Journal of Nanomaterials

Volume 2012 (2012), Article ID 717913, 7 pages

doi:10.1155/2012/717913

Research Article

Nafion Titania Nanotubes Nanocomposite Electrolytes for High-Temperature Direct Methanol Fuel Cells

Nonhlanhla Precious Cele,¹ Suprakas Sinha Ray,² and Lucky Sikhwivhilu³

¹Department of Electrical Engineering, Centre for Energy and Electric Power, Tshwane University of Technology, Staartelitelite Road, Pretoria 0001, South Africa

²DST/CSIR Nanotechnology Innovation Centre, National Centre for Nano-Structured Materials, Council for Scientific and Industrial Research, 1-Meiring Naude Road, Brummeria, Pretoria 0001, South Africa

³Advanced Materials Division, DST/Mintek Nanotechnology Innovation Centre, Mintek, Private Bag X3015, Randburg, Johannesburg 2125, South Africa

Received 10 November 2011; Revised 15 May 2012; Accepted 22 May 2012

Academic Editor: Mauro Coelho dos Santos

Copyright © 2012 Nonhlanhla Precious Cele et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

Nafion-based nanocomposite membranes containing various amounts of titania nanotubes (TNTs) as an inorganic filler have been prepared using melt-mixing method and have been investigated for proton exchange membrane applications. The one-dimensional TNTs have been prepared from potassium hydroxide using hydrothermal route and conventional heating. Nafion R1100 in a protonated form was used, and TNT contents were in a range of 0.5–2.0 wt%. The acid-treated composite membranes, at lowest inorganic additive content, exhibited improved properties in terms of thermal stability and methanol (MeOH) permeability. The best performing nanocomposite was the membrane containing only 0.5 wt% TNTs showing ionic conductivity value of   at 26°C and 100% of relative humidity.

1. Introduction

Currently, titanium dioxide (TiO₂) or titania-derived nanotubes (TNTs) are examined in respect with their possible prominent applications such as catalyst supports [1], photocatalyst [2], gas sensing elements [3], and anode materials for batteries [4]. Titanium-dioxide-supported noble metal catalysts, such as gold [5], silver, or platinum [6, 7], are effective in many important processes, such as selective oxidation and hydrogenation and automobile engine exhaust systems [8].

Principal advantages of the nanotubular form seem to be related to the property that they have high specific surface area, which allows diffusion of active species. The crystal structure of TNTs seems to be a derivative for many photocatalytic applications. Another property is that TNTs are often open at the end and accessible for the interaction with gaseous substances. The TNTs are also thermally stable up to 600°C [6–9]. These are some of the essential criteria for fuel cell electrolytes membranes. This promotes to study the Nafion/TNTs nanocomposite membranes behaviour with the aim to improve Nafion properties such as fuel permeability and thermal and mechanical stability.

Nafion, whose primary structure consists of acid tipped side chains dangling from a perfluorinated backbone, is expected to be compatible with TNTs, due to its reactive nature. The metal ions present in TNTs such as is expected to increase thermal stability of Nafion membrane. The resistance of TNTs in presence of H₂ is likely to improve swelling and mechanical properties of Nafion membranes at higher temperatures greater than 100°C. Therefore, to understand the effect of the interactions between Nafion and TNTs on the proton exchange membrane properties, further investigations were carried out. In this study, the effects of TiO₂ nanotubes on Nafion properties such as water uptake, thermal stability, methanol (MeOH) permeability, and ion conductivity were investigated. The nanocomposite membranes were prepared using melt-extrusion method by varying the nanofiller loadings. The mechanical, thermal properties, and ionic conductivity of membranes were investigated using dynamic mechanical analyser (DMA), thermogravimetric analyser (TGA), and electrochemical impedance spectroscopy (EIS). The vibration studies were carried out by FTIR spectroscopy, providing information on the nanofiller/Nafion, nanofiller/H₂O, Nafion/H₂O interactions, and the conformation of fluorocarbon chains of Nafion hydrophobic domains. Methanol permeability was also investigated using the gas chromatography.

