Characterizations and Significantly Enhanced Dielectric Properties of PVDF Polymer Nanocomposites by Incorporating Gold Nanoparticles Deposited on BaTiO3 Nanoparticles.

Poly(vinylidene fluoride) (PVDF) nanocomposites were fabricated by incorporating BaTiO3 nanoparticles (particle size of ~100 nm, nBT), which were deposited by Au nanoparticles (nAu) with an average particle size of 17.8 ± 4.0 nm using a modified Turkevich method. Systematic characterizations on the synthesized nAu-nBT hybrid nanoparticles and nAu-nBT/PVDF nanocomposites with different contents of a filler were performed. The formation of nAu-nBT hybrid nanoparticles was confirmed with the calculated nAu:nBT ratio of 0.5:99.5 wt.%. The homogeneous dispersion of nAu and nBT in the PVDF polymer was obtained due to the interaction between the negative surface charge of the nAu-nBT filler (compared to that of the nBT) and polar β-PVDF phase, which was confirmed by the zeta potential measurement and Fourier-transform infrared spectroscopy, respectively. A significantly increased dielectric permittivity (ε' ~ 120 at 103 Hz) with a slight temperature-dependent of <±15% ranging from -20 to 140 °C was obtained. Notably, a low loss tangent (tanδ < 0.08) was obtained even at a high temperature of 140 °C. Therefore, incorporating a PVDF polymer with nAu-nBT hybrid nanoparticles is an attractive method to improve the dielectric properties of a PVDF polymer for dielectrics applications.

1. Introduction

Recently, a new method for improving the dielectric and electrical properties of polymer composites, especially for poly(vinylidene fluoride) (PVDF)-based composites, has widely been studied to increase the performance of dielectric polymers [1,2,3,4,5]. Polymer nanocomposites have been focused on due to a large surface area of the nano-filler used, resulting in significantly improved electrical, dielectric, and mechanical properties [4,6,7,8,9,10,11]. To develop dielectric capacitors in embedded devices, polymer composites with low loss tangent (tanδ) and high dielectric permittivity (ε′) are required [1].

The basic method to enhance the dielectric response is to fill high-ε′ ceramic fillers, such as Cu3Ti4O12 ( = Ca, Na0.5Bi0.5, Na0.5Y0.5, and Na0.33Ca0.33Bi0.33) [12,13,14,15], TiO2-nanorod [16], FeO3 ( = Bi and La) [17,18], BaTiO3 (BT) [1,19], (La, Nb) codoped TiO2 [11], and Ba(Fe0.5Nb0.5)O3 [10]) into the polymer matrix. Thus, the giant dielectric oxides, such as TiO2-based, La2-xSrxNiO4, and K1.53(Cu0.76Ti7.24)O16 ceramic particles [16,20,21], may be the interesting filler for use to enhance the dielectric response of polymer composites. Unfortunately, the tanδ values of the ceramic/polymer composites are still too large (>0.1) for applications when the volume fraction (ffiller) of a filler is 0.5 [10,14,15,16,19], which significantly deteriorate the electrical breakdown strength of polymer composites.

Another method to enhance the dielectric response is to incorporate conductive nanoparticles, such as Ag [22,23], Al [24], and Ni [25], into the polymer matrix at volumes close to the percolation threshold. The dielectric response is usually dependent on the morphologies and conductivity of conductive fillers [4]. However, the significantly increased ε′ value of the conductor/polymer composites is accompanied by the enormous value of the conductivity and tanδ near the percolation threshold, which is unsuitable for the applications of the polymer composites. It is worth noting that gold nanoparticle (nAu) is attractive because of its high electrical conductivity and for being nontoxic. Nevertheless, a designed route for obtaining polymer composites with large ε′ and suppressed tanδ must be performed.

The alternative route to obtain high ε′ with a low tanδ value of a polymer composite is to fill it with a hybrid filler, consisting of ceramic particles with high-ε′ as the primary filler and metal nanoparticle as a minor fille. The discrete growth of metal nanoparticles on the surface of ceramic particles is usually designed, such as Ag-deposited BT nanoparticle (nBT) [26,27] and Ag-deposited CaCu3Ti4O12 [28,29], to prevent the continuous contract of the metal nanoparticles, giving rise to the formation of conducting network. Most recently, we found that the dielectric properties of the PVDF polymer composites can be improved by incorporating hybrid particles of Au-deposited BiFeO3, Na0.5Y0.5Cu3Ti4O12, and TiO2-nanorod [30,31,32]. Although the nAu-nBT/PVDF polymer composite is one of the most interesting three-phase composites [33], the systematic characterizations of this composite system have never been reported. Furthermore, the dielectric properties as a function of temperature have also never been reported. The variation of the dielectric properties with temperature is one of the essential data for determining material to use in practical applications.

