A Nafion-Ceria Composite Membrane Electrolyte for Reduced Methanol Crossover in Direct Methanol Fuel Cells

An alternative Nafion composite membrane was prepared by incorporating various loadings of CeO2 nanoparticles into the Nafion matrix and evaluated its potential application in direct methanol fuel cells (DMFCs). The effects of CeO2 in the Nafion matrix were systematically studied in terms of surface morphology, thermal and mechanical stability, proton conductivity and methanol permeability. The composite membrane with optimum filler content (1 wt. % CeO2) exhibits a proton conductivity of 176 mS·cm−1 at 70 ◦C, which is about 30% higher than that of the unmodified membrane. Moreover, all the composite membranes possess a much lower methanol crossover compared to pristine Nafion membrane. In a single cell DMFC test, MEA fabricated with the optimized composite membrane delivered a peak power density of 120 mW·cm−2 at 70 ◦C, which is about two times higher in comparison with the pristine Nafion membrane under identical operating conditions.


Introduction
Direct methanol fuel cells (DMFCs) are one of the promising alternative power sources for portable electronics such as laptops or mobile phones owing to their high energy density, low temperature operation, and low/zero emissions [1,2]. Besides, convenient storage of liquid methanol, and no need for auxiliary units such as humidifiers and reformers allows simple and compact DMFC designs. Despite these advantages, methanol crossover across a polymer electrolyte membrane (PEM) from the anode to the cathode compartment in DMFCs limits their wide spread commercial applications [3]. Methanol crossover not only reduces the fuel efficiency, but also poisons the cathode catalyst by direct oxidation of methanol, resulting in a mixed-potential at the cathode compartment [4]. Hence, the issue of methanol crossover needs to be addressed by developing alterative PEM materials to advance the overall performance of DMFCs.
The PEM is a key component in a DMFC which serves as a both a proton conductor and as a separator between the anode and the cathode reactants. Perfluorosulfonic acid membrane materials such as Nafion with first-rate proton conductivity, and high mechanical and thermal stability are being widely used as efficient PEM materials for fuel cells. However, the application of Nafion membranes in DMFCs is limited because of their high methanol permeability. As a result, it is essential to modify the Nafion membrane to meet the PEM requirements for DMFC applications. Generally, this can be done 2 of 13 by two approaches; (i) composite membranes with hydrophilic organic/inorganic fillers; (ii) surface modification by blending with other polymers [5]. Although the membranes fabricated via surface modification strategies shows a significant reduction in methanol crossover, the drastic reduction in proton conductivity severely affect their performance in fuel cells [6].
To have a balance between proton conductivity and methanol crossover, the composite approach wherein organic/inorganic fillers are incorporated into the Nafion network is believed to be an effective way to prepare the Nafion composite membranes. A major problem associated with this approach is how to obtain a uniform dispersion of the filler materials throughout the polymer matrix and it can be tackled by using nanosized high surface area fillers. Incorporation of nanosized hydrophilic inorganic fillers in the Nafion matrix reduces the methanol crossover by partially blocking the hydrophilic channels along with an improved water uptake and mechanical stability. Many efforts have been focused on the modification of Nafion membranes by incorporation of various inorganic nano fillers into the Nafion matrix to reduce methanol crossover while upholding its proton conductivity [7][8][9][10][11]. Nafion membranes modified with metal oxides such as TiO 2 [12,13], SiO 2 [14,15], aluminosilicates [3], etc., showed promising results towards the DMFC application. The addition of metal oxides with specific morphological properties select specific sites in the Nafion matrix and increase the interaction between polymer matrix and filler materials resulting in superior Nafion composite membranes [16]. Moreover, the hygroscopic nature of metal oxides improves the water retention properties of the resulting membranes. Consequently, many efforts have also been focused on the modification of Nafion membranes by nanofillers such as graphene [11], graphene oxides [9] and inorganic polysiloxane [17], and superior proton conductivity behavior of the resulting composite membranes, with efficient reduction in methanol crossover, has been demonstrated.
