# Poly(Butylene Terephthalate) Based Composites Containing Alumina Whiskers: Influence of Filler Functionalization on Dielectric Properties

Authors: Pietro Russo; Francesca Cimino; Domenico Acierno; Giovanni Lupò; Carlo Petrarca
Journal: International Journal of Polymer Science
 (2014)

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## Abstract

Poly(butylene terephthalate) (PBT) is one of the most widely used semicrystalline thermoplastics polyester because of its superior thermal and mechanical properties, high dimensional stability and excellent processability. In this research PBT-based nanocomposites, including various amounts (up to 10 wt%) of commercial alumina whiskers, have been prepared by using a Brabender internal chamber mixer and analysed in terms of morphological features and dielectric properties. Specific attention has been focused on the effect of the filler functionalization considering 3-glycidoxy propylmethoxysilane (GPS) or 3-methacryloxypropyltrimethoxysilane (MPS) as coupling agents. Tests, performed on compounds filled with neat and functionalized alumina whiskers, show a clear dependence of relative dielectric permittivityεr, invariance of dissipation factor (tgδ), and a sensible increase of volume electrical resistivity (ρv) with the filler’s content and are encouraging for a future introduction of such composites in many electrical applications.


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## Body

## 1. Introduction

Poly(butylene terephthalate) (PBT) resins are semicrystalline thermoplastics with very interesting properties such as excellent dimensional stability, high stiffness and hardness, good resistance to chemicals, good mechanical properties, and processability. Consequently they are used in a wide variety of applications to obtain items mainly obtained by injection molding.However, the ever increasing use of plastics in place of traditional materials has fed an increasing demand to develop higher performance PBT resins suitable for various processing conditions and, thus, to be utilized in various advanced fields by blending with other resins [1–5] or compounding with inorganic fillers [6–11]. In this latter case, with the awareness that optimal combinations of organic (polymer) and inorganic (nanofiller) phases can lead to novel functional materials, if an optimal distribution of the filler is achieved, interesting results are already reported in terms of improvements of several performances as UV resistance [12, 13] and flammability [14–17] of poly(butylene) terephthalate resins.Nowadays, the continuous tendency towards the miniaturization of components, the introduction of more severe duty cycles, the reduction in maintenance costs [18], or new technologies [19, 20] guides the research to investigate novel dielectric materials which would enable achieving higher electrical, mechanical, and thermal performances for electric and electronic applications. At this regard, it is known that ceramics have high dielectric permittivity and significant dielectric strength and high thermal shock resistance and chemical stability against acid-alkali corrosion but they are brittle and have poor mechanical strength. Vice versa, polymers are flexible and easy to process, have low dielectric permittivity, and can withstand high fields. So the idea is to combine the advantages of polymers and ceramics to obtain new hybrid materials with improved dielectric characteristics for several applications as in capacitors, in electrical machines, in cables, and so forth. In particular, with the advent of nanotechnology and the availability of nanosized fillers (having at least one dimension less than 100 nm), the research for “new” materials has focused its efforts on studying polymer composites obtained by adding to the original matrix various nanofillers of different shape, dimension, and weight percentage in order to impart one or more specific properties to the insulation system.In this frame, several results of the research have been already reported on epoxy based nanodielectric systems [21–26], silicone nanocomposites [27, 28] but also regarding composite systems based on thermoplastic matrices as polyethylene [29, 30], ethylene-vinyl alcohol (EVA) [31, 32], and poly(vinylidene fluoride) (PVDF) [33–35].In general, it is well established that the nature of the interfacial region plays a key role in determining the dielectric behavior of these materials. Interaction and enhanced area of the interface by inclusion of nanofillers affect the interfacial polarization through the formation of local conductivity [22]. Increases of permittivity of nanocomposites are mainly attributed to the higher permittivity of fillers with respect to the matrix, while decreases of the same dielectric parameter are usually related to restrictions of polymer chain movements at the interfaces.At this regard, it is worth to consider that in a dielectric material differences between the rate of charge accumulation and the rate of charge removal upon the application of an electrical field induce space charge phenomena which cause local increases of the internal field. Taking into account that this behavior can lead to faster degradation and premature failure of the materials, a specific attention is paid on the mechanisms of space charge formation related to the overall dielectric behavior of polymer materials [36, 37]. The research on composites has demonstrated that nanosized particles reduce the charge accumulation with dynamics much faster than in systems containing microsized ones [38] and that nanocomposites usually exhibit lowered and redistributed space charge when compared with microcomposites [39]. This behavior, according to Montanari et al. [40], can be explained assuming that, in presence of nanoparticles, shallow trap bands are formed, which either distribute or replace the original trap band, especially at high filler loadings. The presence of shallow trap bands results in higher mobility of charge carriers and hence in lower space charge accumulation. However, in certain nanocomposites it is also reported that the presence of deep traps [41], instead, would worsen the same accumulation of charges. Given that the space charge behavior is affected by the nature of both filler and matrix and by the properties of the interface, it is clear that also in this case a better understanding of the dielectric properties of polymer composite materials goes through the analysis of filler-matrix interactions.Main aim of the research was to investigate the effect of relatively low contents of Al2O3 whisker-type nanoparticles on the dielectric properties of polybutylene terephthalate based nanocomposites prepared by batch melt compounding. In light of the above observations, in this work two different chemical pretreatments of alumina whisker particles were used to improve interactions at the interface with the host matrix. The actual yield of chemical modifications based on 3-glycidoxy propylmethoxysilane (GPS) or 3-(methacryloxypropyl)trimethoxysilane (MPS) performed according to routes reported elsewhere [42, 43] was systematically verified by IR spectroscopic investigations.In all cases, after having verified the achievement of a satisfactory dispersion of the filler in the host PBT matrix by morphological observations, effects related to filler content and type of applied particle functionalization on dielectric parameters of products such as volume resistivity, permittivity, and dissipation factor evaluated at room temperature have been reported and discussed invoking the previous mentioned approaches.


