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International Journal of Polymer Science
Volume 2013 (2013), Article ID 903806, 6 pages
http://dx.doi.org/10.1155/2013/903806
Research Article

Preparation of Conductive PANI/PVA Composites via an Emulsion Route

1College of Fashion, Shanghai University of Engineering Science, Longteng Road, Shanghai 201620, China
2Shangtex Holding Co., Ltd., Pingliang Road, Shanghai 200082, China

Received 12 July 2013; Accepted 6 November 2013

Academic Editor: Xiao-Hong Qin

Copyright © 2013 Xiang-Qin Wang 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

A facile and novel strategy for preparing polyaniline/polyvinyl alcohol (PANI/PVA) composite emulsion is reported wherein the reaction is carried out via the emulsion polymerization using ammonium peroxydisulfate (APS) as the oxidizing agent and dodecylbenzene sulfonic acid (DBSA) as the protonic acid. The PANI/PVA composite membranes have been characterized using optical microscope, scanning electron microscope (SEM), thermogravimetric analysis (TGA), Fourier transform infrared spectroscopy (FTIR), and electrochemical workstation. It is interesting that the electrical conductivity of the PANI/PVA composites is estimated to be as high as 1.28 S/cm. The experimental results show that the surface of PANI/PVA composite membranes exhibits good integrity. The PANI particles at the nanoscale are dispersed in the PVA matrix, and the electrochromic behaviors of PANI/PVA composites obtained at different polymerization temperatures can be compared based on cyclic voltammetry (CV) curves, revealing that PANI/PVA composites synthesized at room temperature are better than those synthesized at low temperature.

1. Instruction

Polyaniline (PANI), one of the most thoroughly studied conducting polymers, has received great attention due to its high electrical conductivity, easy producibility, thermal and environmental stability, energy storage, and sensible and electrochemical properties, as well as relatively low cost [1]. The potential applications of PANI include organic lightweight batteries [2], redox capacitors, electromagnetic shielding devices [3], microelectronic devices [4, 5], sensors [611], and electrochromic displays [1219]. A method of preparing the PANI was first presented by Letheby in 1862 [20]; however, the conductive nature and electrochemical property have not been studied in-depth until the late last century. From the early 20th century on, occasional reports about the structure of PANI were published. Subsequent to the investigation of other highly conductive organic materials, MacDiarmid demonstrated the conductive states of PANI which arose upon protonic doping of the emeraldine form of PANI [21]. Conductive polymers such as PANI remain of widespread interest [22], providing an opportunity to address fundamental issues of importance to condensed matter physics, including the metal insulator transition [23], the Peierls instability, and quantum decoherence [24].

During the past few decades, attention has been devoted to the use of conductive polymeric composites for fabrication of displays and sensor devices due to their better stability, flexibility, and cost effectiveness [25]. Extensive studies on the gas sensing properties of conducting PANI composites [26, 27] and polypyrrole (PPy) composites for various oxidizing and reducing gases have been reported [28, 29]. However, in order to solve the limitations on their solubility and electrochemical properties of the conductive PANI composites, which are mainly due to the polymerization ways, nonhomogeneous composite formation, and doping-dedoping properties of the conducting polymers, it is necessary to develop a real composite of conductive polymers with the essential properties of the conductive polymers in addition to the improved processibility and mechanical properties.

In this work, an attempt has been made to prepare a conducting PANI composite material with reasonable conductivity along with good mechanical properties. The PVA reagent is selected as the polymer matrix for the preparation of the composite membrane, and the emulsion polymerization technique with the DBSA as proton acid dopant is used to synthesize the PANI/PVA emulsion. The properties of the PANI/PVA composites obtained from emulsion polymerization have been characterized attached with the related explanations and discussions.

2. Experimental

2.1. Raw Materials and Reagents

Aniline (AN), polyvinyl alcohol (PVA), ammonium persulfate (APS), dodecyl-benzene sulfonic acid (DBSA), and indium-tin-oxide (ITO, (35 ± 5 ohm/sq)) film were purchased. All the chemical reagents were used without further purification, and the distilled water was used during the experiments.

2.2. Preparation of PANI/PVA Composite Emulsion

PANI/PVA composites emulsion was produced using the APS oxidant dissolved in emulsion contained PVA, DBSA, and AN monomer in a three-neck round bottomed flask equipped with mechanical stirring, thermometer, and titration funnel. At first, the the solution contained in the flask was heated at 90°C for 20 minutes to 40 minutes to make PVA particles dissolve adequately, and the reaction mixture was stirred for 30 minutes to ensure that the mixture was cooled to room temperature. The solution appeared to be milk white after the addition of the DBSA reagent and AN monomer sequently. The 10 mL aqueous solution of APS was dropped into the emulsion at different temperatures. The stirring of the mixture continued for another 4 hours after the color of emulsion turned into dark green; the PANI/PVA composite emulsion was obtained for the preparation of the PANI/PVA composite membranes.