Cerium oxide, a rare-earth metal oxide with good hygroscopic properties was also explored as a potential filler material for Nafion in constituting a composite membrane [18,19]. Trogadas et al. studied the effect of incorporating cerium oxide nanoparticles into a Nafion membrane for PEM fuel cells and found that the addition of ceria to the PEM lowered the macroscopic degradation rate by over one order of magnitude without altering the proton conductivity [18]. Weissbach et al. prepared a Nafion-CeO 2 composite membrane and showed that the composite membrane exhibited higher stability with improved water uptake capacity compared to a bare Nafion membrane [19]. However, a detailed study on mitigating methanol crossover and direct performance evaluation of these membranes in the DMFC is lacking.
The present study focused on the preparation of an alternate Nafion composite membrane by incorporating nanosized cerium dioxide filler into a Nafion polymer matrix. The effect of ceria nanoparticles and optimization of the filler content in the composite membrane were examined in terms of methanol crossover, water uptake, proton conductivity, and thermal and mechanical stability along with DMFC performance evaluation. A DMFC comprising the proposed Nafion-CeO 2 (1%) composite membrane delivers a peak power density of 120 mW·cm −2 at 70 • C and ambient pressure and greatly suppresses the methanol permeability of about 40% in relation to the pristine Nafion membrane.

Preparation of Pristine Nafion and Nafion-CeO 2 Composite Membranes
The desired amount of CeO 2 nanoparticles was added into a 5 wt. % Nafion ionomer solution and mixed thoroughly in an ultrasonic bath for 1 h, followed by mechanical stirring for 12 h. The resulting admixture was then poured into a flat glass Petri dish and dried at 80 • C for 6 h. The composite membrane thus formed was removed by adding water. Before any further analysis, all the membranes were pre-treated with 0.5 M sulfuric acid (H 2 SO 4 ) at 80 • C for 1 h followed by washing with de-ionized water until the pH of the washing water reaches neutral. The thickness of all the composite membranes was measured using a digital micrometer and was found to be~160 µm. Pristine Nafion membrane of identical thickness was also prepared without any filler content for comparison.

Physicochemical Characterization
Cerium dioxide was characterized by powder X-ray diffraction (XRD) to identify the phases and to determine the crystallite size. XRD patterns were recorded on a Pan Analytical X-ray diffractometer (Philips, Coventry, UK) using Cu-Kα (λ = 1.54 Å) radiation. The scanning angle 2θ was between 5 • and 80 • with a step size 0.02 • . The surface morphology and corresponding quantitative elemental mappings of pristine Nafion and Nafion-CeO 2 composite membrane was examined in a Field Emission Scanning Electron Microscope (MIRA3, TESCAN, Brno, Czech Republic) equipped with an energy dispersive X-ray (EDX) spectrometer. Morphological differences between the Nafion-CeO 2 composite membranes in comparison with pristine recast Nafion was observed by atomic force microscopy (AFM; Pico SPM-Picoscan 2100, Molecular Imaging, Arizona, AZ, USA). The thermal stability of Nafion-CeO 2 composite membranes were studied using a STA 449 TG-DSC instrument (NETZSCH, Bavaria, Germany) in the temperature range between 30 and 800 • C at a heating rate of 5 • C·min −1 under nitrogen atmosphere. The mechanical strength for pristine Nafion and optimized composite membrane was evaluated from the stress-strain test on a Universal Testing Maching (UTM; H5KT-10066 US, Tinius Olsen Testing Machine Co., Horsham, PA, USA) at 30 • C.