2. Experimental Details

2.1. Materials

Nafion precursor (R1100) was obtained from Ion Power. Potassium hydroxide (KOH) and titanium dioxide powder was purchased from Merck chemicals and used as received.

2.2. Synthesis of TiO₂ Nanotubes

-derived nanotubes (TNTs) were synthesized using a procedure described elsewhere [9–11]. In a typical procedure about 23 g of powder, P25 Degussa, was mixed with 200 mL of 18 M of aqueous solution of KOH. The mixture was heated at 150°C in an autoclave with constant stirring for 24 hours. The product was then washed with deionized water and then dried in an oven at 120°C for 14 hours.

2.3. Membrane Preparation

The TNTs were used as filler during the preparation of polymer nanocomposite membranes. The nanocomposite membranes were prepared by melt-extrusion method using a microextruder Reomix OS (HAAKE) instrument. Nafion (R1100) and TNTs were melt-mixed at 250°C at a rotor speed of 60 rpm for 10 min. The TNTs were added after 2 min of melting Nafion inside the extruder. For each nanocomposite, the amount of TNTs loaded was varied from 0.5 to 2.0 wt% to study the effect of TNTs loading on the properties of Nafion. The nanocomposites samples were then converted into sheets or films with a thickness of about 0.2 mm using a Carver laboratory press at 2 MPa and 250°C. The nanocomposites were then hydrolysed, to introduce cation exchange properties into the membranes. The nanocomposites were immersed in a mixture of 15 wt% potassium hydroxide, 50 wt% of deionized water, and 35 wt% of dimethyl-sulfoxide at 80°C for 2 hours. This was followed by the repeated immersion (three times) in a fresh 3 M nitric acid (HNO₃) for 1 h to complete protonation process.

2.4. Characterisation Techniques

2.4.1. Scanning Electron Microscopy (SEM)

Dry membranes were manually fractured after cooling in liquid nitrogen, to expose their cross section. The morphology of the fractured sample surfaces was analysed using SEM (LEO 1525), operating at an accelerating voltage of 3–10 kV.

2.4.2. The Fourier Transform Infrared

FTIR spectroscopy 800 from Perkin Elmer that was used to study the elementary composition of the nanocomposites studies were carried out from 500 to 4000 cm⁻¹.

2.4.3. X-Ray Diffraction

XRD patterns were measured on a Phillips X’Pert diffractometer using secondary graphite monochromatic CuKα radiation ( Å) at 40 kV/50 mA. Measurements were taken using angle of incidence detector at an angle of 2°, for 2 values over 10–70° in steps of 0.05°.

2.4.4. The Thermogravimetric Analysis

TGA was conducted on a TGA Q500 (TA Instruments) at a heating rate of 10°C/min in air, from room temperature to 800°C.

Mechanical properties of pure Nafion and its TNTs containing composite membranes were studied by a Perkin Elmer DMA 8000 in the dual cantilever bending geometry. The temperature dependence of loss tangent (, loss modulus/storage modulus) of all samples were measured at a constant frequency of 1 Hz with the strain amplitude of 0.02% from room temperature to 180°C with a heating rate of 2°C/min.

2.4.5. Electrical Conductivity

The electrical resistivity was measured at room temperature using the four point collinear probe method. The equidistant tungsten carbide probes have a separation distance () and probe radius of 0.127 cm and 0.005 cm, respectively. The  cm² samples were prepared with a thickness of about 0.2 cm. The Keithley 4200-SCS Semiconductor Characterisation System, equipped with four supply and measure units (SMUs) and an amplifier, was used to perform high-precision direct current characterisation by supplying currents ranging from 1 fA to 1 mA. The resistivity changes as a function of probe spacing (0.127 cm) and is given by:

where is the measured voltage, is the supplied current, and is the thickness of the films [10, 12]. The electrical conductivity is then given by

