# Influence of MWCNTs onβ-Phase PVDF and Triboelectric Properties

Authors: Sejung Kim; Youngjun Song; Michael J. Heller
Journal: Journal of Nanomaterials
 (2017)

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## Abstract

The surface of multiwalled carbon nanotubes (MWCNTs) was chemically modified using 1-pyrenebutyric acid (PBA) to improve its compatibility with polyvinylidene fluoride (PVDF). The carboxylic acid groups of the MWCNTs-PBA (PCNTs) provide aβ-phase nucleation site to the fluorine of PVDF along their surface. The content of the β-phase crystalline structure of PVDF was found to be the highest at a concentration of 1.0 wt.% of PCNTs, and these PVDF-PCNTs composites were utilized as active layers in triboelectric devices. The maximum output voltage achieved was 16 volts at a concentration of 1.0 wt.% of PCNTs in the PVDF composites.


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## Body

## 1. Introduction

Mechanical energy harvesting technology has been investigated in lightweight and biocompatible devices as a wireless power source by employing piezoelectric materials [1–3]. Among all of the available piezoelectric materials, polyvinylidene (PVDF) and its derivatives have been singled out in flexible nanogenerators due to their high dielectric, piezoelectric, and ferroelectric properties [4–6]. The β-phase of PVDF with the all-trans conformation of fluorine atoms leads to high values of electric polarization to the unit cell [7, 8]. Generally, the β-phase of the crystalline structure of PVDF can be enhanced by either mechanical deformation in the uniaxial or biaxial directions or application of a highly intense electric field to the PVDF film above its glass transition temperature [9–11]. As a new energy harvesting technology, contact-electrification based energy conversion devices, that is, triboelectric nanogenerators, have been developed in such a way that they can achieve high efficiency for producing large output power as well as easy fabrication [12–14]. In addition, triboelectric performance can be enhanced by regulating the surface morphology. Regarding the PVDF composites, multiwalled carbon nanotubes (MWCNTs) in PVDF composites can produce inductive charges on the surface during electrospinning, wherein the β-phase of PVDF crystallizes on the surface of the MWCNTs, resulting in the transformation of local amorphous regions into the β-phase crystalline structures [11, 15, 16].In the present work, we investigate the triboelectric performance of PVDF composites with MWCNTs, corresponding to the change in the content ofβ-phase crystalline structure. Also, the surface of the MWCNTs is chemically modified with 1-pyrenebutyric acid (PBA) (PCNTs) in order to investigate the effect of transformation of β-phase crystalline structures of PVDF and their morphological features with respect to the amount of PCNTs loaded in PVDF.


## 2. Experiments

Synthesis of Nanocomposite Particles. The MWCNTs were first dispersed inN-methyl-2-pyrrolidone (NMP) in an ultrasonication bath for 3 hrs. Then, 10 mM of 1-pyrenebutyric acid (PBA) was added to the MWCNTs (Cheap Tubes, Inc.) suspension and the mixture was magnetically stirred for 3 hrs. Once the reaction was complete, the mixture was washed with ethanol at least 5 times, and the resulting PBA-MWCNTs (PCNTs) particles were dispersed inN,N-dimethylformamide (DMF) for the next composite reaction. PVDF (Mw = 50,000 kg mol−1) powder was purchased from Sigma-Aldrich and used as received. PVDF was dissolved in DMF at a concentration of 100 mg/mL at room temperature in order to prevent crystallization during the dissolving process. Then, the chemically synthesized nanoparticle composite was added to the PVDF solution at different ratios by weight. The mixture was treated in an ultrasonication bath for 30 minutes yielding a uniformly mixed PCNTs-PVDF suspension. To obtain the PVDF based nanocomposites, the suspension was dropped onto a plain glass substrate at 200 μL/in2, and the DMF was evaporated by drying in an oven at 85°C overnight.Fabrication of Triboelectric Device and Performance Test. PVDF based nanocomposite nanogenerator devices were fabricated by constructing a sandwiched structure. The thin film of the PVDF nanocomposite is attached to a Cu tape that acts as an electrode and is protected from mechanical damage by a Kapton film. The second layer is a piece of aluminum tape on a Kapton film as well. The two substrates were connected through an acryl spacer with an adhesive on both sides, maintaining a gap (1 mm) between the substrates. In order to evaluate the performance of the device, open-circuit voltages of PVDF composite films are measured with an oscilloscope (Tektronix, TDS 2014B) under a periodical compressive force of about 30 N, vertically applied at a frequency of 3 Hz. Noise reduction of the collected voltage variations of the PVDF nanocomposites was accomplished using a band-pass filter computer program.Characterization. The morphologies of the as-prepared composites were observed by scanning electron microscopy (ESEM, Hitachi) at an acceleration voltage of 10 kV and atomic force microscopy (AFM, Veeco model). X-ray diffraction (XRD) was carried out with the 2-theta range from 10 to 60° at a scan rate of 0.02° min−1 using an XRD diffractometer (Rigaku Rotaflex) with Cu Kα radiation. In addition, the crystal structure of the PVDF composite was investigated by Raman spectroscopy (Renishaw inVia Raman microscope). The modification of MWCNTs with PBA was confirmed by a Fourier transform infrared (FT-IR) spectrometer (PerkinElmer Spectrum Two).