## 2. Materials and Methods

### 2.1. Materials

The polymeric matrix used in this study was the poly(butylene terephthalate) (PBT) POCAN B1505 (MFI 250°C/2.16 kg: 16 g/10 min,ρ: 1.31 g/cm3, Tm: 225°C) supplied by Lanxess GmbH.Commercial alumina whiskers (Al2O3), provided by Sigma-Aldrich with particle diameter 2–6 nm and length 200–400 nm, were used as fillers.3-glycidoxy propylmethoxysilane (GPS) and 3-(methacryloxypropyl)trimethoxysilane (MPS) purchased from Sigma-Aldrich Chemical Company were employed to pretreat alumina whiskers.


### 2.2. Preparation of PBT/Al2O3 Whisker Nanocomposites

The nanocomposites were prepared in laboratory scale in successive phases according to the following procedure. The inclusion of 1%, 3%, 5%, 7%, and 10% by weight of nanosized particles of as received or prefunctionalized alumina whiskers in the molten PBT was carried out by the batch mixing technology. In particular, all composite systems were prepared in a Brabender-type internal mixer (Rheocord EC della HAAKE, NJ) at 235°C for a total mixing time of 10 min. The rotor speed was 80 rpm. The application of a centrifugal force produces a turbulent movement of the melt in which the high shear forces tend to separate the nanoparticles in order to avoid the formation of aggregates. Before compounding, PBT and alumina nanoparticles were dried overnight in a vacuum oven at 90°C. Plane, disc-shaped samples for dielectric measurements, characterized by a thickness ranging between 0.9 and 1.0 mm and diameterd=8cm, were obtained by using a lab hydraulic press operating at 240°C and 70 bar.


### 2.3. Characterization Techniques

Microscopic analysis was performed by using a field emission scanning electron microscope (SEM) Mod. FEI QUANTA 200F equipped with an energy dispersion spectrometer (EDS) Oxford INCA Energy System for element analysis of fractured surfaces. Micrographs have been obtained operating at high vacuum condition on Cr-metalized samples and at 20 kV voltage.SEM observations were completed by qualitative energy dispersion X-ray spectroscopy (EDS, Oxford, INCA Energy System) analyses in order to confirm the nature of dispersed particles.DC Volume resistivity (ρv) was measured at 21°C on the disc-shaped samples. Prior to the measurement, the specimen were held in an oven at the controlled temperature of 30°C for 48 hours. Each specimen was held in a suitable shielded cell with guarded ring electrodes and DC voltage of 1400 V, corresponding to an applied electrical field from 14 to 15.5 kV/cm. Readings of the conduction current were taken after 120 s from the application of the DC voltage, when a stable state was reached.Permittivity and dissipation factor measurements were performed at room temperature (23°C) and low voltage (1.1 V) in the frequency range (100Hz÷5MHz) by using an impedance analyzer HP 4192A and a suitable test cell Agilent 16451B. The dielectric test fixture was equipped with a 4-terminal pair cable assembly and was used in the guarded electrode configuration.