Thus, in this work, the method to improve the dielectric properties of the PVDF polymer with suppressing tanδ over a wide temperature range was proposed. The nAu-nBT hybrid nanoparticle with a low nAu:nBT ratio of 0.5:99.5 was fabricated as a filler in the PVDF matrix. The nAu-nBT and nAu-nBT/PVDF nanocomposites were systematically characterized. The dielectric properties were studied and described to evaluate whether such materials are suitable for dielectric capacitor applications.

2. Experimental Details

2.1. Preparation of nAu-nBT Hybrid Particles

A modified Turkevich method was used to prepare the nAu-nBT hybrid particles [34], which is a method to reduce Au ions antecedent with sodium citrate in deionized (DI) water. First, 1.4 g of nBT powder with an average particle size of ~100 nm (Sigma–Aldrich Co., (St. Louis, MO, USA)) was dispersed in DI water (50 mL) in a beaker to form a white solution at room temperature. Second, the 500 µL of HAuCl4.3H2O (0.65 mM) (Sigma–Aldrich Co., Louis, MO, USA) solution was added into the homogeneous dispersion of nBT particles in the beaker above. Then, the suspension of nBT in the HAuCl4.3H2O solution was heated to ~100 °C under constant stirring. Next, the 4 mL of C6H5Na3O7·2H2O (Sigma–Aldrich Co, Hamburg, Germany) (38.8 mM) solution was dissolved into the above beaker under constant stirring. Usually, the reaction is complete when the color of the solution changes from white to red color. Then, the red color solution was slowly cooled to 25 °C. After that, the red color solution was centrifuged and washed 3–5 times by DI water. Finally, to achieve the nAu-nBT hybrid particles, the solution was freeze-dried [33].

2.2. Preparation of nAu-nBT/PVDF Nanocomposites

We calculated the volume fractions of the PVDF matrix and filler using the equation, where is the percentage of nAu-nBT by volume, is the theoretical density of nAu-nBT, is the density of the PVDF polymer (1.74 g/cm3). The was calculated from the equation, where and are the nBT (6.08 g/cm3) and nAu (19.3 g/cm3), respectively. and are the volume fractions of the nBT and nAu, respectively. We showed that the percentage ratio of nAu:nBT was obtained to be 0.5:99.5 wt%. By using Equations (1) and (2), the was calculated and found to be 6.1 g/cm3. Thus, the nanocomposites with different volume fractions of nAu-nBT hybrid particles can be designed in the experimental using Equation (1). The PVDF polymer nanocomposites filled with nAu-nBT hybrid particles were fabricated. First, PVDF powder (Mw ~ 534,000, Sigma–Aldrich, Saint-Quentin-Fallavier, France) was thoroughly mixed with the nAu-nBT powder in different volume fractions (fAu-) by a wet ball-milling method for 3 h in ethanol using ZrO2 balls as a grinding media. Second, ZrO2 balls were separated from the mixed PVDF and nAu-nBT powders. Then, the ethanol was evaporated from the mixture by heating at 80 °C for 24 h. After that, the mixed powder was molded by hot pressing at 200 °C under 10 MPa for 0.5 h. Finally, the nAu-nBT/PVDF nanocomposite disks with a thickness of ~0.6–1 mm and a diameter of ~12 mm were achieved. Note that the nBT/PVDF nanocomposites were also fabricated using the same method to show the effect of the addition nAu particles.

