Tungsten Oxide and Polyaniline Composite Fabricated by Surfactant-Templated Electrodeposition and Its Use in Supercapacitors

Zou, Benxue; Gong, Shengchen; Wang, Yan; Liu, Xiaoxia

doi:https://doi.org/10.1155/2014/813120

Journal of Nanomaterials

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Nanomaterials for Energy-Efficient Applications

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Volume 2014 | Article ID 813120 | https://doi.org/10.1155/2014/813120

Tungsten Oxide and Polyaniline Composite Fabricated by Surfactant-Templated Electrodeposition and Its Use in Supercapacitors

Benxue Zou,¹Shengchen Gong,¹Yan Wang,¹and Xiaoxia Liu²

Academic Editor: Yongfeng Li

Received20 Mar 2014

Accepted11 May 2014

Published29 May 2014

Abstract

Composite nanostructures of tungsten oxide and polyaniline (PANI) were fabricated on carbon electrode by electrocodeposition using sodium dodecylbenzene sulfonate (SDBS) as the template. The morphology of the composite can be controlled by changing SDBS surfactant and aniline monomer concentrations in solution. With increasing concentration of aniline in surfactant solution, the morphological change from nanoparticles to nanofibers was observed. The nanostructured WO₃/PANI composite exhibited enhanced capacitive charge storage with the specific capacitance of 201 F g⁻¹ at 1.28 mA cm⁻² in large potential window of ~ 0.65 V versus SCE compared to the bulk composite film. The capacitance retained about 78% when the sweeping potential rate increased from 10 to 150 mV/s.

1. Introduction

Electrochemical capacitors (supercapacitors) have been considered as green energy storage devices which offer a number of desirable features such as fast charging/discharging within seconds and long cycle life. In supercapacitors, energy storage is mainly based on underpotential deposition (namely, double layer capacitors) or some redox process (namely, pseudocapacitors). The limitation of electrochemical capacitors to widespread application is their relative low energy density. Thus the challenge for the electrochemical capacitors is to promote the energy storage capability, meanwhile maintaining its high charging/discharging rate. Nanostructured electrode materials can meet these demands due to their high energy storage capacities and power output densities [1, 2].

Conducting polymers and metal oxides in nanosize scale are expected to display enhanced capacitive performance because of their large surface area, high conductivity, and light weight. The very high surface area and low charge transport resistance of nanomaterials favored faster transport of charges and ions between electrode materials and electrolyte in comparison to the bulk materials. Recently, much work has focused on the development of nanomaterials for charge storage. Zhou and coworkers demonstrated that the capacitive performances of polyaniline (PANI) were enhanced with increasing its real surface area [3]. The nanofibrous PANI prepared by the pulse galvanostatic method displayed a high specific capacitance. Nanostructured NiO electrodeposited on stainless steel was reported to retain good supercapacitive performance at high scan rate [4].

Since the size and morphologies of nanoscale materials have significant influence on their properties, many efforts have been devoted to fabricate nanostructured materials [5, 6]. As we know, surfactant is widely used as additive to control the structure and morphologies of conducting polymers and inorganic species [7]. The surfactant self-assembled into organized templates in the bulk of solution or at interface offers potential to produce materials that retain its molecular imprint. It was reported that polymers with nanoparticle and nonfibrillar morphologies can be obtained by using anionic surfactant as the template, while those existing as nanofibers or nanorods structures can be afforded by cationic or nonionic surfactant-assisted chemical polymerizations [8]. Conducting polymer with nanosphere structures was reported to be obtained through an electrochemical synthesis from a surfactant containing solution [9]. Surfactant has also been used in the preparation of inorganic species with high surface area [10, 11]. For instance, Baeck and coworkers described an electrochemical strategy for the formation of thin nanostructured WO₃ films from dilute surfactant solution [12]. Brezesinski utilized supermolecular assemblies of surfactant molecules as the structure-directing template to synthesize a nanocrystal-based porous TiO₂ film [13].