Proton Conductivity
The in-plane proton conductivity of membranes was measured by a four-probe electrochemical impedance spectroscopy (EIS) method using a membrane conductivity cell (BT-112, Bekktech, Southern pines, NC, USA) at different temperatures [20]. The membrane samples with area of 1.5 cm × 2.5 cm were assembled in the cell in contact with four platinum electrodes placed at fixed positions. The potentiostat (SP-150, Biologic, Seyssinet-Pariset, France) was set to apply the frequency range between 1 MHz and 1 Hz and the ac impedance spectra was recorded with amplitude of 10 mV. The temperature and the humidity were controlled by a humidity chamber (SH-242, Espec, Hudsonville, MI, USA) and the samples were equilibrated for at least 30 min at requisite temperature and humidity conditions before the measurements. The resistance value associated with membrane conductivity was determined from the high frequency intercept of the impedance with the real axis. Proton conductivity was calculated using the measured resistance according to following equation: where, σ is the proton conductivity of the membrane in S·cm −1 ; L = 0.425 cm, the fixed distance between two Pt electrodes; R is the membrane resistance in Ω; W is the width of the sample in cm; and T is the thickness of the membrane in cm.

Water Uptake and Ion-Exchange Capacity of the Membranes
The water uptake capacity of the pristine and Nafion composite membranes was measured by measuring the weight difference between the dry and wet membranes. Membrane samples were first dried at 80 • C for 6 h and weight of the dried samples was recorded. The dried membrane sample was soaked in a glass container filled with de-ionized water at room temperature for 24 h. Then, the membrane sample was removed from water and excess surface water was quickly wiped off with tissue paper and the sample reweighed immediately. By using the wet and dry weight of the membrane samples, the water uptake was calculated from Equation (2): where, W d and W w are the weight of dry and wet membranes, respectively. Ion-exchange Capacity (IEC) is defined as the quantity of accessible sulfonic acid groups for proton exchange (in moles) per gram of polymer sample. The IEC of each sample was measured by the acid-base titration method [21]. A membrane sample (0.5 g) was soaked in 3 N NaCl (30 mL) for 24 h. To measure displaced H + ions in sample, a known volume of NaCl solution was titrated against 0.01 N NaOH solution using phenolphthalein as an indicator. IEC of the sample was calculated using the following equation: Volume of NaOH consumed × Molarity of NaOH Weight of the dried sample mmol/g (3)

Fabrication of the Membrane Electrode Assemblies (MEAs) and Fuel Cell Performance Evaluation
Catalyst slurry for the anode and the cathode catalyst layer was prepared by mixing the Pt-Ru/C (Pt-40 wt. % and Ru-20 wt. %) or 40 wt. % Pt/C catalyst with 5 wt. % Nafion ionomer and isopropyl alcohol. To constitute the anode and the cathode electrodes, the homogeneous catalyst slurries were applied on the GDL until a 2 mg·cm −2 metal loading is obtained. The MEAs were fabricated by hot pressing the pre-treated membranes sandwiched between the anode and cathode electrodes at 130 • C under 10 kg·cm −2 for 3 min.
The DMFC performances of the MEAs were evaluated in a standard 4 cm 2 fuel cell test fixture procured from Fuel Cell Technologies Inc. (Albuquerque, NM, USA). 2 M aqueous methanol solution and oxygen were supplied on the anode and cathode inlet of the DMFC, respectively. The flow rates of methanol and oxygen were 2 mL·min −1 and 250 mL·min −1 . The DMFC performance of pristine Nafion and Nafion-CeO 2 composite membranes with different filler content were evaluated at 70 • C under ambient pressure.

Methanol Permeability Measurements
Methanol permeability measurements was performed by the linear sweep voltammetry (LSV) technique in cell mode using a potentiostat (PGSTAT 30, Autolab, Utrecht, The Netherlands) in the voltage range from 0 and 1.0 V at the scan rate of 5 mV·s −1 [22]. Single cells with the active area of 4 cm 2 were assembled and conditioned at open circuit voltage (OCV) for 1 h at 70 • C. During measurements, oxygen on the cathode side was replaced by nitrogen at a flow rate of 100 mL·min −1 and the methanol was passed on the anode side at a flow rate of 2 mL·min −1 at room temperature. The cathode of the cell was served as working electrode and anode of the cell was served as counter and reference electrodes of the potentiostat. The current known as methanol cross-over current that was measured from the cell corresponded to the oxidation of diffused methanol, which reached a plateau when all the methanol was converted to CO 2 under steady state conditions [1].

