Open access peer-reviewed chapter

Effect of Barium Titanate Reinforcement on Tensile Strength and Dielectric Response of Electrospun Polyvinylidene Fluoride Fibers

By Avinash Baji and Yiu-Wing Mai

Submitted: August 3rd 2017Reviewed: January 30th 2018Published: March 12th 2018

DOI: 10.5772/intechopen.74662

Downloaded: 363


In this study, we used electrospinning to obtain polyvinylidene fluoride (PVDF) fibers reinforced with barium titanate (BaTiO3) and investigated the influence of BaTiO3 concentration on the tensile strength and dielectric behavior of PVDF fibers. X-ray diffraction (XRD) study and infrared spectroscopy revealed that PVDF fibers filled with BaTiO3 possessed higher fraction of ferroelectric β-crystals compared to neat PVDF fibers. Further, incorporation of 40 wt% BaTiO3 within the fibers increased their stiffness and strength by 95 and 38%, respectively. These improvements in tensile properties of BaTiO3 filled PVDF fibers arose from the reinforcement effect of BaTiO3. Also, the dielectric response of the BaTiO3/PVDF fibers was characterized. The effective dielectric constants of PVDF fibers reinforced with BaTiO3 were found to increase consistently with BaTiO3 content at all frequencies. The dielectric loss of the fibers did not show any significant change for all concentrations of BaTiO3 within the fibers.


  • electrospinning
  • nanofibers
  • polyvinylidene difluoride (PVDF)
  • barium titanate (BaTiO3)
  • dielectric properties

1. Introduction

There has been substantial recent interest in the development of nanostructured piezo-sensitive composites as they can potentially display combination of desirable physical properties which cannot be obtained in single phase materials [1, 2, 3]. Hence, ceramics such as zinc oxide, bismuth ferrite, lead zirconate titanate, barium titanate (BaTiO3) etc. are widely utilized in actuators, sensors and energy storage devices due to their good piezoelectric and ferroelectric properties [4, 5, 6]. However, their inherit brittleness has limited their use for most engineering applications. By contrast, compliant polymeric materials such as polyvinylidene fluoride (PVDF) and its copolymers are easy to process but generally have low piezoelectric coefficient values when compared to ferroelectric ceramics [7, 8]. Thus, the incorporation of a ceramic phase into an electroactive polymeric matrix could yield composites with improved mechanical integrity and piezoelectric characteristics [1, 2].

Traditionally, such composites are fabricated by dispersing micron or submicron sized ferroelectric ceramics into a dielectric polymer matrix. However, this approach yields composite with film thickness greater than the size of the ceramic particles. Consequently, the composites are invariably found to possess low capacitance densities. Some recent studies demonstrate that reducing the size of the filler particles to nanometer length scales leads to an improvement in the dielectric permittivity of the composite [3, 9]. This is attributed to an increase in the interfacial area which promotes the exchange couple effect, and improves the polarization levels of the composite and its dielectric response [3, 9]. Further, these studies demonstrate that electromechanical coupling and permittivity of the composite can increase by 60 times when large aspect ratio fillers are used and when they are aligned along the poling direction within the matrix phase [10, 11]. Hence, composites reinforced with nanorods or nanowhiskers can display better dielectric permittivity and mechanical strength compared to composites obtained by simply dispersing ceramic powders within a polymer matrix [12, 13, 14, 15].

It is well-known that these piezo-sensitive composites are often subjected to external stimuli such as mechanical stresses, electrical field or coupled electromechanical loads [16]. The induced electric field activates the mechanical stresses and the induced mechanical load generates the electrical field within the piezoelectric material [16]. Since the electric field and mechanical stresses interfere with each other, it is therefore of the utmost importance that the composites have good combined mechanical and piezoelectric responses. In our recent study, we fabricated BaTiO3 reinforced PVDF fibers using electrospinning and characterized their piezoresponse [2]. We showed that these PVDF/ BaTiO3 fibers have tremendous potential for future nanoscale electronic devices. Similarly, other researchers working on PVDF/BaTiO3 composites focused their efforts to characterize the dielectric, piezoelectric and ferroelectric behaviors of the composites [7, 14, 15, 17].