## 2.1. Materials

The polymeric matrix used in this study was the poly(butylene terephthalate) (PBT) POCAN B1505 (MFI 250°C/2.16 kg: 16 g/10 min,ρ: 1.31 g/cm3, Tm: 225°C) supplied by Lanxess GmbH.Commercial alumina whiskers (Al2O3), provided by Sigma-Aldrich with particle diameter 2–6 nm and length 200–400 nm, were used as fillers.3-glycidoxy propylmethoxysilane (GPS) and 3-(methacryloxypropyl)trimethoxysilane (MPS) purchased from Sigma-Aldrich Chemical Company were employed to pretreat alumina whiskers.


## 2.2. Preparation of PBT/Al2O3 Whisker Nanocomposites

The nanocomposites were prepared in laboratory scale in successive phases according to the following procedure. The inclusion of 1%, 3%, 5%, 7%, and 10% by weight of nanosized particles of as received or prefunctionalized alumina whiskers in the molten PBT was carried out by the batch mixing technology. In particular, all composite systems were prepared in a Brabender-type internal mixer (Rheocord EC della HAAKE, NJ) at 235°C for a total mixing time of 10 min. The rotor speed was 80 rpm. The application of a centrifugal force produces a turbulent movement of the melt in which the high shear forces tend to separate the nanoparticles in order to avoid the formation of aggregates. Before compounding, PBT and alumina nanoparticles were dried overnight in a vacuum oven at 90°C. Plane, disc-shaped samples for dielectric measurements, characterized by a thickness ranging between 0.9 and 1.0 mm and diameterd=8cm, were obtained by using a lab hydraulic press operating at 240°C and 70 bar.


## 2.3. Characterization Techniques

Microscopic analysis was performed by using a field emission scanning electron microscope (SEM) Mod. FEI QUANTA 200F equipped with an energy dispersion spectrometer (EDS) Oxford INCA Energy System for element analysis of fractured surfaces. Micrographs have been obtained operating at high vacuum condition on Cr-metalized samples and at 20 kV voltage.SEM observations were completed by qualitative energy dispersion X-ray spectroscopy (EDS, Oxford, INCA Energy System) analyses in order to confirm the nature of dispersed particles.DC Volume resistivity (ρv) was measured at 21°C on the disc-shaped samples. Prior to the measurement, the specimen were held in an oven at the controlled temperature of 30°C for 48 hours. Each specimen was held in a suitable shielded cell with guarded ring electrodes and DC voltage of 1400 V, corresponding to an applied electrical field from 14 to 15.5 kV/cm. Readings of the conduction current were taken after 120 s from the application of the DC voltage, when a stable state was reached.Permittivity and dissipation factor measurements were performed at room temperature (23°C) and low voltage (1.1 V) in the frequency range (100Hz÷5MHz) by using an impedance analyzer HP 4192A and a suitable test cell Agilent 16451B. The dielectric test fixture was equipped with a 4-terminal pair cable assembly and was used in the guarded electrode configuration.


## 3. Results and Discussion

### 3.1. Morphology

All investigated composites were systematically investigated by morphological point of view to verify the actual distribution of the alumina particles within the polymer matrix.As an example, Figures1, 2, and 3 compare micrographs, at equal magnification, of systems containing 1, 5, and 10% by weight of alumina whiskers, respectively. Pictures clearly highlight in all cases the existence of a uniform distribution of dots. Holes which appeared in case of nonfunctionalized samples are probably just related to the expulsion of included particles during the fracture of samples. Instead, expectedly, dots appeared to be linked to the host matrix in case of functionalized systems for which the fracture step induced a certain yielding behaviour of the polyester matrix just in correspondence of alumina particles.SEM micrographs of fracture surfaces of samples containing 1% by weight of alumina whiskers as received (a), functionalized with GPS (b), and functionalized with MPS (c).
(a)
(b)
(c)SEM micrographs of fracture surfaces of samples containing 5% by weight of alumina whiskers as received (a), functionalized with GPS (b), and functionalized with MPS (c).
(a)
(b)
(c)SEM micrographs of fracture surfaces of samples containing 10% by weight of alumina whiskers as received (a), functionalized with GPS (b), and functionalized with MPS (c).
(a)
(b)
(c)The nature of these dots was verified by an EDS elemental analyses. At this purpose, punctual sampling of the dots gave rise to typical spectra shown in Figure4. The analysis of characteristic peaks with the aid of suitable data banks confirmed the attribution of dispersed dots to alumina fillers.Elemental EDS analysis of fracture surfaces. Punctual sampling in (a) gives rise to the spectra reported in (b).
(a)
(b)