2.4.6. Electrochemical Impedance

Proton conductivity of fuel cell membrane was measured using a galvanostatic four-point probe AC electrochemical impedance spectroscopy (EIS) technique, which is relatively so insensitive to the contact impedance that it could be adequate to accurately test membranes with high conductivity. A standard electrochemical conductivity cell was used as a reference. The experimental data was fitted to the equivalent circuits and the electrolyte resistance () was estimated from fitting procedure. The proton or ionic conductivity () is calculated by

where is the proton conductivity, is the distance between the electrodes and   denotes the electrolyte resistance, respectively. and are the length and thickness of the membrane, respectively. The electrochemical cell was connected using a two-point probe technique to an Auto lab model 4.90006 potentiostat and Frequency Response Analyser (FRA). The home made cell was used with the electrode spacing of 1 cm, and the  cm² membranes were used. The FRA electrochemical impedance software was used for the impedance measurements and analysis from 1 MHz to 1 Hz with the AC voltage amplitude of 5 mV.

2.4.7. Liquid Uptake

The nanocomposites films were completely dried in vacuum at 100°C for 24 hours and weighed () and then placed in water/methanol (50/50) by volume solution at 25°C for 24 h. The nanocomposites films were then wiped dry quickly with filter paper and weighed (). The water/methanol uptake was then calculated as

A methanol diffusion homemade cell was used based on previous reports [13]. Compartment A was filled with methanol solution and compartment B was filled with the same volume of deionized water. The membrane was clamped between the two compartments, and these were kept under stirring conditions during the experiment to avoid any concentration build-up in the two compartments. Methanol concentration profiles were determined over a period of time at different operating temperatures. Samples were kept for about 30 min between compartments. The concentration of methanol was determined by gas chromatography (GC).

2.4.8. Methanol (MeOH) Permeability

The measurements were carried out using a testing device constructed in our laboratories. The polymer membranes with surface area of  cm² were inserted between vessels A and B. A 250 mL solution of MeOH (2 M) was transferred to vessel A, whilst vessel B was filled with 250 mL of deionised water (H₂O). After 24 h, the amount of methanol that crossed through the membrane to vessel B was determined by gas chromatography (GC 17A, Shimadzu model). The gas chromatograph was equipped with a capillary column (14% cyanopropyl phenyl methyl polysiloxane, ) and a flame ionisation detector (FID). The permeability of methanol through the membrane can be expressed with diffusion coefficient, () using (4) [14]

where is the slope of the concentration profile (mol/cm³ · s), is the volume of a solution in compartment (cm³), is thickness of the membrane (cm), is the active surface area of the membrane (cm²), and Δ is the difference of methanol concentration between two compartments (mol/cm³).

3. Results and Discussions

3.1. Structure and Morphology of Titania Nanotubes

The SEM results of the TNTs samples are shown in Figure 1. The samples show the tubular structures with diameter ranging from 10 to 20 nm. Large bundles of TNTs structures agglomeration are observed (see low magnification). This is attributed to the presence of ions in the TNT structures, which can lead to an increase in the surface charge and electrostatic attraction between the tubes leading to agglomeration. This thermodynamic synthesis mechanism results in the formation of KTiO₂(OH) due to the presence of .

Figure 1: The SEM micrographs of titanium dioxide nanotubes synthesised using hydrothermal conventional heating method.

Figure 2(a) shows the FTIR spectra for TNTs that have been annealed at 300°C. The peaks corresponding to physically adsorbed water (O–H stretching mode at ~3400 cm⁻¹ and O–H bending mode at ~1640 cm⁻¹) all disappeared due to the higher annealing temperature of 300°C. This is consistent with the literature [15]. Only the Ti–O stretching mode is observed at ~640 cm⁻¹ and 400 cm⁻¹; this is attributed to the amorphous and anatase phase of TNT. XRD patterns for TNTs are shown in Figure 2(b) revealed the presence of both anatase and rutile phase. The additional peaks are ascribed to the interaction of ions and TiO₂ and have been previously reported [10, 15].