Results and Discussion
As received CeO 2 powder was characterized by its powder X-ray diffraction pattern and FE-SEM for better understanding of its crystalline phases and surface morphology. Figure 1a shows the XRD pattern which displays diffraction peaks at 2θ of 28. group (COD 9009008). The obtained XRD patterns for CeO 2 are in good agreement with the literature reports [23,24]. By using the Scherrer formula, the crystallite size of CeO 2 was calculated from the (111) diffraction and it is found to be 52.62 nm. The morphology of CeO 2 was analyzed by FE-SEM and the corresponding images are presented in Figure 1b. It can be seen that the CeO 2 exhibits a cubic-like morphology. The incorporation of this nanosize CeO 2 in the Nafion matrix resulted in a uniform distribution. with the literature reports [23,24]. By using the Scherrer formula, the crystallite size of CeO2 was calculated from the (111) diffraction and it is found to be 52.62 nm. The morphology of CeO2was analyzed by FE-SEM and the corresponding images are presented in Figure 1b. It can be seen that the CeO2 exhibits a cubic-like morphology. The incorporation of this nanosize CeO2 in the Nafion matrix resulted in a uniform distribution. The surface morphology of recast pristine Nafion membrane and Nafion-CeO2 composite membrane were investigated by FE-SEM analysis and the corresponding images are shown in Figure 2. It can be seen that the pristine Nafion membrane has a relatively neat and smooth surface (Figure 2a). Cerium dioxide fillers dispersed homogeneously throughout the Nafion matrix and increased the surface roughness in case of composite membrane, as shown in Figure 2b. The EDX elemental analyses for pristine Nafion and Nafion-CeO2 composite membranes are shown in Figure 2f,g respectively. The existence of three peaks for Ce and the increased intensity of the O peak in the EDX spectrum of the composite membrane (Figure 2g) confirm the presence of CeO2 nanoparticles in the Nafion matrix. The density and distribution of C, O and Ce in the composite membrane is mapped as shown in (Figure 2c-e). The selected area used for mapping is shown in The surface morphology of recast pristine Nafion membrane and Nafion-CeO 2 composite membrane were investigated by FE-SEM analysis and the corresponding images are shown in Figure 2. It can be seen that the pristine Nafion membrane has a relatively neat and smooth surface (Figure 2a). Cerium dioxide fillers dispersed homogeneously throughout the Nafion matrix and increased the surface roughness in case of composite membrane, as shown in Figure 2b. The EDX elemental analyses for pristine Nafion and Nafion-CeO 2 composite membranes are shown in Figure 2f,g respectively. The existence of three peaks for Ce and the increased intensity of the O peak in the EDX spectrum of the composite membrane (Figure 2g) confirm the presence of CeO 2 nanoparticles in the Nafion matrix. The density and distribution of C, O and Ce in the composite membrane is mapped as shown in (Figure 2c-e). The selected area used for mapping is shown in the square box in Figure 2b. It can be seen that the elemental Ce of ceria nanoparticles is distributed homogeneously on the entire surface of the Nafion-CeO 2 composite membrane. Further, the O content is denser in the case of Nafion-CeO 2 composite membrane compared to the pristine Nafion membrane.