## 3. Results and Discussion

A schematic representation shows the process for the chemical surface modification of MWCNTs and the triboelectric device structure shown in Figure1. MWCNTs are chemically modified with 10 mM of 1-pyrenebutyric acid (PBA) inN-methyl-2-pyrrolidone (NMP) for 3 hours under gentle stirring. Subsequently, the chemically modified MWCNTs (PCNTs) are filtered under vacuum and washed with ethanol to remove the unreacted PBA followed by dispersion inN,N-dimethylformamide (DMF). The PVDF polymer solution is prepared at a concentration of 10 w/v% in DMF by ultrasonication. In order to prepare the PCNTs-PVDF composite films, the prepared PVDF solution and PCNTs solution are mixed by ultrasonication for 1 hour with varying weight ratios of PCNTs from 0 to 2 wt.%. Then, the PVDF-PCNTs solution was drop-casted (200 μL in−2) onto a plain glass substrate followed by evaporation of the solvent (DMF) in an oven at 85°C overnight under ambient conditions. These PVDF-PCNTs composite films are easily peeled off of the glass substrate without damage. Our schematic PVDF-PCNTs composites based triboelectric device is demonstrated in Figure 1(b). The first layer is composed of an aluminum tape on a Kapton film used as a substrate. The second layer is a piece of the polymer composite attached with a copper tape on a Kapton film as well. The two substrates are connected through an acryl spacer with adhesives on both sides, maintaining a gap (1 mm) between the substrates. In order to characterize the electric output, open-circuit voltages (Voc) of PVDF-PCNTs based triboelectric devices fabricated by different types of PVDF-PCNTs films were measured under a periodical compressive force of 30 N applied at a frequency of 3 Hz.Figure 1
Schematic process to fabricate the nanocomposite of PVDF-PCNTs. (a) Surface modification of MWCNTs with PBA. (b) Nanocomposite of PVDF-PCNTs (1 × 1 inch) and circuit diagram of the PVDF composite-based triboelectric device.
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(b)The morphology of the PCNTs was investigated by a scanning electron microscope (SEM) in Figure S1a (in Supplementary Material available online athttps://doi.org/10.1155/2017/2697382), which showed entangled individual features on the substrate. The morphological features of the PVDF composite films were analyzed by using SEM (Figure 2) for pure PVDF, PVDF-PCNTs, and PVDF-MWCNTs composite films. While the pure PVDF has a large grain boundary domain (~5 μm) with corrugated surface, the PVDF-PCNTs film has a smaller grain boundary, and its surface is changed into an elongated corrugated surface after introducing the PCNTs into the PVDF matrix (Figure 2(b)). In comparison, the nonmodified MWCNTs in PVDF films do not have a large effect on forming a grain boundary, but MWCNTs are aggregated in the middle of the PVDF films (Figure 2(c)). The cross-sectional SEM images of PVDF composite films also reveal how well dispersed the PCNTs (Figure 2(b)(iii)) and aggregates of MWCNTs are in the PVDF matrix (Figure 2(c)(iii)). Consequently, it is evident that the MWCNTs are uniformly dispersed in the whole PVDF matrix by increasing the affinity to the solvents and the polymer followed by preventing phase separation. In addition, roughness was investigated by atomic force microscopy (AFM) (Figure 3). The PVDF-PCNTs films were examined with the PCNTs concentrations of 0 wt.% and 1.0 wt.% to the PVDF. We denoted the PVDF composite film including 1.0 wt.% PCNTs as PVDF-10PCNT. We examined RMS values at both large and small scales and found that the roughness does not change much between the two composites. The RMS values are 567.5 and 580.3 nm at 14.6 × 14.6 μm and 1.359 and 1.818 nm at 3 × 3 μm for the pure PVDF and PVDF-10PCNT, respectively. The roughness of PVDF films was not largely changed.Figure 2
Surface characterization of PVDF-PCNTs nanocomposite films using SEM. (a) Pure PVDF, (b) PVDF-10PCNT, and (c) PVDF-MWCNTs composite films. (i) Top-view SEM images of each composite film and (ii) magnification of the rectangular region. (iii) Cross-sectional SEM images of each composite film. Scale bar is 2μm for (a)-(i), (b)-(i), and (c)-(i) and 500 nm for the rest of the images.
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(c)Figure 3
