Polypyrrole (PPY) powder was chemically synthesized using ferric chloride (FeCl3) and characterized by X-ray diffraction (XRD), Le Bail Method, Fourier Transform Infrared Spectrometry (FTIR), and Scanning Electron Microscopy (SEM). XRD pattern showed a broad scattering of a semicrystalline structure composed of main broad peaks centered at 2 = 11.4°, 22.1°, and 43.3°. Crystallinity percentage was estimated by the ratio between the sums of the peak areas to the area of amorphous broad halo due to the amorphous phase and showed that PPY has around 20 (1)%. FTIR analysis allowed assigning characteristic absorption bands in the structure of PPY. SEM showed micrometric particles of varying sizes with morphologies similar to cauliflower. Crystal data (monoclinic, space group P 21/c, (2) Å, (2) Å, (2) Å,  Å, (2) Å and  Å) were obtained using the FullProf package program under the conditions of the method proposed by Le Bail. Molecular relaxation was performed using the density functional theory (DFT) and suggests that tetramer polymer chains are arranged along the “” direction. Average crystallite size was found in the range of 20 (1) Å. A value of 9.33 × 10−9 S/cm was found for PPY conductivity.

1. Introduction

Intrinsically Conductive Polymers (ICPs) with conjugated double bonds have attracted attention in fundamental and applied researches, emerging with great deal of technological applications [15]. Polypyrrole, polythiophene, polyaniline, and polyacetylene have been intensively studied due to their good environmental stability and high electrical conductivity, making them more desirable than metals in many cases [6, 7].

Among ICPs, polypyrrole (PPY) is especially promising in commercial applications [8]. Polypyrrole has been applied as electrochromic and electronic devices, membrane separation, light-weight batteries, sensors, rechargeable batteries, microwave shielding, supercapacitors, drug delivery, corrosion protection, and artificial muscle [1, 915]. However, the inherently poor solubility in common solvents, which originates from the strong inter- and intrachain interactions, has limited some PPY’s practical applications [1619]. Figure 1 shows the PPY molecular structure.

Many studies have been made to characterize PPY, but few focus on structural characterization through structural refinement methods. Understanding the structure and morphology of semicrystalline materials is essential to the development of new technological applications. X-ray diffraction (XRD) pattern was used to obtain structural information using the Le Bail whole powder pattern decomposition method applied to a semicrystalline PPY for determination of cell parameters and crystallite size and shape. Fourier Transform Infrared Spectroscopy (FTIR) was used for structural information of the bonds; Scanning Electron Microscopy (SEM) was carried out for the investigation of the polymer morphology. Then, these results were correlated with the obtained electrical conductivity.

2. Experimental

2.1. Polymer Synthesis

Pyrrole (Sigma-Aldrich) was distilled before use. All other reagents were used as received. All reactions were conducted at room temperature. Chemically polymerized polypyrrole was obtained by oxidative polymerization using FeCl3 as oxidant in aqueous medium based on the literature [20], with some modifications. Pyrrole (1.0 M) solution was added drop by drop to the oxidizing agent aqueous solution in the ratio of 1 : 3. Then, the polymerization was conducted for 3 hours under constant stirring using 300 rpm. This preparation was filtered under vacuum and washed with distilled water and methanol.

2.2. Fourier Transform Infrared Spectroscopy (FTIR)

FTIR spectra were measured in a spectrophotometer Bomem-MB Series, Hartmann & Braun, in the range of 400–2000 cm−1 and 16 scans. Pellets were prepared with KBr in mass ratio of 1 : 100.

2.3. XRD Measurements and Crystallinity Estimative

XRD data were obtained at the laboratory of X-ray crystallography of IFSC/USP, São Carlos, SP, Brazil, using a Rigaku Rotaflex diffractometer equipped with graphite monochromator and rotating anode tube, operating with Cu , 50 kV, and 100 mA. Powder diffraction patterns were obtained in step scanning mode, = 5–70°, step of 0.02° and 3 s/step, where is the Bragg angle. Routine software was used for the peak deconvolution of the semicrystalline pattern and determination of area due to the noncrystalline phase. Crystallinity percentage was estimated by the ratio between the sums of the peak areas to the area of noncrystalline broad halo due to the noncrystalline phase.