Energies 2017, 10, 259 6 of 13 the square box in Figure 2b. It can be seen that the elemental Ce of ceria nanoparticles is distributed homogeneously on the entire surface of the Nafion-CeO2 composite membrane. Further, the O content is denser in the case of Nafion-CeO2 composite membrane compared to the pristine Nafion membrane. Corresponding quantitative EDX elemental mappings for carbon (c), oxygen (d), ceria (e) for Nafion-CeO2 (1 wt. %) composite membrane (quantitative EDX elemental mapping performed on a particular area is marked in Figure 2b); EDX spectra of pristine Nafion (f) and Nafion-CeO2 (1 wt. %) composite membrane (g).
Deeper understanding of the interaction between fillers with Nafion matrix and the related morphological changes was obtained from AFM images as shown in Figure 3. The images were recorded for a scan area of 10 µm × 10 µm. As seen in topography image, the pristine Nafion possesses narrowed hydrophilic channels with smooth surfaces. On the other hand, the added CeO2nanoparticles effectively cover the hydrophilic channels causing increased surface roughness in the composite membranes. From the topography and phase images, we can clearly see significant changes in the surface morphology with the addition of CeO2, which indicates the strong interaction of filler material with the Nafion matrix. Figure 3e,f present the surface roughness analysis of the pristine and composite membranes. The root mean square (RMS) roughness values of 16.3 nm and 25.2 nm obtained for pristine and composite membranes, respectively, indicate an increase in the surface roughness in the case of composite membrane due to the presence of CeO2 nanoparticles. The increased roughness for Nafion composite membranes is highly beneficial to improve the contact between the electrodes and membrane.  Figure 2b); EDX spectra of pristine Nafion (f) and Nafion-CeO 2 (1 wt. %) composite membrane (g).
Deeper understanding of the interaction between fillers with Nafion matrix and the related morphological changes was obtained from AFM images as shown in Figure 3. The images were recorded for a scan area of 10 µm × 10 µm. As seen in topography image, the pristine Nafion possesses narrowed hydrophilic channels with smooth surfaces. On the other hand, the added CeO 2 nanoparticles effectively cover the hydrophilic channels causing increased surface roughness in the composite membranes. From the topography and phase images, we can clearly see significant changes in the surface morphology with the addition of CeO 2 , which indicates the strong interaction of filler material with the Nafion matrix. for Nafion composite membranes is highly beneficial to improve the contact between the electrodes and membrane. TGA curves of the pristine Nafion and Nafion-CeO2 composite membranes are compared in Figure 4a, wherein a typical three stage weight loss is observed for all the membranes. The primary weight loss at the temperature range between 30 and 200 °C is related to the loss of surface and bound water molecules. The second weight loss region between 200 and 400 °C corresponds to the degradation of ion-exchange functionalities from the side chains. No significant weight loss change was observed for both pristine and composite membranes up to this temperature range. The final weight loss between 400 and 500 °C is attributed to the degradation of the main chain (i.e., the Teflon backbone) of the Nafion membrane. The composite membranes showed a better stability at this temperature compared to pristine Nafion. This can be attributed to the presence of the ceramic fillers and their close interaction with the hydrophobic Nafion backbones [25]. The thermal degradation of pristine Nafion membrane concurs with the literature reports [26] and all the membranes retain up to 90% of their original weight until 300 °C in which the fuel cell operating temperature falls. The tensile strength of optimized Nafion-CeO2 (1 wt. %) composite membrane and pristine Nafion membrane are shown in Figure 4b. Even though the composite membrane exhibits a lower elongation, the Young's modulus (calculated by dividing stress by strain) for the composite membrane is 130 MPa, which is much higher than that of pristine Nafion membrane (71 MPa). TGA curves of the pristine Nafion and Nafion-CeO 2 composite membranes are compared in Figure 4a, wherein a typical three stage weight loss is observed for all the membranes. The primary weight loss at the temperature range between 30 and 200 • C is related to the loss of surface and bound water molecules. The second weight loss region between 200 and 400 • C corresponds to the degradation of ion-exchange functionalities from the side chains. No significant weight loss change was observed for both pristine and composite membranes up to this temperature range. The final weight loss between 400 and 500 • C is attributed to the degradation of the main chain (i.e., the Teflon backbone) of the Nafion membrane. The composite membranes showed a better stability at this temperature compared to pristine Nafion. This can be