2.3. Preparation of PANI/PVA Composite Membranes

PANI/PVA composite membranes were prepared using the spin-coating machine (KW-4A Model). An appropriate amount of solution was spread on the substrate of the instrument into a thin film at the rotational speed of 600 rpm (evolutions per minute) for 15 s (second) and 5000 rpm for 40 s. The PANI/PVA composite membranes were obtained after drying in a vacuum oven at the room temperature for about 4 hours.

2.4. Characterization and Analysis

The four-probe tester with a measuring range of 10−2~105 Ω and the UT70A universal digital multimeter with a higher limit of the measuring range about 103 Ω were used to measure the surface resistivity of PANI/PVA composite membranes.

The XS-213 optical microscope and the S-3400N scanning electron microscope (SEM) with a resolution at nanoscale were used to analyze the morphology of the PANI/PVA composite membranes.

The AVATAR 380 Fourier transform infrared spectroscopy (FTIR) analyzer was used to characterize the molecular structure and chemical composition of PANI/PVA composites. The spectra data were recorded from 3800 to 750 cm−1 with the step size of about 1.929 cm−1.

The Germany STA PT-1000 thermal gravimetric (TG) analyzer was used to investigate the thermal stability of PANI/PVA composites. The samples were heated from room temperature to 700°C at a slow heating rate of 10°C/min. The TG experiment was carried out in the nitrogen atmosphere with the gas flow of 100 mL/min.

The CHI420A type electrochemical workstation was used to investigate the electrochromic properties of PANI/PVA composite membranes.

3. Results and Discussion

3.1. The Doping Mechanism of PANI

The PANI was synthesized with the molar ratio of APS to aniline monomer set to be 0.95–1 : 1 and the molar ratio of DBSA to aniline monomer set to be 1.03 : 1 in our experiments. The conductivity of PANI composite membrane can be up to 1.28 S/cm.

As illustrated in Figure 1, the basic skeleton of the molecular chain of PANI does not change after doping by DBSA protonic acid; only the electrons are transferred and rearranged within the molecular chain. The doping process of PANI could be divided into three steps from nonconductive state to a conductive state.

903806.fig.001
Figure 1: The doping mechanism of PANI.

Step  1. DBSA is decomposed into H+ in the emulsion, and then the H+ is combined with N atom, which is from the polymer chain between the head and the tail of the class quinone of PANI oxidation unit. The univalent N atoms were converted to univalent positive charge, because the H+ had no valence electrons; when bonding with the N, the N atoms provided the electron, thereby enabling the polymer chains to take positive charge.

Step  2. Because the class quinone structure with univalent N atoms is unstable, the rearrangement of electrophilic substitution reaction is prone to occur in AN molecular. So, the polymer chains within the charge can be redistributed, and the partial positive charge N atoms are transferred from the quinone structure to the N atoms on the benzene’s reducing unit. On the contrary, the electrons can be diverted from the benzene structure to the quinone structure; the benzene structure is partially oxidized attributed to the loss of electrons, and the quinone ring of the quinone structure is partially reduced due to the achieving of electrons. So, the ring electronic structure tends to be similar. Therefore, it can be seen that the doping of PANI is a unique intramolecular redox reaction, no gain or loss of electrons.

Step  3. The charge rearrangement of the doped PANI became similar or even identical electronic structure; ultimately, the formation of a large conjugated system was obtained throughout the whole molecular chain; the positive charge was nonuniformly distributed in the entire conjugated system. The charge delocalization of the molecular chain of PANI intramolecular and intermolecular was optimized to promote the moving of charges in the molecular chain due to using a large scale and slow diffusion of the organic acid DBSA.

Simultaneously, the process of PANI hydrolysis can be promoted by the solvent effects between dodecylbenzene sulfonic group and water; the good conductivity and improved solubility of the doped PANI can be achieved.

3.2. Morphology Analysis

The membrane samples were obtained via spin-coating method using the PANI/PVA emulsion synthesized in our laboratory; the stirring speed during the process of polymerizing varied between 1000, 1600, and 2200 rpm, respectively.

Figures 2(a), 2(b), and 2(c) were the images of PANI captured by the optical microscope with a magnification of 3000x. The spherical shaped granules can be observed on the surface of the PVA polymer, with the diameter ranging from 0.5 to 1 μm. It could be seen that the low speed led to agglomeration. However, the dispersion of PANI particles could be optimized when the stirring speed increased to 2200 rpm.

fig2
Figure 2: The optical microscope images of PANI/PVA composite membranes with the stirring speed of (a) 1000 rpm; (b) 1600 rpm; and (c) 2200 rpm.

Figure 3 was the SEM image captured by S-2700 SEM; the morphology of the PANI/PVA composite membrane was observed with a very excellent uniformity; the reason behind this is that the small force of PANI chains is insufficient to provide the minimum molecular chain force of agglomeration. Therefore, the PANI/PVA composite membrane should be suitable for the preparation of the electrospun material and the electrochromic devices.