Figure 2: (a) FTIR spectra of TNTs and (b) XRD patterns of TNTs synthesised using hydrothermal conventional heating method and annealed at 300°.

3.2. Structural Properties of Nanocomposite Membranes

The FTIR spectra showing vibration bands of Nafion and Nafion/TNTs nanocomposites are shown in Figure 3. The bands around 1200–620 cm⁻¹ denote – stretching, and the bands around 1050 cm⁻¹ denote the–SO₃-symmetric stretching. All these bands are characteristics of the Nafion membrane [14, 16–18]. The vibration bands of Nafion and nanocomposite membranes are similar; this might be due to the very small amount of TNTs loading or poor interaction with polymer matrix.

Figure 3: FTIR spectra of Nafion and its TNTs-based nanocomposite membranes with different TNTs loadings in wt% taken from 500 to 4000 cm⁻¹.

3.3. Morphology

The SEM investigation was performed on the nanocomposite membranes, and micrographs are shown Figure 4. Samples were frozen and fractured to expose the cross-sectional surface of the nanocomposite membranes containing various amounts of TNTs in wt% 4(a) 0.5, 4(b) 1.0, and 4(c) 2.0. The micrographs show the presence of inorganic structures, homogeneously dispersed into polymer matrix. This indicates the presence of bundle TNTs into Nafion matrix. SEM images show similar dispersion for all TNTs loadings. This is in agreement with XRD results, demonstrating that TNTs nanocomposite had the same d-spacing independent of TNTs loadings. This good dispersion suggests that the number of accessible sites on the surface of TNTs is high contributing to the adhesion and electrostatic interaction.

(a)

(b)

(c)

Figure 4: The SEM micrographs of the nanocomposite membranes containing various amounts of TNTs in wt% (a) 0.5, (b) 1.0, and (c) 2.0.

3.4. Water/Methanol Uptake and Electrical Conductivity

The hydration of the Nafion membranes is crucial to maintain higher proton conductivity. However, the methanol or fuel crossover must be reduced to avoid the catalyst poising and improve the fuel cell performance. The water/methanol uptake was analysed to maintain higher fuel cell performance. The water uptake increases from 19% for pure Nafion to a maximum of about 22% for 1.0 wt% TNTs composite as shown in Figure 5. The water uptake of N-0.5 wt% TNTs and N-2 wt% TNTs remains at about 20%. The increase in water uptake with addition of TNTs suggests an increase in hydrophilic nature of Nafion.

Figure 5: The bulk electrical conductivity and water-uptake plots of Nafion, and its TNTs-based nanocomposite membranes containing various amounts of TNTs.

The bulk electrical conductivity of Nafion and its TNTs-based nanocomposite membranes is shown in Figure 5. The electrical conductivity of Nafion increases from 0 to 0.06 , when modified with 0.5 wt% of TNTs; it further increases to about 0.08 , with 1.0 wt% incorporation. As the amount of TNTs into Nafion matrix increases to 2 wt%, the electrical conductivity decreases to zero, which is the same as that of pure Nafion. This decrease is associated with the electrical percolation threshold of Nafion and also the poor interaction between Nafion and TNTs as observed in FTIR spectra for 2 wt%.

3.5. Thermal Stability

Thermogravimetric analyses (TGA) of Nafion and its TNTs-based nanocomposite membranes are shown in Figure 6. Thermal degradation profiles of the nanocomposite samples are similar and show that the membranes are more thermally stable up to about 400°C compared to Nafion. The first degradation stage in a range of 30–120°C is assigned to the decomposition of physically adsorbed water present in the membranes. The weight loss in the range of 250–400°C is associated with the degradation of –SO₃H-groups of Nafion [17]. This increase in thermal stability is attributed to the presence of TiO₂ nanostructures into Nafion. The results show a slightly higher thermal stability for 0.5 wt% of TNTs. This is attributed to the good interaction between Nafion matrix, which is in agreement with the SEM results.

Figure 6: TGA plot of Nafion and TNTs-based nanocomposite membranes, with different loadings measured in nitrogen at 5°C per min.