Determination of roughness of PVDF composite films by AFM analysis. (a, b) The pure PVDF surface AFM images at a scale of 14.6μm × 14.6 μm and 2 μm × 2 μm, respectively. (c, d) PVDF-10PCNT surface images at a scale of 14.6 μm × 14.6 μm and 3 μm × 3 μm, respectively.
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(d)In order to analyze the crystalline structure of PVDF-PCNTs composite films, X-ray diffraction (XRD) was carried out at the speed of 1°/min and the range from 10° to 60° (Figure4(a)). This describes the XRD results for PVDF-PCNTs composite films corresponding to the loaded amount of PCNTs. In order to demonstrate the transition of PVDF crystalline structures, the pure PVDF and PVDF-MWCNTs composite films are also analyzed; it can be found that three distinctive peaks are observed at three different diffraction angles (2θ): 18.4°, 19.9°, and 26.5° corresponding to (020), (110), and (021) crystal plane from the α-phase crystalline structure [8]. When it comes to the PVDF-PCNTs composite films, the peak at 2θ = 20.8° is observed corresponding to (110) of the β-phase crystalline structure, which indicates that the crystalline phase transition occurred from the α-phase to the β-phase. According to the amount of PCNTs in the PVDF films, the nanocomposite with 1.0 wt.% PCNTs loading can be observed to possess the highest relative peak intensity at 20.8 when the β-phase is increased. This indicates that the addition of PCNTs can induce phase transition from the α-phase crystalline structure to the β-phase crystalline structure in the PVDF-PCNTs nanocomposite films. In addition, the PVDF-PCNTs nanocomposite film with PCNT 1.0 wt.% loading can also be confirmed to possess the highest relative peak intensity at = 20.6° and β-phase crystalline structure decreased upon a further increase of the PCNTs concentration to 2 wt.%.Figure 4
Spectroscopic analysis for the transition of crystalline structure of PVDF composite films. (a) XRD patterns and (b) FT-IR spectra of the pure PVDF and PVDF-PCNTs nanocomposite films corresponding to the amount of PCNTs from 0 to 2 wt.%.
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(b)For the further investigation of crystalline transition of PVDF-PCNTs nanocomposite films, FT-IR was carried out in the region between 1500 and 550 cm−1 with a spectral resolution of 1 cm−1. For each spectrum, 10 scans were averaged. Figure 4(b) shows FT-IR spectra for nanocomposite films of the pure PVDF and PVDF with different PCNTs concentrations. As demonstrated in the XRD results, it was found that the PVDF-PCNTs nanocomposite films consisted of the α-phase and the β-phase PVDF. The absorbance bands at 613 cm−1 (CF2 bending), 763 cm−1 (CF2 wagging vibration), and 975 cm−1 (CF2 rocking vibration) were related to the α-phase [8]. However, the absorbance bands at 838 cm−1 (CH2 rocking), 875 cm−1 (CF2 stretching), 1173 cm−1 (CH2 wagging), and 1231 cm−1 (CH2 rocking) were observed, which were related to the β-phase PVDF [11]. From Figure 4(b), it was found that the α-phase crystalline structure certainly exists in the PVDF-PCNTs nanocomposite films with various PCNT loadings by inducing the nucleation of the β-phase. We believe that the crystalline phase transition from α- to β-phase is due to the fact that the carboxylic acid groups enhance the compatibility of the PCNTs with CF2 groups in the PVDF due to strong interaction that can induce the crystallization of β-phase PVDF along the surface-mediated MWCNTs [15, 17, 18]. Nonetheless, the absorbance bands from the β-phase increase significantly at four different bands, while the peaks corresponding to the α-phase crystal decrease. Therefore, the FT-IR spectra results indicate that α-phase crystal peaks were transformed to β-phase crystal peaks by introducing the nucleation site from PCNTs, which is consistent with the results of XRD analysis.Figure5(a) shows the open-circuit voltage output of the five different PVDF-PCNTs types: pure PVDF and PVDF-PCNTs with four different loading amounts of PCNTs. While the mechanical deformation is applied at 3 Hz, the response time is 1.17 and 0.93 sec for the pure PVDF and PVDF-10PCNT composite films, respectively (Figure S2). The results clearly show that the order of the output performance of each of the PVDF-PCNTs compositions is PVDF < PVDF-20PCNTs < PVDF-01PCNTs < PVDF-05PCNTs < PVDF-10PCNT. The maximum output voltage is up to 16 volts, which is almost 8 times as high as the pure PVDF based triboelectric devices. Therefore, we assumed that the increased β-phase content is attributed to the enhancement of the triboelectric effect due to its polarizability of the crystalline structure of PVDF.Figure 5