903806.fig.003
Figure 3: The SEM image of PANI/PVA composite membrane.
3.3. The FT-IR Spectrum Analysis

The presence of pristine PVA was seen as strong absorption peaks at a wavenumber of 3412 cm−1, which was attributed to the –OH stretching bend, for the C–O stretch at 1096 cm−1 which was observed in Figure 4(a). In PANI/PVA composites, the peaks of PANI at 1699 cm−1 and 1456 cm−1 were attributed to the C=N stretching vibration of quinone ring and the C=C stretching vibration associated with quinone ring and benzene ring structures, respectively. The bands at 1402 cm−1, 1165 cm−1 corresponding to the C–N stretching vibration and the C–H plane blending vibration were clearly seen. The N=Q=N class electronic absorption structure model stretching vibration absorption peak was at about 1058 cm−1 and 1112 cm−1 nearby, and the peak at 750~850 cm−1 was assigned to the C–H plane bending vibration peak in 1, 4 substituted benzene ring. The data analysis and the literature elaborated consensus [30].

fig4
Figure 4: The FTIR absorption spectrum of PVA (a) and PANI/PVA (b).

The FTIR spectra of pure PVA and PANI/PVA were compared with the membrane samples from Figure 4; the spectrum of PVA was similar to that of PVA in the PANI/PVA composites; the presence of PANI in PANI/PVA composites had a little influence on the PVA.

3.4. The Thermogravimetric Analysis

Figure 5 showed the thermogravimetric curves (TGA) of pure PVA and PANI/PVA composites at 10°C/min heating rate. From the TG-DTG curve, the thermal decomposition point presented obviously at the temperature of 260°C, but from the thermal decomposition process of PANI/PVA composites, the typical decomposition point of PVA disappeared, and because PANI/PVA composite material contains an emulsifier called PVA, unreacted reagents called DBSA, the thermal decomposition process of PANI/PVA material was not obvious, and the whole curve still showed a decreasing trend. And the PANI/PVA composites seemed to undergo four stages of degradation based on Figure 5.

fig5
Figure 5: The curve of PANI/PVA composite membrane about thermal gravimetric analysis.

The first part was the water-based weight loss stage. The evaporation of deionized water and the bonding water from the intermolecular led to the mass loss of composite materials when the temperature was up to 100°C, and the volatilization of a small amount of additives might be the part of weightlessness.

The second part was weight loss phase of PVA thermal decomposition. As the temperature continuously increased to 140–180°C, PVA dehydration etherification played an important role in weight loss; continuing to heat up, PANI also lost a small amount of weight due to PANI oxidation.

The third part was mainly the section of PANI thermal decomposition. As the temperature increased to 273°C, the increasing movement rate of polymer macromolecular chains was enhanced as the temperature increased to 273°C. Meanwhile, the molecules released gases leading to the mass loss. Through the bond energy analysis, the production of gases such as NH3 and CO2 was the main mass loss at this stage.

The fourth stage was called carbonization phase; the temperature rose to 560°C, and the TG curve decreased slowly and then reached a platform. At this stage, most of polymers were carbonized and the temperature had less impact on the mass loss of the residues. As depicted in Figure 5, the residual mass tended to a steady state.

3.5. Cyclic Voltammetry Curves for the PANI/PVA Composites

Conductive PANI membrane samples deposited on the transparent conducting ITO electrodes with the coating thickness of 20 μm were prepared by the KW-4A spin coater. At a constant rate of 200 mV/S from the initial potential of −1.5 V to the final potential of +1.5 V using the hydrochloric acid (1 Mol/L) as electrolyte, the CV curves for PANI/PVA composites, obtained under room temperature and ice-water bath separately, were carried out for electrochemical characterization of the PANI/PVA composite membranes, and the results were shown in Figure 6.

fig6
Figure 6: The CV curves of PANI/PVA composite membranes.

With applied potentials from −1.5 to +1.5 V, both devices showed electrochromic activity with color change from yellowish-green (reduction state) to green (neutral state) and sky blue (oxidation state). Comparing the CVs in Figure 6, it could be found that PANI/PVA composite membranes have unobvious redox peaks, and the area of PANI/PVA composite membrane at room temperature surrounded by the CV curve is larger than that at ice-water bath, indicating that room temperature condition has much more specific electrochemical property.

4. Result and Prospect

The PANI/PVA composite was prepared via emulsion polymerization followed by the proton acid doping. The proposed polymerization method indicated that emulsion polymerization was an effective and facile strategy for the fabrication of great amount of PANI/PVA composites. PANI particles with estimated diameter of 0.5~1 μm were shown to be evenly dispersed in PVA matrix. The typical C=N stretching vibration of the quinone ring at 1699 cm−1 and the C=C stretching vibration associated with the quinone ring and the benzene ring structures at 1456 cm−1 were the characteristic peaks of conductive PANI. The PANI/PVA composites thermal decomposition was up to 273°C. The CV curves indicated that the PANI/PVA material at room temperature has much more specific electrochemical property and was much more appropriate for electrochromic device than that at low temperature.

Further work is on the way to improve the thermal stability and measure the conductivity change of the PANI composite membranes under different potentials in order to make a more comprehensive understanding of the mechanism of the PANI composite electrochromic device.

Acknowledgment

This work was financially supported by Shanghai University of Engineering Science Graduate Student Research Innovation Project (2012yjs44).

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