Compared to single component materials, conducting polymer based nanocomposites exhibit superior properties due to the synergistic effects. Recently, Hu and coworkers embedded SnO₂ nanoparticles in the PANI networks by in situ polymerization on surfaces of inorganic metal oxide nanoparticles; these nanocomposites showed high rate capability and cyclic stability for supercapacitor [14]. Murugan et al. demonstrated an in situ intercalation polymerization of 3,4-ethylenedioxythiophene to prepare a nanocomposite of poly(3,4-ethylenedioxythiophene) (PEDOT) and MoO₃, in which the PEDOT was intercalated into layers of MoO₃ [15]. Composite films of WO₃ and PANI exhibited electrochromic properties with improved stability through immobilizing the oxide in the polymer matrix [16–18]. Our previous studies showed that the composites of PANI and WO₃ exhibited superior electrochemical sensing and pseudocapacitive properties compared to the respective single component [19, 20]. A model supercapacitor assembled by the obtained WO₃/PANI composite as the negative electrode material displayed a significantly promoted energy density and improved cyclic stability. In this work, we present a simple and convenient method to fabricate PANI and tungsten oxide nanostructured composites on carbon electrode by electrocodeposition with sodium dodecylbenzene sulfonate (SDBS) surfactant as the template. Morphologies of the composites were investigated by scanning electron microscopy (SEM), while cyclic voltammetry and chronopotentiometry (CP) were carried out to study capacitive properties of the composites.

2. Experimental

2.1. Materials and Instrumentation

Aniline was purified by distillation before use. All other chemicals were of analytical grade and used as received. Electrochemical experiments were conducted with a multichannel potentiostat (VMP3, Bio-Logic-Science Instruments) in a three-electrode electrolytic cell. The reference and counter electrodes were saturated calomel electrode (SCE) and platinum plate (ca. 1 cm²), respectively. Carbon cloth purchased from SGL (Germany) with geometric area of 0.78 cm² was used as the working electrode. All potentials are relative to the SCE.

2.2. Composite Films Preparation

Composite films of WO₃/PANI were electrochemically deposited on carbon substrates by cyclic voltammetry. A potential range between −0.6 and 0.9 V at 50 mV/s was used. Prior to the deposition of the film, the carbon substrates were cleaned by water and acetone and then cleaned by potential dynamic scanned from −1.0 to 1.0 V for 2 cycles in 1 M H₂SO₄. All the films were grown by 25 cyclic voltammetric scans and then rinsed with distilled water.

The solution used for composite film deposition contained tungsten acid (0.15 M), H₂O₂ (0.04 M), and H₂SO₄ (0.5 M) with different amount of aniline and sodium dodecylbenzene sulfonate (SDBS). SDBS concentrations of 0, 1.3, 2.6, 5.2, 57.4, and 130 mM were used and the films produced were denoted as , , , , , and .

The composite films prepared from solutions containing 57.4 mM SDBS in the presence of 75 and 175 mM aniline were denoted as and , while those from solutions containing 130 mM SDBS in the presence of 75 and 125 mM aniline were denoted as and , respectively.

2.3. Composite Film Characterization

Pseudocapacitive behaviors of the films were studied by cyclic voltammetry and chronopotentiometry (CP) in 1 M H₂SO₄ electrolyte. The morphologies of the samples were investigated by scanning electron microscopy (SEM, LEO SUPRA 35). The FT-IR spectra were recorded using Spectrum One FT-IR spectrometer (Perkin-Elmer, USA) with KBr pellets of powder samples scraped off from C substrate. The UV-vis spectra were recorded on composite films deposited on ITO using Lambda 35 UV/vis spectrophotometer.

3. Results and Discussions

3.1. Influence of SDBS Surfactant Concentration on Morphology of the Composite

Electrocodeposition of WO₃ and PANI was conducted through 25 cyclic voltammetric scans between −0.6 and 0.9 V at 50 mV/s in solutions containing various concentrations of SDBS surfactant. Surface morphologies of the composite films , , , , , and , obtained from 0, 1.3, 2.6, 5.2, 57.4, and 130 mM SDBS, were investigated by SEM (Figure 1). As can be seen in Figure 1, the particle size decreases with increasing concentration of SDBS in solution at lower concentration range (< 5.2 mM). The and composites show the smallest size of nanoparticles having average diameter of 10~50 nm. At the higher concentration of SDBS (e.g., 130 mM), particular large spherical particles assembled from 1D oriented nanoribbon-like structure were observed (Figure 1(f)), which indicate that the morphology of the composite is controllable by SDBS surfactant.

(a)

(b)

(c)

(d)

(e)

(f)

As we know, the SDBS surfactant consists of hydrophilic sulfonic acid and long hydrophobic alkyl chain. The spherical micelles are formed at the critical micelle concentration (cmc). The cmc for SDBS is about 1.5 mM in aqueous solution [21]. With the increase of SDBS concentration in solution, the spherical micelles self-assemble into larger spherical, cylindrical aggregates in solution, or flat bilayer micelles on the surface [22]. The aggregated micelles are negatively charged outside, so the anilinium cation can form complex structures by electrostatic interaction. The incorporation of aniline monomer with surfactant causes the aggregated micelle to swell and enlarge [7]. These complexes were assumed to serve as structure template in the electrochemical polymerization process. At the lower SDBS concentrations (about 2~4 cmc), the smaller spherical micelle may facilitate the smaller particle size of the composite formed on the electrode (Figures 1(c) and 1(d)). With the increasing concentration of SDBS (e.g., 130 mM), the micelle becomes larger and more SDBS may aggregate more aniline monomers inside/outside the micelle, which more likely lead to the original 1D direction growth of the polymers as shown in Figure 1(f).