In this work, the tensile deformation behavior of PVDF/BaTiO3 fibers obtained using electrospinning is characterized. Their deformation mechanisms are discussed based on their microstructural evolution, such as crystalline structure development induced by the presence of BaTiO3 within the fibers. Finally, results on dielectric permittivity of these nanofibers are presented.

2. Experimental work

2.1. BaTiO3 fibers

We used sol-gel based electrospinning to prepare barium titanate fibers. Briefly, 5.1 g of barium acetate was dissolved in 12 ml of glacial acetic acid; and to this solution, 5.9 ml of titanium isopropoxide was added to obtain BaTiO3 precursor solution [18]. The solution for electrospinning was prepared by dissolving 2.5 g poly(vinyl pyrrolidone) (PVP, MW = 360,000) in 11 ml of solvent solution which was prepared by mixing equal parts of dimethyl formamide (DMF) and ethanol together. Then, BaTiO3 precursor solution was added to the PVP solution.

Electrospinning was conducted using the BaTiO3/PVP solution at 20 kV with 0.07 mm/min as the solution feed rate. The spacing between needle and grounded metal collector was 15 cm. A vacuum oven at 100°C was used for 1 h to dry the fibers. After which the fibers were put in a furnace and annealed at 750°C for 1 h. The resultant fibers, referred to as Sample 1, were BaTiO3 fibers.

2.2. BaTiO3 reinforced PVDF fibers

PVDF fibers filled with 0, 10, 20 and 40 wt% of BaTiO3 were obtained as described in the following steps. In the first step, Sample 1 fibers of known content were dispersed into DMF solution. The solution was sonicated for 0.5 h and then stirred for 1 h to obtain a slurry solution. 18 wt% of PVDF powder was added to the slurry solution for electrospinning.

Electrospinning was conducted at 18 kV on this solution with a feed rate fixed at 0.12 mm/min. PVDF fibers filled with 0, 10, 20 and 40 wt% of BaTiO3 were obtained. This set of BaTiO3-PVDF fiber samples are referred to as Sample 2.

2.3. Microstructure characterization

A scanning electron microscope (FESEM, Zeiss ULTRA plus) was used to observe the microstructure of Sample 1 and Sample 2 fibers. The surface of the samples were gold-coated with a sputter coater before they were examined using SEM. An accelerating voltage of 2–3 kV was used for imaging the samples. Transmission electron microscopy (TEM, Philips CM120 Biofilter) was also used to image Sample 1 and Sample 2 fibers. Sample 2 fibers were electrospun directly on a 400-mesh copper grid and then examined using the TEM.

2.4. X-ray analysis and infrared spectroscopy

The diffraction behavior of Sample 1 and Sample 2 fibers were studied using an X-ray diffractometer (XRD Shimadzu S6000) with Cu Kα radiation (λ = 1.54 Å). The 2θ scan was varied between 15 and 70° and the scan speed was set at 1°/min with 0.02° step size. Bruker Fourier transform infrared spectroscopy system (FTIR, IFS 66v) was used to collect the spectra of Sample 2 fibers. The fibers were scanned from 5000 to 400 cm−1 in attenuated total reflectance mode (ATR).

2.5. Mechanical properties

The mechanical integrity of the fibers was analyzed using tensile tests on the aligned fiber samples conducted on an Instron 5567 (2.5 N load cell) testing machine with a cross-head speed of 5 mm/min. The loading direction was parallel to the fiber axis.

Dynamic mechanical measurements on Sample 2 fibers were obtained by a dynamic mechanical analyzer (DMA, TA Instruments). An oscillation amplitude of 10 μm, 3°C/min heating ramp rate and 1 Hz frequency were used.

2.6. Dielectric properties

The frequency-dependent capacitance and loss tangent of Sample 2 fibers as a function of BaTiO3 content were measured using a frequency-response dielectric analyzer (Novocontrol alpha analyzer) with scanning frequencies ranging from 103 to 107 Hz.

3. Results and discussion

Uniform distribution of the ferroelectric ceramic phase within the piezoelectric PVDF matrix is an important prerequisite to obtain electroactive composites with improved physical and mechanical properties, e.g., ferroelectricity, tensile strength, and stiffness [1, 11, 14]. Here, we use electrospinning to obtain PVDF fibers with uniformly dispersed and distributed BaTiO3. The effects of BaTiO3 loading on the structure development and tensile strength of the fibers are evaluated.