attributed to the presence of the ceramic fillers and their close interaction with the hydrophobic Nafion backbones [25]. The thermal degradation of pristine Nafion membrane concurs with the literature reports [26] and all the membranes retain up to 90% of their original weight until 300 • C in which the fuel cell operating temperature falls. The tensile strength of optimized Nafion-CeO 2 (1 wt. %) composite membrane and pristine Nafion membrane are shown in Figure 4b. Even though the composite membrane exhibits a lower elongation, the Young's modulus (calculated by dividing stress by strain) for the composite membrane is 130 MPa, which is much higher than that of pristine Nafion membrane (71 MPa). Water uptake and ion-exchange capacity have a strong influence on the proton conductivity of a PEM. The water molecules present in a PEM play a vital role in the proton conduction via both the vehicular and Grotthuss mechanisms. The water uptake and IEC values of pristine Nafion and Nafion-CeO2 composite membranes are listed in Table 1. Table 1. Water uptake capacity, Ion-exchange capacity, proton conductivity, peak power density, methanol crossover current density of pristine Nafion and Nafion-CeO2 Composite membranes. From the table, the water uptake capacity of the composite membranes considerably increased upon addition of CeO2 nanoparticles compared to pristine Nafion membrane. The water uptake Water uptake and ion-exchange capacity have a strong influence on the proton conductivity of a PEM. The water molecules present in a PEM play a vital role in the proton conduction via both the vehicular and Grotthuss mechanisms. The water uptake and IEC values of pristine Nafion and Nafion-CeO 2 composite membranes are listed in Table 1.
From the table, the water uptake capacity of the composite membranes considerably increased upon addition of CeO 2 nanoparticles compared to pristine Nafion membrane. The water uptake capacity of composite membrane with 1 wt. % filler content is about 25.9% as compared to 18.3% for pristine membrane. The increase in water uptake capacity of the composite membranes can be attributed to the hygroscopic nature of CeO 2 nanoparticles and their uniform distribution over the polymer matrix. However, the water uptake decreased when the content of CeO 2 is more than 1 wt. %, probably due to the aggregation of oxide filler in the composite membrane [27]. Table 1. Water uptake capacity, Ion-exchange capacity, proton conductivity, peak power density, methanol crossover current density of pristine Nafion and Nafion-CeO 2 Composite membranes. IEC, which measures the density of proton exchangeable groups present in the membrane, is an important parameter. The IECs of pristine Nafion and Nafion-CeO 2 composite membranes was measured and are summarized in Table 1. The IEC of pristine Nafion is about 0.91 m·mol·g −1 , and the IEC value of all the composite membranes was slightly lower. The decrease in the IEC value of composite membrane is mainly due to the addition of CeO 2 nanoparticles with no proton dissociation ability and a trivial ionic aggregation in the Nafion-CeO 2 composite matrix.

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Besides the filler content in the composite membrane, the size, shape and dispersion of filler particles play a major role and are the deciding factors in determining membrane compatibility, proton conductivity, methanol permeability, etc. [28]. The addition of nanofillers to the Nafion matrix without any phase separation increases the proton conductivity due to the higher water uptake capacity and hinders the methanol transport across the membrane. The proton conductivity of pristine Nafion and Nafion-CeO 2 composite membrane as a function of temperature under fully humidified conditions is shown in Figure 5. The proton conductivity of all the membranes gradually increased as the temperature increased up to 90 • C, and started to decline at 100 • C due to the non-availability of adequate water molecules. At all the temperatures, Nafion-CeO 2 composite membranes showed superior proton conductivity compared to pristine Nafion membrane. The measured proton conductivity for the pristine Nafion membrane and Nafion composite membrane with 1 wt. % CeO 2 content at 70 • C is 136 mS·cm −1 and 176 mS·cm −1 , respectively. The increase in the proton conductivity of about 30% for the composite membranes is mainly due to their higher water uptake capacity with specific orientation and interaction of fillers with the polymer. The bulk water molecules present in the membrane act as charge carriers according to the vehicular mechanism [29]. Thus, the proton conductivity appreciably increased for the composite membrane developed in this study as a result of superior vehicular mechanism although there is small decline in the IEC. Nevertheless, conductivity slightly decreased for the Nafion-CeO 2 composite membrane with the filler content of above 1 wt. % because of its lower water uptake and sensible interruption in the proton conducting channels of the Nafion.