3.6. Proton Conductivity and Methanol (MeOH) Permeability

To evaluate the influence of TNTs on the membranes electrochemical behaviour, electrochemical impedance spectroscopy measurements were performed. Figure 7  shows a Nyquist plot of Nafion and TNTs-based nanocomposites at 100% relative humidity. The plot gives electrolytes resistance () of the materials. The nanocomposite containing 0.5 wt% TNTs has the lowest  Ω (see Table 1). The electrolyte resistance increases as the TNTs  loading increases to 1.0 and 2.0 wt%. This is indicative of a decrease in proton conductivity. This suggests that the amount of TNTs strongly influence the proton conductivity of Nafion. This decrease in proton conductivity can be due to the TNTs structures hindering the permeability of hydrogen ions. Whereas the electrolytes resistance decreases when 0.5 wt% TNTs was incorporated, indicating an increase in proton conductivity compared to pure Nafion. This increase in proton conductivity is related to the increase in water uptake observed with 1 wt% TNTs nanocomposite. The MeOH permeability was increased to   with 1.0 wt% TNTs nanocomposite and sharply decreases to   as the amount of TNTs increases to 2 wt%. This behaviour is due to the MeOH permeability percolation threshold, which is affected by TNTs dispersed in Nafion.

Table 1: Parameters for circuit elements evaluated by fitting data to the equivalent circuit and calculated conductivity for prepared composite membranes. The average calculated error is about 8%.

Samples
t a
R b

P d
(/P)e

(cm)
(Ω)
(S/cm)
(cm²·s⁻¹)
(s·S·cm³)

Nafion
0.020
230
0.070

N-0.5 wt% TNTs
0.022
210
0.072

N-1.0 wt% TNTs
0.022
690
0.022

N-2.0 wt% TNTs
0.021
1150
0.014

aThickness of the membrane, belectrolyte resistance, cproton conductivity, dmethanol permeability of nanocomposite membranes, eratio of proton conductivity and water/MeOH uptake measurements.

Figure 7: Nyquist plots of Nafion and its TNTs-based nanocomposite membranes, with different TNTs loadings ranging from 0.5 to 2.0 wt%, measurements done at room temperature (26°C) and 100% relative humidity.

The ratio of proton conductivity () and methanol permeability () was calculated in order to estimate the performance of these nanocomposite membranes in fuel cell applications. The calculated values of proton conductivity and MeOH permeability are shown in Table 1. A decrease in the ratio was observed with an incorporation of TNTs in difference proportions.

4. Conclusion

In this paper, TNTs-based Nafion nanocomposite membranes were prepared in different proportions by melt-extrusion method. Water uptake of nanocomposite membranes resulted higher than that of pure Nafion, with N-1.0 wt% TNTs reaching maximum of 21.5%. The highest electrical conductivity was observed with 1.0 wt% TNTs nanocomposite but remains at zero with 2.0 wt% TNTs nanocomposite. The thermal stability of Nafion increases with incorporation of TNTs. A reduced MeOH permeability was observed with 2.0 wt% TNTs nanocomposite membrane. The proton conductivity of Nafion slightly increases when 0.5 wt% TNTs and then decreases with an increase in the amount of TNTs. The best performing nanocomposite was the membrane containing only 0.5 wt% TNTs showing ionic conductivity value of   at 26°C and 100% of relative humidity.

Acknowledgments

The authors would like to thank the Department of Science and Technology (RSA), the Council for Scientific and Industrial Research (CSIR), and the Tshwane University of Technology for financial support.

References

J. Z. Xu, W. B. Zhao, J. J. Zhu, G. X. Li, and H. Y. Chen, “Fabricating gold nanoparticle-oxide nanotube composite materials by a self-assembly method,” Journal of Colloid and Interface Science, vol. 290, no. 2, pp. 450–454, 2005.