The microstructure and size of Samples 1 and 2 are examined using SEM and TEM. Figure 1A and B show typical SEM and TEM images of Sample 1 BaTiO3 fiber indicating an average fiber diameter of ~170 ± 50 nm. SEM image (Figure 1A) reveals that the fibers are composed of fine-grained structures which are assembled and organized to obtain a fibrous geometry. These grains are dense and closely packed as evident in the TEM image (Figure 1B). Figure 2A and B show representative SEM and TEM microstructures of PVDF fibers filled with 20 wt% BaTiO3. An average fiber diameter of Sample 2 (Figure 2A) is ~210 ± 40 nm. SEM image shows that the surface morphology of BaTiO3/PVDF fibers appears rough.

Figure 1.

(A) SEM and (B) TEM images of BaTiO3 fiber (Sample 1). The microstructure shows that BaTiO3 grains are self-assembled and self-organized to yield a fibrous geometry.

Figure 2.

(A) SEM image of PVDF reinforced BaTiO3 fibers (Sample 2). The inset in the figure shows the microstructure of uniaxially aligned fiber arrays. Aligned PVDF fibers as a function of BaTiO3 content were collected for characterizing their tensile properties. (B) TEM images of typical PVDF fibers reinforced with 20 wt% BaTiO3. It is evident that the BaTiO3 fiber is embedded within the PVDF matrix and aligned along its fiber axis. The inset in the figure shows a higher magnification image taken of another fiber area.

Arrows in Figure 2A clearly point to slight bulges in the fiber which are owing to the inclusions of BaTiO3 within the PVDF fibers. The inset in Figure 2A shows an array of uniaxial aligned and tightly packed fibers which can be easily collected to form a test coupon for tensile experiments. The dispersion quality of BaTiO3 in PVDF can be conveniently examined from the TEM image (Figure 2B). Consistent with the SEM images, bulges in the fiber are also noticed (see Figure 2B). A magnified TEM image taken from another area of the fiber is given in the inset of Figure 2B, which confirms the alignment of BaTiO3 along the fiber axis.

The crystalline phase change in PVDF due to the presence of BaTiO3 is determined using XRD and FTIR. Figure 3A shows the XRD patterns of PVDF fibers filled with 0, 10, 20 and 40 wt% BaTiO3. For reference, the XRD pattern of neat BaTiO3 (Sample 1), that has a cubic-tetragonal structure which is responsible for its ferroelectric and dielectric properties [19, 20], is shown in Figure 3B revealing the strong peaks. The XRD peaks of Sample 1 fibers displayed in Figure 3A match closely the cubic-tetragonal structure of BaTiO3 (JCPDS 31-0174 & JCPDS 05-0626) [2, 19, 20, 21]. Sample with 0 wt% BaTiO3 shows 5 peaks corresponding to PVDF crystal structures at 18.3, 20.2, 35.5, 41.1 and 56.1° [7, 22, 23, 24]. The peaks at 18.3° and 35.6° (Figure 3A) are attributed to the α-crystalline structure of PVDF. The peaks at 20.2, 41.1 and 56.1° are due to the ferroelectric β-crystalline phase of PVDF [2, 7]. Evidently, the main peak for neat PVDF is recorded at 20.2°, which is indexed to the 200/110 reflections of the β-crystalline structure. Nonetheless, XRD peaks corresponding to both PVDF and BaTiO3 crystalline phases are clearly shown for the fibers reinforced with 10, 20 and 40 wt% BaTiO3. The intensity of the peak at 20.2° is moderately increased with BaTiO3 content. Furthermore, the intensities of the peaks related to BaTiO3 are seen to increase and become more prominent with increasing filler content in the composite fibers.

Figure 3.

(A) XRD patterns of PVDF fibers as a function of BaTiO3 content. All peaks corresponding to the crystalline phases of PVDF and BaTiO3 are evident in the fibers reinforced with BaTiO3. (B) XRD pattern of neat BaTiO3 to identify the cubic and tetragonal structure of BaTiO3.