2.3. Characterization Techniques and Dielectric Measurement

The phase compositions of the nAu-nBT powders and nAu-nBT/PVDF composites were investigated using X-ray diffraction (XRD; PANalytical, EMPYREAN, Shanghai, China). The morphologies of the nBT and nAu-nBT particles were revealed using transmission electron microscopy (TEM; FEI Tecnai G2 20, Eindhoven, The Netherlands). The nAu-nBT powder was also characterized by UV-vis absorption spectroscopy (Shimadzu, UV-1800, Beachwood, OH, USA). The stability properties and the electrostatic surface charge of nBT, nAu, and nAu-nBT were measured using Zetasizer (ZS-90 Malvern Instruments, Manchester, UK). Field-emission scanning electron microscopy (FE-SEM, FEI Helios Nanolab G3 CX) was used to show the dispersion of the nAu-nBT particles, while energy dispersive X-ray spectroscopy (EDS) was used to determine the elemental composition of the nanocomposites. FE-SEM-EDS mapping images were also corrected. Prior to characterizing the morphologies, the nanocomposites were immersed in liquid N2 for 5 min. After that, the nanocomposites were fractured. Then, the cross-sections of the nanocomposites were coated by Au sputtering for 2 min. The phases of the PVDF polymer matrix were characterized using Fourier transform infrared spectroscopy (FTIR; Bruker, TENSOR27, Bremen, Germany). The thermal behavior of nAu-nBT/PVDF nanocomposite was characterized by differential scanning calorimetry (DSC, PerkinElmer, 8000 Advanced Double-Furnace, Solingen, Germany).

Before dielectric measurements, the disk samples were painted on both sides with silver paste and then dried at 100 °C for 30 min. The dielectric properties of the nAu-nBT/PVDF nanocomposites were investigated using an impedance analyzer (KEYSIGHT, E4990A, Santa Rosa, CA, USA) under an AC oscillation voltage of 500 mV over a frequency range of 102–106 Hz and temperature range of −60 to 140 °C.

3. Results and Discussion

The TEM images of the morphologies of nBT particles and nAu-nBT hybrid particles are revealed in Figure 1a,b, respectively. The nBT particles are nearly spherical in shape with a particle size of ~100 nm. The nAu particles have a spherical shape and are randomly deposited on the surface of nBT particles. As shown in Figure 1c, the size distribution of nAu is narrow with an average particle size of ~17.8 ± 4.0 nm, which is comparable to the particle size of nAu prepared by the Turkevich method reported in the literature [33,34].

Figure 1

TEM images of the surface morphologies of (a) nBT and (b) nAu-nBT particles. (c) Size distribution of nAu nanoparticles deposited on nBT.

To demonstrate the complete deposition of nAu particles on the surface of nBT, UV-vis spectroscopy was used to examine the existence of nAu particles. As shown in Figure 2, the noticeable absorbance peak at the wavelength of ~520 nm was observed in the UV-vis spectrum of the HAuCl4.3H2O solution (red color solution in the inset (1)), indicating the formation of nAu particles in this process [35]. This result is similar to those reported in the literature [35,36]. After the above solution was centrifuged to precipitate the nAu-nBT powder, the separated transparency solution (inset (2)) was further characterized by UV-vis spectroscopy. The UV-vis spectrum showed no absorbance peak, confirming that there was no residual nAu in the separated transparency solution. This result confirmed that most all of the nAu can be reacted completely and decorated on the surface of nBT. This result was consistent with that observed in the TEM image, as shown in Figure 1b. According to the designed starting raw materials used for fabricating the nAu-nBT hybrid particles, the percentage ratio of the nAu:nBT in the starting materials used was 0.5:99.5 wt%. Thus, the ratio of the nAu:nBT in the obtained nAu-nBT hybrid particles should be ≈5:99.5 wt%.

Figure 2

UV-vis spectra of HAuCl4.3H2O solution (1) and separated transparency solution after HAuCl4.3H2O solution (2) was centrifuged; insets (1) and (2) show the photo images corresponding to the UV-vis spectra #1 and #2.

The XRD patterns in the 2θ range of 10°–70° for the nAu-nBT and nBT powders are displayed in Figure 3. The BT phase was confirmed in both the nAu-nBT and nBT powders. The tetragonal phase structure of BT can usually be detected at room temperature. As shown in the inset of Figure 3, the characteristic peak at 2θ ≈ 45° ((200) plane) of the nBT showed a single peak, indicating a cubic phase structure of the nBT particles used due to the nanoparticle form [26,37]. The XRD pattern of the nAu-nBT powder also showed the characteristic peaks corresponding to the (111) and (200) planes of Au (JCPDS 00-001-1172), confirming the presence of nAu in the hybrid powder. Although Au is expensive, it was used in minimal quantities compared to that of the silver (Ag)-deposited nBT hybrid particles [26,27,38] or Ni-Na0.33Ca0.33Bi0.33Cu3Ti4O12 [39].

Figure 3

XRD patterns of nBT powder and nAu-nBT hybrid powder.

