst support materials, such as, substoichiometric titanium oxide [6, 7], indium tin oxide , niobium-doped titania , tungsten oxide [10, 11], and tin oxide . Among these, niobium-doped titania (Nb-TiO2) [9, 13–15] is a particularly promising candidate. TiO2 is notable for its photocatalytic and strong metal support interaction (SMSI) properties [16, 17]. TiO2 is also readily available, cheap, and nontoxic . The use of Nb doping has been found to significantly improve the electrical conductivity of TiO2, which allows its use in electrocatalytic reactions . In this study, we present a simple wet-chemical route to grow Pt nanoparticles (NPs) on mesoporous Nb-TiO2 hollow spheres, with controlled Pt loadings, in environmentally friendly aqueous solution. PtNPs/Nb-TiO2 catalysts exhibit higher catalytic activity for ORR and better stability than the benchmark E-TEK commercial Pt/C catalysts.
2. Materials and Methods
Hexadecyltrimethylammoniumbromide (HATB), titanium (IV) isopropoxide (TTIP), niobium (V) ethoxide (8 mol %), ethanol, HNO3, hexachloroplatinic acid (H2PtCl6·6H2O, 99.95%), and formic acid (HCOOH, 98%) were purchased from Sigma-Aldrich. Aqueous latex (mean diameter 200 nm) suspension (10 wt%) was purchased from Duke Scientific. All chemicals were used as received without further purifications. All solutions were prepared with ultrapure water purified with the Millipore water system (18.2 MΩ·cm resistivity @25°C).
2.2. Preparation of Mesostructured Nb-TiO2 Support
The mesostructured Nb-TiO2 support was prepared according to the method described in . Briefly, 0.015 g of HATB, 14.7 mL of aqueous latex suspension, and 105 mL of ethanol were added in a PTFE beaker, and then the solution was stirred vigorously for 30 min while HNO3 was added to adjust the pH to 3. A second solution was prepared by adding the precursors, 6.9 mL of TTIP and 0.5 mL niobium (V) ethoxide to 100 mL of ethanol. The second solution was added to the stirred latex-surfactant mixture using a peristaltic pump at a rate of 1 mL/min. The resulting suspension was processed using a Buchi B-290 spray drier to produce a fine white powder, consisting of the Nb-TiO2 and latex template, which was followed by heat treatment at 500°C for 2 h under argon in order to remove the latex template. To obtain rutile phase , the as-synthesized Nb-TiO2 powder were heated at 1050°C under hydrogen.
2.3. Preparation of PtNPs/Mesostructured Nb-TiO2 Composite
The Pt nanoparticles were synthesized by the formic acid method as described in the literature [20–22]. The as-prepared mesostructured Nb-TiO2 was used as the supporting substrate for Pt deposition. For the deposition of 40 wt% Pt on Nb-TiO2, 22 mg of H2PtCl6·6H2O (7.5 mg Pt) and 1 mL of HCOOH are added to 20 mL of water. Nb-TiO2 (11.25 mg) was then dispersed in the above solution by mild ultrasonication for 30 min. After this initial dispersion, the solution is heated to 80°C and kept at this temperature for 30 min. After the reaction is completed, the product was washed thoroughly with deionized water and then dried in a vacuum oven at 60°C.
2.4. Physical Characterization
The morphologies and microstructures of the as-prepared samples were examined by scanning electron microscope (SEM, Hitachi S-4800) operated at 5 kV, and transmission electron microscopy (TEM, JEOL JEM-2100) operated at 200 kV. X-ray diffraction (XRD) patterns were recorded on a Bruker D8 Advance diffractometer equipped with a Cu Kα radiation source. X-ray photoelectron spectroscopic (XPS) analysis was carried out in a VG ESCALAB 220iXL, using monochromated Al Kα source (1486.6 eV), at a base pressure of mbar. High-resolution spectra were obtained at a perpendicular take-off angle, using a pass energy of 20 eV and steps of 0.05 eV. All the binding energies were calibrated by referring to the C1s line at 284.8 eV from adventitious carbon. After Shirley background removal, the component peaks were separated using the public domain XPS Peak program version 4.1 .