2.4. Le Bail Method

Le Bail Method was performed using the software package FullProf [21]. All parameters were refined by the least-squares method [22]. The pseudo-Voigt function modified by Thompson-Cox-Hastings was used as peak profile function [23]. Instrumental resolution function parameters were obtained from a lanthanum hexaborate standard, LaB6. The PPY structural parameters obtained by Warren and Madden [11] were used as initial parameters for the Le Bail Method (monoclinic, Å, Å, Å, , , and ). Spherical harmonics parametrization (SHP) [24] was used to account for the possible crystallite anisotropy; particle size was determined from the information on line profile (peak width and shape) [25, 26].

2.5. Geometry Optimization

Molecular relaxation was performed using the density functional theory (DFT) as implemented in Quantum Espresso package [27], with the generalized gradient approximation (GGA) of Perdew-Burke-Ernzerhof (PBE) for the exchange-correlation energy [28] and the BFGS quasi-Newton algorithm for the geometry optimization. The energy cutoff for the wave functions and for the charge density was taken as 0.816 keV and 3.264 keV, respectively. The optimization process was evaluated until the forces on each atom become less than 10−4 eV/Å. The molecular plots were made with the XCrySDen package [29].

2.6. SEM Analysis

SEM experiments were performed using a Supra 35, Carl Zeiss, 3.0 kV. Powder samples were deposited on a carbon tape and the surface morphology was obtained at room temperature.

2.7. DC Electrical Conductivity Measurements

Electrical connections were made in PPY pellet which was coated with silver ink. Measurements were performed at room temperature (300 K) using a Keithley Model 2612A from 500 mV to 10 V.

3. Results and Discussion

3.1. FTIR Analysis

Figure 2 shows the FTIR spectra of pure PPY obtained from 2000 to 500 cm−1, the most useful range for chemical characterization of organic materials [30, 31]. Bands located at 773 cm−1 and 913 cm−1 were attributed to C–H stretching. A band at 1026 cm−1 may be assigned to =C–H in plane deformation vibration. A band at 1152 cm−1 was attributed to C–H in and out of plane deformations. Bands at 1458 cm−1 and 1542 cm−1 were assigned to vibration of pyrrole ring (C–N) and ring stretching mode (C=C, C–C), respectively. Bands located at 1206 cm−1 and 1293 cm−1 were assigned, respectively, to N–C stretching band and =C–H in plane vibration. Bands observed in the present study are consistent with those available in the scientific literature and confirmed the polymerization of pyrrole [3237].

3.2. X-Ray Diffraction and Crystallinity Estimative

Structural aspects in polymers continue to be an interesting researched topic [38, 39]. Understanding the regular arrangement of polymeric materials is essential for the evaluation of the material properties and the proposition of new technological applications.

A typical X-ray diffraction pattern of PPY prepared using FeCl3 is presented in Figure 3 showing the position in of all possible Bragg reflections. Broad peaks were observed indicating some structural ordering of nanometric dimensions, typical of nanostructured polymers with low degree of crystallinity (fringed micelles model). XRD pattern showed that four broad peaks (better observed in Figure 4) related to the scattering from PPY chains at the interplanar spacing are centered at ~; 22.7°; 29.8°; and 44.3° [40]. The large amount of disorder inherent in the PPY matrix means the X-ray peaks are broad Gaussians and the higher order peaks are severely damped [11].

To estimate the crystallinity percentage of semicrystalline polymers, it is assumed that the polymer consists of a well-defined mixture of noncrystalline and crystalline regions [41, 42]. Many methods have been applied for the estimation of crystallinity percentage in semicrystalline materials, and it has become increasingly apparent that these methods do not always give the same result. However, all current methods assume implicitly a two-phase model of crystallites embedded in a noncrystalline matrix.