(a) Triboelectric device ofVoc with different loading PCNTs from 0 to 2 wt.%. (b, c) The mechanism of the band energy alignment for electron transport in the triboelectric device during mechanical deformation.
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(c)As a result of the periodic mechanical deformation between the PVDF-PCNTs films and the electrode, electrostatic charges are oppositely generated and distributed on each surface of the insulating polymeric materials. The produced charges will not be conducted away or neutralized due to the insulating nature of polymer films, resulting in the accumulation of charges on the surface of composite films. Then, the charges will be conducted across the external load between the two electrodes to minimize the energy created by the triboelectric potential. Simultaneously, mechanical compression between the two layers of polymers leads to a reduction of the interplanar distance. According to the literature, we need to consider the relationship between the surface morphology and the triboelectric effect in order to enhance the triboelectric device performance because the surface triboelectric charges are the direct driving force for transport of induced electrons between electrodes in a triboelectric device [12–14, 19]. Firstly, the change in the capacitance is largely improved during the mechanical deformation due to the presence of the air void (low dielectric constant, ~1). Secondly, the triboelectric effect with a structured surface is largely enhanced due to the increased interface with the air corresponding to the unstructured surface followed by generating more surface charges during the friction. Lastly, the triboelectric charges are more easily separated due to their fast charge saturation on the structured surface. However, in our device using PVDF-PCNTs nanocomposite films, the roughness is not largely changed compared to the pure PVDF films.Lastly, we now consider the charge transfer between the PVDF-PCNTs nanocomposite dielectric layers and electrodes. In our device, the unequal effective work function of two electrodes was adopted such as Al and Cu. Generally, the electrons will flow from the lower work function of materials into the higher work function of materials. As illustrated in Figures5(b) and 5(c), we adopted the two different work function electrodes, aluminum (4.2 eV) and copper (4.7 eV). Moreover, PVDF has an energy level with an effective work function of around 5.0 eV. When it comes to the charge transfer, electrons flow from the Fermi level of aluminum to the PVDF due to its lower work function during the friction followed by making the PVDF surface negatively charged. Then, the electric field is developed, followed by the decrease of the potential difference between aluminum and PVDF, and the charge transfer will stop until the saturation of electrons. The center of the positive charges does not coincide in every molecule of PVDF in its polar β-phase, but the bond charge is zero when β forms naturally because of the random arrangement of dipoles. As a result, an enhanced charge density of triboelectric effect can be expected. The surface charge density thus determines the amount of induced electrons that flow to screen electric field from the triboelectric charges.


## 4. Conclusion

In conclusion, we have demonstrated the relationship between the dielectric nanocomposites and the triboelectric effect by adopting the PVDF based nanocomposites composed of PVDF-PCNTs to open a novel and simple approach. The PVDF-PCNTs films play an important role and benefit the performance aspect and should be considered with charge generation, charge separation, and charge transport in the device. PVDF-PCNTs are a soft material and could easily be fabricated into a patterned morphology by simple solvent evaporation. The increase inβ-phase of PVDF-PCNTs nanocomposite films was seen in terms of the addition of nucleation sites without phase separation in the PVDF matrix. Lastly, the different energy level of materials is helpful for charge separation/transfer in the device.



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