2.5. Electrode Preparation
The electrochemical measurements were conducted at room temperature in a standard three-electrode cell using a glassy carbon (GC) rotating disk electrode (RDE) setup with a voltalab model PGZ100 potentiostat (Radiometer Analytical) and rotation control (MSR, Pine Instruments). A Pt wire served as the counter electrode, with a saturated calomel electrode (SCE) as the reference which was separated from the working electrode compartment by a closed electrolyte bridge. All potentials in this study, however, are referenced to the reversible hydrogen electrode (RHE). The working electrode was prepared with a procedure similar to the one reported previously . Typically, 5 mg catalyst was sonically mixed with 5 mL H2O/isopropanol/Nafion (5/1/0.0017 in volume ratio) for 12 min to make a suspension. GC disk electrodes (5 mm diameter, 0.196 cm2, Pine Research Instrument) served as the substrate and were polished to a mirror finish. An aliquot of catalyst suspension was pipetted onto the carbon substrate, resulting in approximate Pt loadings of 13 μgPt cm−2 for all catalysts. The catalyst films were dried under flowing nitrogen (N2) at room temperature.
2.6. Electrochemical Measurements
The working electrode, in an argon (Ar) purged 0.1 M HClO4 solution at room temperature, was first cycled 200 times between 0 and 1.1 V at a 1 V/s scan rate in order to produce a clean electrode surface. The cyclic voltammetry (CV) measurements were conducted by cycling the potential between 0 and 1.1 V, with a scan rate of 20 mV/s. The electrochemical surface areas (ECSA) were calculated from the hydrogen adsorption peak of the CV. The oxygen reduction reaction (ORR) experiments were performed in oxygen-saturated 0.1 M HClO4 solution at room temperature. The RDE rotating rate was 1600 rpm and sweep rate was 5 mV/s. Current densities were normalized in reference to the geometric area of the GC RDE electrode (0.196 cm2). The CV measurements for accelerated durability tests (ADT) were conducted by potential cycling between 0.60 and 1.40 V in a N2 purged 0.1 M HClO4 solution at room temperature, with a scan rate of 50 mV/s. In each case, ADT testing consisted of 30,000 cycles.
3. Results and Discussion
Figure 1(a) is an SEM image of the as-synthesized Nb-TiO2 nanostructures that clearly shows the hollow structures. The typical Nb-TiO2 spheres have diameters of 100–150 nm, which is the rutile phase confirmed by XRD analysis (JCPDS, no. 21-1276, Figure S1, see Supplementary Material available online at http://dx.doi.org/10.1155/2012/389505). The TEM image in Figure 1(c), further confirms that the shape of Nb-TiO2 nanostructures with mesoporous shells are spherical and fairly uniform in size. Furthermore, each mesoporous shell is composed of small, 10–20 nm nanoparticles. Figures 1(b) and 1(d) show the SEM and TEM images, respectively, of Pt NP/Nb-TiO2 composite with 20 wt% Pt loading. These images clearly display the homogeneous Pt deposition throughout the Nb-TiO2 support. The average sizes of Pt nanoparticles on Nb-TiO2 were obtained by measuring 100 randomly chosen nanoparticles under higher magnification TEM observation (Figure 2(a)). It is clearly seen that Pt nanoparticles with narrow size distribution have the mean size of 4 nm. The selected area electron diffraction (SAED) patterns reveal the single crystallinity of both Pt nanoparticles and the Nb-TiO2 support. High-resolution TEM (HRTEM) analysis (Figure 2(b)) further confirms the highly crystalline features of the support as well as Pt nanoparticles. The fringes with lattice spacing of 0.23 nm can be indexed as the (111) plane of face-centered-cubic (fcc) Pt, and the angle between two (111) planes also matches well with the fcc Pt. The lattice spacing of 0.25 nm can be indexed to (101) plane of rutile TiO2.