The most used method to access the crystalline portion of a given material using XRD date is the deconvolution method [43]. For the curve fitting, assumptions such as the shape and number of peaks and an appropriate function have to be made. An important hypothesis for this analysis is that increased noncrystalline contribution is the main contributor to peak broadening. However, in addition to crystalline disorder (noncrystalline content), there are other intrinsic factors that influence peak broadening, such as crystallite size and nonuniform crystal strain.

Deconvolution of the XRD peaks is showed in Figure 4. The green curve, below the experimental black curve, corresponds to a Chebyshev polynomial [44] of sixth order, arranged through the minimum of the narrower peaks. The noncrystalline broad halo component (from 50° to 70° degrees in ) contributes to the XRD pattern with a broad halo generating diffuse scattering, which is often confused with the background. This broad halo shows a short-range structure, such as distance distributions between nearest neighbors. The resulting curve indicates a noncrystalline phase with a maximum at . Applying the Ehrenfest formula [45], , the interatomic distances can be estimated, where λ is the wavelength of X-rays and is the half angle of diffraction. Thus, a wide distribution of distances with maximum at 6.9 Å was noted. This is in agreement with the distances between nitrogen atoms of parallel chains, which correspond to 6.2 Å [46].

Assuming the amorphous contribution, the Chebyshev polynomial is subtracted from the total pattern allowing the crystalline peaks obtainment, as shown in Figure 4. Comparing the experimental area with the area of the polynomial curve, the estimate of crystallinity percentage of PPY corresponds to 20%. The four observed peaks were best fitted using Gaussian curves, revealing symmetrical features of the pattern, which is typical of isotropic structures.

3.3. Le Bail Method Analysis

The use of Le Bail Method [47, 48] to obtain structural information from semicrystalline patterns is not very common due to the large overlapped peaks on diffractograms. Nevertheless, it has been used to characterize some conducting polymers as polyaniline and substituted polyanilines [4951]. This process uses iteratively the Rietveld decomposition formula for whole powder pattern decomposition (WPPD) in the FullProf program package [52]. A fair approximation to the observed integrated intensity can be made by separating the peaks according to the calculated values of the integrated intensities as follows:where is a measure of the contribution of the Bragg peak at position to the diffraction profile at position . The sum is overall , which can theoretically contribute to the integrated intensity . So there is a bias introduced here by the apportioning according to the calculated intensities; this is why the observed intensities are in fact said to be “observed” under quotes, in the Rietveld method. These “observed” intensities are used in the and calculations [47].

The Le Bail Method allows only refining the unit cell parameters and what would be the effectively measured intensities are only the intensities suggested by the profile fitting based on a distribution of intensities using a profile function [23] for each overlapped reflection constituting the few very broad peaks. These are due to the low crystallinity and small crystallite size.

This refining method has recently been utilized to obtain structural information of semicrystalline materials, even taking into account the large overlapped peaks on XRD patterns. Structural refinement of PPY through Le Bail Method started using as initial parameters those reported by Warren and Madden [11]. XRD patterns showed a good fit using a monoclinic unit cell model, P21/c, with lattices , , and equal to 7.1499 (2) Å, 13.9470 (2) Å, and 17.3316 (2) Å, respectively, and the angle equal to 61.5640 (2)°. The observed () and calculated () diffractograms and the residual line () as well as indexes for the main reflections are showed in Figure 5. Table 1 shows the refined parameters for PPY.

Anisotropic size broadening can be written as a linear combination of spherical harmonics and it is supposed that anisotropic size contributes only to the Lorentzian component of the total Voigt function. The explicit formula of the intrinsic integral breadth using the SPH treatment of size broadening is given by [26] where is the size contribution to the integral breadth of reflection (), are real spherical harmonics (arguments and are the polar angles of the vector with respect to a Cartesian crystallographic frame) [53], and are refinable coefficients, depending on the Laue class. After refinement of the coefficients , the program calculates the apparent size (, in Å) along each reciprocal lattice vector if the parameters are fetched to the program from an external instrumental resolution function file.