The crystalline structure confirmation for the fibers reinforced with BaTiO3 was done aided by the FTIR spectra recorded for the fibers. Figure 4A shows the IR spectra of Sample 2 fibers. All the samples show peaks at 766, 840, 1280, 1400 and 1432 cm−1. The bands corresponding to 766, 1400 and 1432 cm−1 in the spectra are indexed to the α-crystals of the PVDF matrix, while the bands at 840 and 1280 cm−1 in the spectra are indexed to the β-crystals of PVDF [2, 7, 2324]. These results indicate that the fiber samples irrespective of the BaTiO3 content contain both α and βcrystals in PVDF matrix. However, the content of α- and β-crystalline structures inside the PVDF fibers due to the BaTiO3 inclusion is estimated using the Beer–Lambert law. Thus, according to Beer-Lambert law, α- and β-crystalline content can be estimated by using the absorbencies for α- and β-crystals at 766 and 840 cm−1, respectively. The fraction of β-phase is calculated from [25, 26]:


where and are the corresponding absorbency at 766 and 840 cm−1. Figure 4B shows the fraction of β-crystals estimated within the PVDF matrix for Sample 2 fibers. The β-crystals content within the sample fibers increases from 81% estimated for neat fibers to 87% for fibers reinforced with 40 wt% BaTiO3. This shows that the inclusion of BaTiO3 improves the ferroelectric crystal phase formation within the PVDF fibers.

Figure 4.

(A) IR spectra of fibers as a function of BaTiO3 content. α- and β-related bands of PVDF are indexed in the spectra. (B) Fraction of β-phase as a function of BaTiO3 content. The β-phase fractions are determined using Eq. (1).

The FTIR data corroborates the XRD results. The improvement in the fraction of β-crystals within PVDF can be attributed to the changes in crystalline structure development due to the inclusion of BaTiO3. It proves that the BaTiO3 content in PVDF fibers plays an important role in influencing the crystallization of PVDF and also promotes phase change within the PVDF. These results on crystallization induced by BaTiO3 content are in agreement with the results reported by Dang et al. [17]. They show that BaTiO3 can be easily absorbed on surfaces of PVDF due to the presence of interstitial hydrogen ion BaTiO3 lattice. This also helps in the dispersion of BaTiO3 in polar DMF solvent. The homogeneous dispersion and absorption of BaTiO3 on the surface of PVDF plays an important role to induce crystal structure changes [17].

We will now characterize the deformation behavior of these PVDF fibers filled with BaTiO3 and also illustrate the mechanisms behind the improved mechanical integrity of the composite fibers. Figure 5A shows typical stress–strain curves for BaTiO3/PVDF fibers. The break strain decreases with increasing BaTiO3 content within the fiber. Figure 5B shows the tensile modulus and tensile strength of the composite fibers. In general, as the BaTiO3 content increases, the composite fibers become stiffer and stronger. The stiffness and strength of neat PVDF fibers are increased by 36 and 12%, respectively, when they are filled with 10 wt% BaTiO3 content. These tensile results of BaTiO3/PVDF fibers are contrary to those obtained by Fang et al. [16] on thin films of BaTiO3/poly(vinyledene fluoride-trifluoroethylene) (P(VDF-TrFE)) [16]. In their study, adding BaTiO3 to P(VDF-TrFE) softened and reduced the matrix tensile strength. Reductions in both stiffness and strength of the composite films are attributed to the weak chemical bonding between the BaTiO3 particles and P(VDF-TrFE) matrix and the inhibition of crystallinity due to the addition of BaTiO3 particles. By contrast, we attribute the increase in tensile properties of BaTiO3/PVDF fibers to the reinforcement effect of BaTiO3. We employ DMA to investigate the influence of BaTiO3 on the polymeric chain mobility within the fibrous matrix and attribute the increase in strength and stiffness of the fibers to the reinforcement effect of BaTiO3. Figure 6 presents the loss tangent (tan δ) as a function of temperature for BaTiO3/PVDF fibers. The β-transition region of the fibers relates to the glass transition temperature (Tg) of the fibers. Comparing the effect of BaTiO3 content on the fibrous matrix, neat PVDF fibers show a peak of the tan δ versus temperature curve at the lowest temperature (−37.33°C) while the composite fibers show peaks of the tan δ versus temperature curves at higher temperatures. For example, fibers filled with 10, 20 and 40 wt% BaTiO3 show Tg at −36.06, −35.44 and −31.9°C, respectively. This explains that the mobility of neighboring chains surrounding the BaTiO3 phase is inhibited. In neat PVDF fibers, the chains are relatively free to rotate while in fibers filled with BaTiO3 phase, the BaTiO3 freezes the movement of the chains. The fact that BaTiO3 are adsorbed on PVDF surface may also explain the BaTiO3 inclusion restricts the mobility of PVDF chains.