3.2. Influence of Aniline Concentration on Morphology of the Composite

It is interesting to note that aniline concentration also significantly influences morphology of the composite. Figure 2 presents the surface morphologies of and films afforded from 57.4 mM SDBS solutions with 75 and 175 mM aniline and and films afforded from 130 mM SDBS solutions with 75 and 125 mM aniline, respectively. The composite particles tend to be of one-dimensional arrangement when aniline concentration increases in solution. Cationic anilinium is considered to be amphiphilic molecular because of its cationic head group and hydrophobic phenyl ring [23]. As the aniline concentration increases, more aniline monomer will be involved in micelle formation, and the competition between surfactant/monomer supermolecules and aniline monomer itself micelles may take place. Thus the increase of aniline concentration may exert influences on micelle compositions and structures. During the electrodeposition process, the preferentially 1D direction growth of polyaniline and the elongation of the rigid micelle result in the formation of 1D arrangement of the composite.

(a)

(b)

(c)

(d)

Similar trends were observed on similarly prepared PANI. Figure 3 shows the SEM images of PANI films of , , and electrodeposited from solutions containing 75, 125, and 175 mM aniline, respectively. PANI is prone to grow in 1D directions as the concentration of aniline increased in solution. The short PANI nanorods with average diameter of 150~200 nm gradually changed to long interconnected PANI nanofibers with diameter of 80~100 nm.

(a)

(b)

(c)

3.3. Influence of SDBS Concentration on Pseudocapacitive Properties of the Composite

To investigate the pseudocapacitive properties of the composite films, cyclic voltammetric scans were conducted on , , , , , and in 1 M H₂SO₄ (Figure 4(a)). The WO₃-related (A/A′) and PANI-related (B/B′ and C/C′) redox pairs can be seen in Figure 4(a), similar to our previously reported WO₃/PANI composite [19]. The redox pair B/B′ which corresponds to the exchange between fully reduced (leucoemeraldine) and half-oxidized (emeraldine) PANI is a good indicator for the electrochemical activity of PANI. The currents of B/B′ are higher for the composites made in the presence of SDBS than that from free of SDBS. When SDBS was added in the solution up to 2.6 mM, the WO₃-related (A/A′) peak currents on the cyclic voltammograms (CVs) of the composites were increased. However, the currents decreased with the further increase of SDBS concentration, indicating the restriction of the tungsten oxide deposition probably because of the strong electrostatic repulsive force between the negative headgroup of the surfactant micelles and tungstate anions (suggested by the micrograph of Figure 1(f)). The composite exhibited higher electroactivities of both WO₃ and PANI in Figure 4(a). This should be related to the nanostructure of the film which may provide more opportunity for the reactive centers on the film to contact with electrolyte and so facilitate the charge transfer in the bulk of the film.

(a)

(b)

The galvanostatic charge-discharge measurements were carried out by CP on these composite films (Figure 4(b)). The WO₃/PANI composite films display pseudocapacitive behaviors in a comparatively larger potential range from −0.5 V to 0.65 V versus SCE due to the combination of electrochemical activities of WO₃ and PANI. The large potential range is favored for the increase of energy density for supercapacitors. The specific capacitances of the composite films increase with the increase of SDBS concentration up to 2.6 mM (inset of Figure 4(b)). The CP results show that composite film exhibits the highest specific capacitance of 201 F/g. The inefficient contribution of WO₃ to the total capacitance of the composite can be observed in the negative potential range of the CP curves of and , which is in agreement with cyclic voltammetry results.