In DMFC, methanol crossover is a critical factor which is responsible for about a 30% performance reduction as methanol crossover results in cathode catalyst poisoning and low fuel efficiency. Nafion possesses high methanol permeability because of its widened hydrophilic channels, and partially blocking these channels will significantly reduce the crossover. In the composite approach, the extent of methanol crossover largely depends on the distribution of fillers and their effective interaction with the polymer matrix [30]. The uniform distribution of added fillers in Nafion membranes reduces the size of channels that are available for methanol passage whereas immense agglomeration has a negative impact on methanol crossover. The methanol crossover limiting current densities of pristine Nafion and Nafion-CeO 2 composite membranes were measured electrochemically and the results are shown in Figure 6. It can be clearly seen that the methanol crossover decreases after modification of the Nafion membrane with CeO 2 nanoparticles. A limiting current density of 106 mA·cm −2 is obtained for the single cell assembled with 1.25 wt. % CeO 2 -Nafion composite membrane, which is about 40% lower than that of pristine Nafion membrane (181 mA·cm −2 ). The decrease in methanol crossover can be understood from the FE-SEM surface morphology of Nafion-CeO 2 composite membrane where the CeO 2 nanoparticles are uniformly distributed in the Nafion matrix.
to the non-availability of adequate water molecules. At all the temperatures, Nafion-CeO2 composite membranes showed superior proton conductivity compared to pristine Nafion membrane. The measured proton conductivity for the pristine Nafion membrane and Nafion composite membrane with 1 wt. % CeO2 content at 70 °C is 136 mS·cm −1 and 176 mS·cm −1 , respectively. The increase in the proton conductivity of about 30% for the composite membranes is mainly due to their higher water uptake capacity with specific orientation and interaction of fillers with the polymer. The bulk water molecules present in the membrane act as charge carriers according to the vehicular mechanism [29]. Thus, the proton conductivity appreciably increased for the composite membrane developed in this study as a result of superior vehicular mechanism although there is small decline in the IEC. Nevertheless, conductivity slightly decreased for the Nafion-CeO2 composite membrane with the filler content of above 1 wt. % because of its lower water uptake and sensible interruption in the proton conducting channels of the Nafion. In DMFC, methanol crossover is a critical factor which is responsible for about a 30% performance reduction as methanol crossover results in cathode catalyst poisoning and low fuel efficiency. Nafion possesses high methanol permeability because of its widened hydrophilic channels, and partially blocking these channels will significantly reduce the crossover. In the composite approach, the extent of methanol crossover largely depends on the distribution of fillers and their effective interaction with the polymer matrix [30]. The uniform distribution of added fillers in Nafion membranes reduces the size of channels that are available for methanol passage whereas immense agglomeration has a negative impact on methanol crossover. The methanol crossover limiting current densities of pristine Nafion and Nafion-CeO2 composite membranes were measured electrochemically and the results are shown in Figure 6. It can be clearly seen that the methanol crossover decreases after modification of the Nafion membrane with CeO2 nanoparticles. A limiting current density of 106 mA·cm −2 is obtained for the single cell assembled with 1.25 wt. % CeO2-Nafion composite membrane, which is about 40% lower than that of pristine Nafion membrane (181 mA·cm −2 ). The decrease in methanol crossover can be understood from the FE-SEM surface morphology of Nafion-CeO2 composite membrane where the CeO2 nanoparticles are uniformly distributed in the Nafion matrix. The application