Figure 5.

(A) Stress-strain curves obtained from tensile tests conducted on fiber samples as a function of BaTiO3 concentration. (B) Plot of tensile strength and modulus of fiber samples as a function of BaTiO3 content.

Figure 6.

Plot of tan δ versus temperature obtained using DMA. The effect of BaTiO3 content on the glass transition temperature (Tg) of the fiber is evaluated.

The effect of BaTiO3 content on the relative permittivity of Sample 2 fibers has been studied over a broad frequency range from the measured capacitance (C) which is given by:


where εr is relative permittivity of capacitor, d thickness of samples, A surface area, and ε0 is free space dielectric constant taken as 8.854 × 10−12 F/m. The dependence of relative permittivity, εr, and dielectric loss tangent of BaTiO3/PVDF fibers on frequency are shown in Figure 7A and B, respectively. Clearly, the dielectric permittivity increases with BaTiO3 content; but the dielectric loss tangent remains nearly the same for all fibers. The relaxation drop in relative permittivity at ~105 Hz is due to the characteristic dielectric behavior of PVDF matrix, and the rapid drop in dielectric permittivity after 105 Hz is because the dipole relaxations of the fibers lag behind the fast change of the applied field [1, 4, 17]. Finally, the relative permittivity of fibers with 0, 10, 20 and 40 wt% BaTiO3 at 103 Hz are 5.4, 10.6, 13.13 and 14.6, respectively (see Figure 7A).

Figure 7.

(A) Frequency dependence of effective dielectric constant (measured at 300 K) of PVDF fiber as function of BaTiO3 content. (B) Frequency dependence of effective dielectric loss tangent (measured at 300 K) of PVDF fiber as functions of BaTiO3 content.

Typically, the dielectric loss of a material should be as low as possible for its use in capacitor applications. Figure 7B compares the dielectric loss tangent of the sample fibers as a function of frequency. Typically, the loss tangent of BaTiO3 reaches a maximum value in the gigahertz and terahertz frequency range and it does not show any significant dielectric losses up to the megahertz frequency range. Thus, the dielectric loss of PVDF fibers filled with BaTiO3 recorded at low frequency (up to 106 Hz) is mainly attributed to the loss tangent values of PVDF. A moderate increase in the loss tangent above 106 Hz frequency is due to the loss tangent contribution arising from the BaTiO3. It is evident from Figure 7B there is a clear dielectric loss peak at 5 MHz which is attributed to the relaxation loss process of PVDF [17]. These results show that the dielectric properties of BaTiO3/PVDF are useful for applications in electronic devices.

4. Conclusion

In this study, we use electrospinning to obtain PVDF fibers reinforced with BaTiO3. We demonstrate the effect of BaTiO3 on the crystalline structure developments, tensile and dielectric properties of PVDF fibers. Reinforcing PVDF fibers with BaTiO3 promotes the formation of ferroelectric β-crystalline phase within the fibers. Tensile strength and stiffness of the fibers increase with BaTiO3 content. Finally, the effective dielectric permittivity and dielectric loss of the fibers increase with BaTiO3 content at all frequencies studied.


We thank the Australian Research Council (ARC) for the continuous support of this project (#DP0665856).

© 2018 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution 3.0 License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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Avinash Baji and Yiu-Wing Mai (March 12th 2018). Effect of Barium Titanate Reinforcement on Tensile Strength and Dielectric Response of Electrospun Polyvinylidene Fluoride Fibers, Novel Aspects of Nanofibers, Tong Lin, IntechOpen, DOI: 10.5772/intechopen.74662. Available from:

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