The obtained nAu-nBT hybrid particles were incorporated into the PVDF matrix with different contents for fabricating the nAu-nBT/PVDF nanocomposites. The FE-SEM images of the morphologies of fractured surfaces of the PVDF polymer and nAu-nBT/PVDF nanocomposites with fAu- = 0.1 and 0.5 are shown in Figure 4. The continuous phase of the PVDF polymer was observed, as shown in Figure 4a. The nAu-nBT particles were randomly distributed throughout the PVDF matrix with a small degree of agglomeration, as shown in Figure 4b. The morphology of the nanocomposite with fAu- = 0.5 is shown in Figure 4c. The continuous phase of the PVDF matrix decreased. A small number of pores were observed due to the increased fAu-.

Figure 4

FE-SEM of fractured surface for nAu-nBT/PVDF nanocomposites with fAu- = (a), 0 (PVDF), (b), 0.1 and (c) 0.5.

To confirm the phase compositions, the pure PVDF polymer and nAu-nBT/PVDF nanocomposites with various contents of nAu-nBT hybrid (10–50 vol%) were characterized using the XRD technique. As indicated in Figure 5, the non-polar α-phase and the polar β- and γ-phases were detected in the XRD pattern of the PVDF polymer. The diffraction peaks at 2θ ≈ 18°and 26.7° can be assigned as the α-phase, corresponding to the (100) and (021) planes, respectively. The β-phase peak was indexed at 2θ ≈ 20.4° and 36.6°, corresponding to the (110) and (200) planes, respectively. The γ-phase peak was detected at 2θ ≈ 18.6°, corresponding to the (020) plane [3,40,41,42]. For the nAu-nBT/PVDF nanocomposites with low fAu-, the intensity of these PVDF-phases was very low due to the high crystallinity of the filler. Furthermore, all PVDF-phases cannot be observed in the nAu-nBT/PVDF nanocomposites with high fAu-. The phases of a PVDF polymer in the composites can be formed in several phases, depending on to preparation method and types of fillers [2,3].

Figure 5

XRD patterns of PVDF and nAu-nBT/PVDF nanocomposites with various contents of nAu-nBT (fAu- = 0.1–0.5).

The nAu-nBT/PVDF nanocomposites were further characterized using the FTIR technique to identify the phases of the PVDF polymer matrix. Figure 6 shows the FTIR spectra of the PVDF and nAu-nBT/PVDF nanocomposites. The FTIR peaks for the α-phase were observed at the wavenumbers of 766, 791, 873, 1179, and 1401 cm−1 [40,41]. The peak at 840, 1072, and 1275 cm−1 confirmed the presence of the β-phase of PVDF polymers [41]. It is worth noting that the characteristic peaks of the β- and γ-phases around 840–841 cm−1 were very close. The absorption values at 766 (Aα) and 840 cm−1 (Aβ) for the α and β phases, respectively, were used to calculate the β-phase content (F(β)) [41], as the following equation. where Kα and Kβ are the absorption coefficients of the α and β phases, the values of which were 6.1 × 104 and 7.7 × 104 cm2·mol−1, respectively [41]. The F(β) values of the nAu-nBT/PVDF nanocomposites with fAu- = 0.1, 0.2, 0.3, 0.4, and 0.5 were 56, 53, 45, 43, 41, and 39%, respectively. The polar β-phase in the nanocomposites was dependent on the relative volume fraction.

Figure 6

FTIR spectra of nAu-nBT/PVDF nanocomposites with various contents of nAu-nBT (fAu- = 0.1–0.5).

The zeta potential measurements of the nAu, nBT, and nAu-nBT hybrids were performed by dispersing these particles in DI water to examine the electrostatic surface charge. The zeta potential of nBT cannot be measured because the dispersion of nBT was not stable in DI water, which precipitated in a few minutes. Nevertheless, the average zeta potential values of the nAu and nAu-nBT were obtained to be −23.33 ± 4.05 mV and −16.87 ± 0.65 mV, respectively. The nBT and nAu-nBT were further dispersed in dimethyl sulfoxide (DMSO) solution for measuring the zeta potential values. The average zeta potential values of the nBT and nAu-nBT were obtained to be 6.26 ± 1.20 mV and −6.62 ± 0.16 mV, respectively. The average positive-electrostatic surface charge of the nBT was changed to a negative charge by depositing with nAu particles. This result also confirmed that the nAu can decorate on the surface.