of composite membranes developed in this study was evaluated in a DMFC single cell at 70 °C under ambient pressure. Comparative polarization curves and power densities of pristine Nafion and Nafion-CeO2 composite membranes are shown in Figure 7a. The pristine Nafion membrane showed a high polarization loss and low peak power density due to the high methanol crossover and low proton conductivity. In contrast, MEAs fabricated with the Nafion-CeO2 composite membranes exhibited higher peak power densities compared to pristine Nafion membrane. Among the composite membranes, Nafion-CeO2 composite membrane with 1 wt. % filler content possesses a peak power density of 120 mW·cm −2 which is about 50% higher than that of pristine Nafion membrane under identical operating conditions. The high proton conductivity and low methanol permeability are responsible for the improvement in overall cell performance. Even though the composite membrane with 1.25 wt. % CeO2 has a lower methanol permeability, it exhibits a lower peak power density compared to Nafion-CeO2 (1 wt. %) mainly due to its lower The application of composite membranes developed in this study was evaluated in a DMFC single cell at 70 • C under ambient pressure. Comparative polarization curves and power densities of pristine Nafion and Nafion-CeO 2 composite membranes are shown in Figure 7a. The pristine Nafion membrane showed a high polarization loss and low peak power density due to the high methanol crossover and low proton conductivity. In contrast, MEAs fabricated with the Nafion-CeO 2 composite membranes exhibited higher peak power densities compared to pristine Nafion membrane. Among the composite membranes, Nafion-CeO 2 composite membrane with 1 wt. % filler content possesses a peak power density of 120 mW·cm −2 which is about 50% higher than that of pristine Nafion membrane under identical operating conditions. The high proton conductivity and low methanol permeability are responsible for the improvement in overall cell performance. Even though the composite membrane with 1.25 wt. % CeO 2 has a lower methanol permeability, it exhibits a lower peak power density compared to Nafion-CeO 2 (1 wt. %) mainly due to its lower proton conductivity behaviour. Stability of the pristine Nafion and Nafion-CeO 2 (1 wt. %) composite membrane was evaluated in DMFC under OCV condition at 70 • C for 50 h as shown in Figure 7b. After 50 h of test, Nafion-CeO 2 (1 wt. %) composite membrane showed improved stability compared to pristine Nafion under identical operating conditions and is exclusively credited to the presence and interaction of nanofiller materials with the Nafion matrix.

Conclusions
In this study, we have developed a novel Nafion composite membrane by incorporating CeO2 nanoparticles for application in DMFCs. The composite membrane showed improved proton conductivity with low methanol permeability as a result of effective interaction of nanosized CeO2 with the polymer matrix. As a result, the optimized composite membrane (Nafion-CeO2 (1 wt. %) delivered a peak power density of 120 mW·cm −2 which is about 50% higher than that of a pristine Nafion membrane. These results established that the Nafion-CeO2 composite membranes developed in this study area promising candidate as high performing polymer electrolyte membranes for DMFC applications.

Conclusions
In this study, we have developed a novel Nafion composite membrane by incorporating CeO 2 nanoparticles for application in DMFCs. The composite membrane showed improved proton conductivity with low methanol permeability as a result of effective interaction of nanosized CeO 2 with the polymer matrix. As a result, the optimized composite membrane (Nafion-CeO 2 (1 wt. %) delivered a peak power density of 120 mW·cm −2 which is about 50% higher than that of a pristine Nafion membrane. These results established that the Nafion-CeO 2 composite membranes developed in this study area promising candidate as high performing polymer electrolyte membranes for DMFC applications.