It was possible to visualize the crystallites in directions , , and using the GFourier Program [54]. It is important to stress that these crystallite shapes do not refer to the actual shape but to the features of a rather rough and approximated model. Those shapes are related to the symmetry properties of the distribution of columns of scattering centers in crystalline domains of the given phase. PPY showed an average crystallite size of 20 (1) Å with a standard deviation (anisotropy) of 3 Å. It is important to stress that the standard deviation appearing in the global average apparent size is calculated using the reciprocal lattice directions so it is a measure of the degree of anisotropy, not of the estimated error. There is a smaller apparent size of 15 Å in the direction and almost equivalent along and , respectively, 21 and 18 Å. The refined average crystallite size 2D and 3D projections for PPY are showed in Figures 6(a) and 6(b). Crystallite shape is quite similar with the particle morphology of PPY, which can be described as a cauliflower-like shape morphology, as will be evidenced by SEM [5557].

3.4. Geometry Optimization

In Figure 7 we present the molecular structure obtained after geometry optimization, where the monomers lie in different plans. Note that this figure is a model for PPY tetramer unit cell using the refined cell parameters obtained previously by the Le Bail Method. The chloride ions (counter ions) on the structure voids of PPY tetramer were not introduced in this model. This model suggests that polymer chains are arranged along the “” direction. For the same monomer, the interatomic distances between two C atoms or between a C atom and a N atom are slightly different: 1.37 Å for N–C bond, 1.39 Å for C–C bond adjacent to the N–C bond, and 1.41 Å for C–C bond opposite to the N atom. The H–N and H–C bond lengths are 1.01 Å and 1.08 Å, respectively. The bond length of two carbon atoms of adjacent monomers is around 1.44 Å.

3.5. SEM Analysis

SEM technique was used in order to identify the PPY morphology at room temperature. The morphological features of chemically synthesized PPY have revealed that mostly the polymeric growth is similar to the crystallite shapes. SEM images of PPY are shown in Figures 8(a) and 8(b). All images showed a cauliflower-like morphology constituted by microspherical grains [57]. It has been reported that this morphology is related to the dopant intercalation difficulty in the disordered polymeric chain [56, 57].

3.6. DC Electrical Conductivity Measurements

In the case of conducting polymers, the total conductivity is a function of interchain and intrachain mobility of the counter ion. The interchain mobility depends on the degree of crystallinity, temperature, and protonation (doping) level. In addition, the counter ions are capable of introducing defects by causing significant charge polarization in neighboring chains [58].

The relationship between applied voltage and current is given by , where , the factor of proportionality, is the nanocomposite electrical resistance (). To verify the DC electrical conductivity of nanocomposite, the dimensions of pellet sample were considered, represented by , where is the pellet thickness, is the area of the straight section, and is the electrical resistivity. For a plot of , the angular coefficient provides the inverse of resistivity, that is, electrical conductivity [58]:

The DC electrical conductivity, , for pure PPY shows different values in the literature, closely related to their methods of synthesis. The DC electrical conductivity of PPY at room temperature was found to be 9.33 × 10−9 S/cm. This value is of the same order of magnitude of the camphor sulfonic acid (CSA) doped PPY films obtained by Navale et al. (2014) [1].

4. Conclusion

We successfully synthesized PPY by chemical polymerization using iron (III) chloride as oxidant agent. Through FTIR technique, it was possible to identify characteristic absorption bands related to chemical bonds and functional groups present in PPY structure, which allowed its structural and organic chemical characterization. XRD technique showed a semicrystalline pattern with crystallinity around 20%. PPY unit cell parameters were obtained through Le Bail Method. Microstructure analysis showed an average crystallite size around 20 Å. Molecular relaxation using the density functional theory (DFT) suggested that the tetrameric chain is lying along “” axis in unit cell. SEM analysis suggested a cauliflower-like morphology. DC electrical conductivity obtained at room temperature was found in the magnitude of 10−9 S/cm.

Conflict of Interests

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


The authors are grateful to the Brazilian Agency FAPEAM (Fundação de Amparo à Pesquisa do Estado do Amazonas) for the financial support for this publication based on the Edital Papac 020/2013.