The Pt loading can be readily tuned by simply changing the mass ratio of the precursor and support, while keeping the ratio between Pt precursor and HCOOH constant. Figure 3(a) shows a TEM image of the product resulting from a mass ratio of H2PtCl6 precursor to substrate (Nb-TiO2) of 1 : 9, corresponding to 10 wt% Pt. At a higher mass ratio of 2 : 3, corresponding to 40 wt% Pt, the density of the Pt nanoparticles increases with some aggregation; however, their size remains consistent at approximately 4 nm.
X-ray photoelectron spectroscopy (XPS) was employed to study the chemical composition and status of the product. Figure 4 shows the Pt 4f, Ti2p, Nb3d, and O1s high-resolution XPS spectra taken from Pt/Nb-TiO2 composites with different Pt loading levels (10, 20, and 40 wt% Pt), which were calibrated by placing the principal C 1s peak at 284.8 eV. Obviously, continued weakening of the Ti2p signaled at 459.0 and 464.8 eV, Nb3d signaled at 207.6 and 210.3 eV, and O1s signaled at 532 eV is accompanied by the continued strengthening of the Pt 4f signals at 71.1 and 74.4 eV with increasing Pt content . These results suggest that the surface of the Nb-TiO2 spheres becomes more covered with Pt nanoparticles that shield the Nb-TiO2 surface from the XPS detection. The deconvolution of the Pt spectrum (inset in Figure 4(a)) shows only one doublet assigned as Pt 4f7/2 and Pt 4f5/2, which further confirms that the nanoparticles are pure metallic Pt. We obtained a relative atomic concentration ratio O : Ti of 2 for the products from the experimental XPS peak areas, which further confirms that the support is TiO2 with 8 at% Nb doping.
To study the electrochemical properties of the Pt NP/Nb-TiO2 composites, electrochemical measurements were conducted with a glassy carbon electrode (GCE) modified by Pt NPs/Nb-TiO2 composites, with Pt loadings of 10, 20, and 40 wt%, respectively. For comparison, a GCE supporting a commercial Pt/C catalyst (E-TEK) with 30 wt% Pt loading was also tested. Figure 5(a) shows the cyclic voltammograms (CVs) of these fours catalysts recorded at room temperature in Ar-saturated 0.1 M HClO4 solution at a scan rate of 20 mVs−1. For all electrodes, the Pt loadings were kept at approximately 13.0 μgPt/cm2. The CVs show strong peaks characteristic of hydrogen adsorption/desorption peaks below ~0.4 V and Pt oxidation/reduction peaks beyond ~0.6 V, and no considerable change in the shape is seen among these catalysts. The electrochemical surface areas (ECSAs) of Pt catalysts were determined by measuring the charge collected in the hydrogen (H) adsorption/desorption region after double-layer correction and assuming a value of 210 μC/cm2 for the adsorption of a monolayer of hydrogen . The obtained ECSAs for the four catalysts are listed in Table 1. We can see that commercial Pt/C catalyst (E-TEK) shows the largest electrochemical surface area (ECSA) with 57 m2/gPt. The 40 wt% Pt/Nb-TiO2 has ECSA value of 47 m2/gPt, followed by the 10 wt% and 20 wt% Pt/Nb-TiO2 which have ECSA values of 40 m2/gPt and 37 m2/gPt, respectively. Interestingly, while there is no observed trend in Pt ECSA with the increasing Pt loading on Nb-TiO2, it can be suggested that by this Pt deposition method, similar Pt particle size can be produced even at higher Pt loading on the metal oxide substrate.