3.4. Characterization of the WP Nanocomposite

EDX and FT-IR spectra were recorded to characterize the typical nanocomposite of . The EDX spectrum displays the signals of W from WO₃ and N from PANI in Figure 5(a). From FT-IR spectra in Figure 5(b), exhibits characteristic vibrations of both PANI and WO₃. The peaks at 1575 and 1416 cm⁻¹ are due to the stretching vibration of quinoid (N=Q=N) and benzenoid (N–B–N) rings, respectively [23], which appear at 1566 and 1473 cm⁻¹ in the spectrum of PANI. Bands at 1135 cm⁻¹ in the spectrum of and 1114 cm⁻¹ in that of PANI are attributed to the characteristic band of protonated PANI [24]. As can be observed in Figure 5(b), the intensity of the peak at 1114 cm⁻¹ in the spectrum of PANI is rather higher than that of the . This is mainly attributed to the consumption of H⁺ near or on the electrode surface by WO₃ deposition process, which results in the decrease of the protonated degree of PANI in the composite. The deposition process of WO₃ can be represented by the following equation [25]:

(a)

(b)

The absorption peak at 1636 cm⁻¹ for , corresponding to the peak at 1630 cm⁻¹ for WO₃, is attributed to the in-plane bending mode (H₂O) of structure water [26]. The O–W–O stretching mode appears as a broad band around 620 cm⁻¹ which is similar to that of WO₃ at 618 cm⁻¹ [27]. The broad peak at 1058 cm⁻¹ in the WO₃ spectrum was overlapped with the characteristic protonated PANI peak at 1135 cm⁻¹ in the spectrum of .

The UV-vis spectra of the (deposited on ITO) were shown in Figure 6, together with the spectra of . The band at 320–360 nm corresponds to electron transition of benzenoid segments, which can be assigned to the intermediate state of PANI between leucoemeraldine and emeraldine [8]. The bands at ca. 470 and ca. 800 nm are concerned with the doping level and formation of polarons and bipolarons (quinoid segments), respectively. From Figure 6, the band at 320–360 nm in the spectra of moved to the long wavelength (red shift) in comparison with , likely because of the increasing delocalized degree of conjugate system in . Furthermore, the demonstrated the increased intensity of the band at ca. 470 nm and the absorption band at around 800 nm with a long tail, which correspond to the polaron bands related transitions, implying the emeraldine salt form of PANI in [5, 28].

3.5. Pseudocapacitive Properties of the WP Nanocomposite

Figure 7(a) presents the cyclic voltammograms of the composite film at scan rates of 10~150 mV/s with potential range from –0.5 V to 0.65 V. The mirror-like images of CV curves reveal the typical pseudocapacitive behavior with rapid current response on voltage reversal. The CV curves still remain nearly mirror-like image without obvious distortion even at scan rate of 150 mV/s. This excellent rate capability should be mainly attributed to the large accessible surface areas and low charge transport resistance provided by the nanostructures of the composite which facilitate electrolyte ion and charge transport during charge-discharge process. The area capacitance is calculated to be 0.284 F/cm² at thescan rate of 10 mV/s and 0.222 F/cm² at 150 mV/s. The capacitance retained about 78% when the scan rate increased from 10 to 150 mV/s, which is comparable to those of previously reported nano-MnO₂ (retained about 46% from 10 to 150 mV/s) [29], ordered mesoporous WO_3-x (about 45% from 10 to 50 mV/s) [30], and polyaniline stabilized WO₃ nanocomposite (about 36% from 5 to 100 mV/s) [18].

(a)

(b)

Constant current charge-discharge experiments were conducted on and by chronopotentiometry at various current densities. Ragone plots were obtained based on these experiments (Figure 7(b)). The film has much higher energy density than film at the same power density. The energy density of the electrode is found to be 37 Wh kg⁻¹ at the power density of 650 W kg⁻¹ and 25 Wh kg⁻¹ at 5 kW kg⁻¹, which is 46% higher than that of film at 650 W kg⁻¹ and 56% higher at 5 kW kg⁻¹. Moreover, the nanocomposite film also shows higher energy density and power density than other recently reported values of composite films (Figure 7(b)) [31–34].

4. Conclusions

The electrocodeposition of tungsten oxide and polyaniline composite nanostructures using SDBS surfactant as the template showed that both the SDBS and aniline monomer in the deposition solution could act as the structure direction reagent in the formation of the nanostructured composite film. The morphology of the composite is controllable by SDBS and aniline monomers in solution. The resulting composite film with spherical nanoparticles was formed from 2.6~5.2 mM SDBS (about 2~4 times of cmc). With the concentration of aniline monomer increased in the solution, one-dimensional growth trends were observed for both of PANI and the composites. Nanostructured composite of obtained from the solution containing 2.6 mM SDBS displayed the best capacitive performance and rate capability. The specific capacitance can be retained about 78% with the increasing of sweeping potential rate for cyclic voltammetric scans from 10 to 150 mV/s, which make it useful for negative electrode for supercapacitors.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgment

This work was supported by Liaoning Province new Ph.D. startup fund (Project no. 20131039).

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Copyright © 2014 Benxue Zou 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.

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