I. Paramasivam, J. M. Macak, and P. Schmuki, “Fabrication of titania nanomaterial and study characters of dye-sensitized solar cells: from one-dimension to silver surface modification of TiO₂,” Electrochemistry Communications, vol. 10, no. 20, pp. 71–75, 2008.

S. K. Hazra and S. Basu, “High sensitivity and fast response hydrogen sensors based on electrochemically etched porous titania thin films,” Sensors and Actuators B, vol. 115, no. 1, pp. 403–411, 2006.

J. Xu, C. Jia, B. Cao, and W. F. Zhang, “Electrochemical properties of anatase TiO₂ nanotubes as an anode material for lithium-ion batteries,” Electrochimica Acta, vol. 52, no. 28, pp. 8044–8047, 2007.

L. Armelao, D. Barreca, G. Bottaro et al., “Recent trends on nanocomposites based on Cu, Ag and Au clusters: a closer look,” Coordination Chemistry Reviews, vol. 250, no. 11-12, pp. 1294–1314, 2006.

G. M. Nuñez, R. J. Fenoglio, and D. E. Resasco, “Enhanced methane production from methanol decomposition over Pt/TiO₂ catalysts,” Reaction Kinetics and Catalysis Letters, vol. 40, no. 1, pp. 89–94, 1989.

S. C. Chan and M. A. Barteau, “Preparation of highly uniform Ag/TiO₂ and Au/TiO₂ supported nanoparticle catalysts by photodeposition,” Langmuir, vol. 21, no. 12, pp. 5588–5595, 2005.

Y. Ishibai, J. Sato, S. Akita, T. Nishikawa, and S. Miyagishi, “Photocatalytic oxidation of NOx by Pt-modified TiO₂ under visible light irradiation,” Journal of Photochemistry and Photobiology A, vol. 188, no. 1, pp. 106–111, 2007.

M. M. Souza, N. F. Ribeiro, and M. Schmal, “SOFC using pure hydrogen considering air back diffusion phenomenon,” International Journal of Hydrogen Energy, vol. 32, no. 2, pp. 423–425, 2007.

L. M. Sikhwivhilu, S. Sinha Ray, and N. J. Coville, “Influence of bases on hydrothermal synthesis of titanate nanostructures,” Applied Physics A, vol. 94, no. 4, pp. 963–973, 2009.

T. Kasuga, M. Hiramatsu, A. Hoson, T. Sekino, and K. Niihara, “Formation of titanium oxide nanotube,” Langmuir, vol. 14, no. 12, pp. 3160–3163, 1998.

S. Pavlidou and C. D. Papaspyrides, “A review on polymer-layered silicate nanocomposites,” Progress in Polymer Science, vol. 33, no. 12, pp. 1119–1198, 2008.

N. P. Cele, S. Sinha Ray, S. K. Pillai et al., “Carbon nanotubes based nafion compositemembranes for fuel cell applications,” Fuel Cells, vol. 10, no. 1, pp. 64–71, 2010.

S. Quezabo, J. C. T. Kwak, and M. Falk, “An infrared study of water-ion interactions in perfluorosulfonate (Nafion) membranes,” Canadian Journal of Chemistry, vol. 62, no. 1, pp. 958–966, 1984.

U. Jeong and Y. Xia, “Synthesis and crystallization of monodisperse spherical colloids of amorphous selenium,” Advanced Materials, vol. 17, no. 1, pp. 102–106, 2005.

M. Falk, “An infrared study of water in perfluorosulfonate (Nafion) membranes,” Canadian Journal of Chemistry, vol. 58, no. 1, pp. 1496–1501, 1980.

H. L. Yeager and A. Steck, “Cation and water diffusion in nafion ion exchange membranes: influence of polymer structure,” Journal of the Electrochemical Society, vol. 128, no. 9, pp. 1880–1884, 1981.

Xie, Q. Zhuang, Q. Wang, X. Liu, Y. Chen, and Z. Han, “In situ synthesis and characterization of poly(2, 5-benzoxazole) / multiwalled carbon nanotubes composites,” Polymer, vol. 52, no. 1, pp. 5271–5276, 2011.