Figure 5(b) shows the rotating disk measurements, at 1600 rpm, for the ORR on three Pt/Nb-TiO2 catalysts, along with the commercial Pt/C catalyst (ETEK) for comparison. The corresponding electrochemical parameters are listed in Table 1. From the figure, the ORR on all catalysts is diffusion controlled when the potential is less than 0.7 V and is under mixed diffusion-kinetic control in the potential region between 0.7 and 0.85 V. From Table 1, we can see that, as compared to the E-TEK Pt/C catalyst, 10 wt% PtNPs/NbTiO2 composite shows the best performance with 15% and 63% higher mass and specific activities, respectively. Furthermore, overall comparison of the ORR activities indicates that all the homemade PtNPs/Nb-TiO2 composites exhibit higher mass and specific activities than those of the commercial E-TEK Pt/C catalyst. This improvement in activity is significant considering 100 m2/g BET surface area  which is 2/5 of that of Vulcan XC carbon support of commercial Pt/C catalyst. The enhancement in the ORR activity might be due to the homogeneous distribution of small Pt nanoparticles and the mesoporous surface structure of the TiO2 hollow spheres.
The durability of the catalysts was determined in an accelerated durability test (ADT) by continuously applying linear potential sweeps from 0.60 to 1.4 V (versus RHE), causing surface oxidation/reduction of Pt and the oxidation of support. The surface reaction involves the formation of PtOH and PtO derived from the oxidation of water that causes the dissolution of Pt via the Pt2+ oxidation state [25, 26]. The test was conducted by applying potential sweeps at scan rate of 50 mV/s in a N2 saturated, 0.1 M HClO4 solution at room temperature. For comparison, commercial E-TEK Pt/C (30 wt% Pt) catalyst with a similar Pt loading as that in Pt/Nb-TiO2 (40 wt% Pt) was subjected to the same potential cycling conditions. It is generally believed that the performance degradation of the electrodes in PEMFC is mainly due to the ECSAs decrease of the catalysts. After 30,000 cycles, changes in the Pt ECSA were determined. As shown in Figures 6(a) and 6(b), cyclic voltammetry was used to determine the Pt surface area of Pt/Nb-TiO2 and Pt/C electrodes by measuring the H adsorption before and after potential cycling. Figure 6(c) shows that, for Pt/Nb-TiO2, ~40% of the original Pt surface area remained after 30,000 cycles potential cycling, which is 2.1 times higher than the ~19% remaining for the commercial E-TEK Pt/C catalyst. These results reveal that the Pt on Nb-TiO2 support is more electrochemically stable. The enhanced stability might be attributed to: (a) the higher corrosion resistance of Nb-TiO2 support compared to carbon in acidic environments, (b) a strong Pt-metal oxide support interaction inhibiting the sintering of the Pt [16, 17].
In summary, we have demonstrated a facile wet-chemical method to grow single-crystalline Pt nanoparticles on mesoporous Nb-doped TiO2 hollow spheres in aqueous solution, without using any surfactant. The use of Nb-TiO2 hollow spheres as substrate provides a new type of cost-effective support with high corrosion resistance for growing Pt nanoparticles. The growth density of Pt nanoparticles on Nb-TiO2 support could be controlled by manipulating the mass ratios between the Pt precursor and the Nb-TiO2 support. PtNP/Nb-TiO2 catalysts show enhanced activity and stability compared with the commercial E-TEK Pt/C catalyst.
This research was supported by General Motors of Canada, Natural Sciences and Engineering Research Council of Canada (NSERC), Canada Research Chair (CRC) Program, Canada Foundation for Innovation (CFI), and Ontario Early Researcher Award and the University of Western Ontario. S. Sun is grateful to the NSERC CGS scholarship and G. Zhang thanks the NSERC postdoctoral fellowship. The authors thank the help and discussion with Drs. P. Mani, M. Balogh, I. Butta, M. Militello, C. Wong, and X. Xiao.
Figure S1 shows the XRD pattern of Nb -TiO2 sphere support after heat treatment at 1050°C under hydrogen. It was apparent that rutile phase TiO2 was dominant in the product. In addition, a lower oxidation state of titanium (Ti4O7) was also detected by XRD. This phase has been known as one of the most highly conductive and most stable TinO2n–1 compounds . These phases could further improve the electrical conductivity for the TiO2, which is one of the important parameters for fuel cells.
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