As demonstrated in Figure 7a, for a low fAu-, the nAu-nBT hybrid particles with a negative surface charge interacted with the positive charge (–CH2 dipole) of the β-PVDF polymer matrix, resulting in good compatibility between the PVDF polymer and a hybrid filler (Figure 4b) due to a large F(β). As demonstrated in Figure 7b, for a high fAu-, the significantly decreased F(β) resulted in the agglomeration of nAu-nBT hybrid particles (Figure 4c). This is because the total negative charge of the hybrid particles in the composite is larger than the total positive charges of the β-PVDF polymer.

Figure 7

(a) Interaction between –CH2 dipole of PVDF polymer and negatively surface charge of nAu-nBT hybrid particles. (b) Schematic of loading of different concentrations of nAu-nBT filler into PVDF polymer chain with an increasing vol% of nAu-nBT.

Figure 8 shows the DSC curves of the PVDF and nAu-nBT/PVDF nanocomposites with fAu- = 0.1, 0.3, and 0.5. The incorporation of nAu-nBT hybrid particles into the PVDF polymer caused a slight decrease in the melting temperature (Tm), which was similar to that observed in the nAu-nBT/PVDF composites [32]. As shown in Table 1, the melting enthalpy (ΔH) of the nanocomposites decreased significantly as the nAu-nBT increased. The X of polymer nanocomposite was calculated using the following equation (4). where ΔH and ΔH100% are the melting enthalpies of crystallization of the nanocomposites and the melting enthalpy of fusion of pure crystallization PVDF (104.7 J g−1), respectively [32]. The X of the PVDF polymer matrix reduced from 39.53% to 5.58% for the nanocomposite with fAu- = 0.5, which may be attributed to the inhibited polymer chain movement by the hybrid filler.

Figure 8

DSC thermograph of PVDF and nAu-nBT/PVDF nanocomposites with various contents of nAu-nBT.

Table 1

Melting temperature (Tm), melting enthalpy (ΔHm), and crystallinity degree (XC) of nAu-nBT/PVDF nanocomposites with fAu- = 0.1, 0.2, and 0.3.

fn Au-nBT	Tm (°C)	ΔHm (J g−1)	XC (%)
0 (PVDF)	159.17	41.39	39.53
0.1	158.94	27.30	26.07
0.3	157.12	11.59	11.07
0.5	155.25	10.03	5.58

Figure 9 displays the dielectric properties at 25 °C in the frequency range of 102–106 Hz for the PVDF and nAu-nBT/PVDF nanocomposites. As shown in Figure 9a, the dielectric response in the nAu-nBT/PVDF nanocomposites continuously increased as the filler loading increased. Furthermore, the ε′ in the range of 103–106 Hz was almost independent of the frequency. However, the ε′ was in the range of 102–103 Hz and slightly decreased with increasing frequency. This result is usually due to interfacial polarization, especially at the interface between the nanocomposite sample and electrode [43]. The slight reduction in ε′ at the frequency of 106 Hz can be explained by the dielectric relaxation of dipolar polarization due to the orientation of C-F in the PVDF matrix [44]. The nAu-nBT/PVDF nanocomposites with fAu- = 0.1, 0.2, 0.3, 0.4, and 0.5 exhibited the largely increased ε′ values of ~41.79, 61.93, 80.73, 103.88, and 120.35, respectively (at 103 Hz). It is important to note that the ε′ value of the nAu-nBT/PVDF nanocomposite with fAu- = 0.4 was much larger than that of the two-phase nBT/PVDF nanocomposite with fBT = 0.4 (ε′ ~ 66.1) [19]. Thus, the significantly increased dielectric response in the nAu-nBT/PVDF nanocomposites should be correlated to the presence of nAu particles. For the two-phase nBT/PVDF nanocomposites, the primary cause of the enhanced dielectric response is due to the high ε′ value of the nBT particles compared to that of the PVDF polymer matrix [19], while the greatly enhanced dielectric response is due to the interfacial polarization which can only be dominant in a low-frequency range [37]. For the three-phase nAu-nBT/PVDF nanocomposites, the significantly increased dielectric response over the measured frequency range is likely due to the Maxwell–Wagner–Sillars (MWS) polarization at the nBT-nAu and PVDF-nAu interfaces [45]. The MWS effect was related to the trapped free charges at the discontinuous surfaces between the insulating and conducting phases. Hence, macroscopic dipoles could be created under an applied electric field, giving rise to the enhancement of the dielectric response in the three-phase nanocomposites. Furthermore, good compatibility between the PVDF polymer matrix and the hybrid filler particles is another cause of the observed increased dielectric response.

Figure 9

(a) Dielectric permittivity (ε′) and (b) dielectric loss tangent (tanδ) at 25 °C (102–106 Hz) of PVDF and nAu-nBT/PVDF nanocomposites with different contents of nAu-nBT.

The tanδ values of the nAu-nBT/PVDF nanocomposites are shown in Figure 9b. A low-frequency tanδ value tended to increase with increasing fAu-. The increased tanδ in a low-frequency range is attributed to the interfacial polarization associated with the DC conduction at the interface between the nanocomposite sample and electrodes, corresponding to the observed decrease in the low-frequency ε′. At 103 Hz, the nAu-nBT/PVDF nanocomposite with fAu- = 0.5 was 0.076. It can be explained that the suppressed tanδ has resulted from the modified surface of the nBT particles. The surface of nBT was still an insulating surface, in which the long-range motion of free charge carriers was inhibited by preventing the direct contact between nAu particles [26,30,31,32,38]. The sharp increase in tanδ in a high-frequency range was correlated to the decreased ε′, which originated by the αa relaxation due to the glass transition of the pure PVDF polymer [46]. Notably, the dielectric properties of the nAu-nBT/PVDF nanocomposite with fAu- = 0.5 were greatly be improved with increased ε′ of ~120 and retained low tanδ. The improved dielectric properties of the nAu-nBT/PVDF nanocomposites were comparable to those of three-phase polymer nanocomposites [26,30,31,32]. The effect of nAu particles on the dielectric response of the nAu-nBT/PVDF nanocomposites with different fAu- is demonstrated in Figure 10a,d. The ε′ values of the nAu-nBT/PVDF nanocomposites were compared to those values of the nBT/PVDF nanocomposites. As clearly seen, the ε′ values of the nBT/PVDF nanocomposites increased by incorporating a small number of nAu particles. These results indicated that the addition of nAu particles produced interfacial polarization, giving rise to the enhanced ε′ value.

Figure 10

Comparison of dielectric permittivity (ε′) at 25 °C of nBT/PVDF and nAu-nBT/PVDF nanocomposites with different volume fractions: (a) 0.5, (b) 0.4, (c) 0.3, and (d) 0.2.

Besides the increased ε′ value with retaining tanδ, the temperature stability of the dielectric properties was also important to study the polymer nanocomposites in practical applications. The dielectric properties at 103 Hz as a function of temperature are shown in Figure 11. As depicted in Figure 11a, the ε′ of the nAu-nBT/PVDF nanocomposites with fAu- = 0.4 and 0.5 showed good stability at temperatures ranging from −20 to 140 °C According to the EIA standard [47], the changes in ε′ at 1 kHz (or capacitance change) with a temperature of the nAu-nBT/PVDF nanocomposites with fAu- = 0.4 and 0.5 were, respectively, limited to ±7.5% and ±2.2% in the temperature range from +10 °C to +130 °C compared to the ε′ value at 25 °C, which was the operating temperature range for the Z7F and Z7C (+10 °C to +125 °C) capacitors, respectively. The rapid change in ε′ at a low-temperature range resulted from the freezing of the dipole moments [26]. As shown in Figure 11b, the tanδ of the nAu-nBT/PVDF nanocomposites was slightly dependent on the temperature over the measured range, while the tanδ of the PVDF polymer greatly increased as the temperature increased, which was the α-relaxation [48]. Notably, a low tanδ (<0.08) of the nAu-nBT/PVDF nanocomposite with fAu- = 0.5 was achieved even at a high temperature of 140 °C.

Figure 11

(a) Dielectric permittivity (ε′) and (b) dielectric loss tangent (tanδ) at 103 Hz (−60–140 °C) of PVDF and nAu-nBT/PVDF nanocomposites with different contents of nAu-nBT.

4. Conclusions

The successful fabrication of nAu-nBT hybrid particles using a modified Turkevich method was demonstrated. The hybrid particles were used as a filler in the PVDF polymer to fabricate dielectric polymer nanocomposites. Greatly increased ε′ values and low tanδ values were obtained in the nAu-nBT/PVDF nanocomposites. Furthermore, the dielectric properties of the nanocomposites were stable with temperature over a wide temperature range. The nAu-nBT hybrid particles can increase the dielectric response of the polymer nanocomposites via the creation of interfacial polarization. The suppressed tanδ was due to a small number of conductive nAu particles used, which were discretely grown on the surface of the nBT particles. This observation can also cause the improved temperature stability of the dielectric properties of the nanocomposites.