### 3.2. DC Volume Resistivity

The data presented in the paper are an average value of five samples; three measurements were made for each sample, taking care that between two consecutive measurements the sample was held between grounded electrodes until the short circuit currents fell below the noise level.Results indicated both an influence of filler functionalization and filler content on DC volume resistivity, as highlighted by the picture shown in Figure5. The volume resistivity is higher than that in the unfilled resin; in particular, the introduction of a small amount of filler (less than 1% by weight) increased the DC volume resistivity value (ρv) of about 4 orders of magnitude for the functionalized (MPS and GPS) samples and of about 3 orders of magnitude for the nonfunctionalized samples (NOf). When increasing the filler content, resistivity slightly decreases and in the nonfunctionalized samples we find a sudden drop at 10% alumina content.Figure 5
Volume resistivity versus alumina content: comparison among nonfunctionalized and functionalized systems.With respect to this latter behavior, it is worth to note that, generally, the introduction of inorganic fillers into the matrix can increase the DC conductivity since nanofiller particles, modifying the relaxation of the matrix at the interface, act as ion scavenger which becomes a possible source of ionic carriers to increase the conductivity [44]. The increase in resistivity, instead, may be attributed to the creation of new trap bands, deeper than the original trap band of the base polymer. In fact, the nanoparticle surface creates a change in the polymer structure which can become dominant as the size of filler is reduced and, due to such a structural change, new band can be originated by the surface interaction between the nanofillers and the base polymer, which reduces carrier mobility and increases volume resistivity. The decrease of resistivity with filler content probably indicates that a critical interfacial area has been reached, which corresponds to a minimum of charge carriers mobility and energy and to a strong and stable bonding between the nanofiller surface and the polymer matrix. If the nanocomposite is not functionalized, for high filler contents such an effect disappears and at 10% filler content the composite is similar to the unfilled material. Experiments are underway to investigate the dielectric behavior in case of nanofiller contents lower than 1% by weight.


### 3.3. Dielectric Spectroscopy

Tests were performed using standard equipment and, also in this case, the reported data are mean values of 3 measurements for sample. Each specimen, prior to the measurement, was kept in an oven at a controlled temperature of 30°C.We were interested in the real partε′ of complex permittivity ε* of the material and in the dissipation factor tgδ which, respectively, are related to the energy stored in the medium and to losses in the dielectric. Firstly we used the instrumentation to measure the capacitance C and the dissipation factor of each specimen and then the real part of the complex permittivity was obtained by the geometry of the samples.Regarding the real part of permittivity, this dielectric parameter is generally increased if the base polymer is filled with microsized particles since the filler have higher permittivity than unfilled polymers and cause interfacial polarization phenomena of the Maxwell-Wagner-Sillars type by blocking of charges at the interfaces. On the contrary, in the case of nanosized fillers, as reported in Figure6, our results showed a slight decrease of relative permittivity εr′ with a filler content up to 3% wt, a result which is in accordance with many experimental observations [45]. Lower permittivity values can be considered as a sign of a good nanocomposite. This reduction, in line with previous considerations, is probably ascribed to the restriction of polymer chain movement by nanoparticles, due to the modified molecular structure and chain dynamics which cause a strong surface interaction between the filler and the polymer matrix [46]. The multilayered core model proposed by Tanaka [47] takes into account this phenomenon by introducing a tightly bonded first layer between the nanofiller and the polymer matrix. Such bonding leads to restricted mobility of polymer chains and to lower permittivity values.Relative permittivity (ε) as a function of the applied frequency (f) for systems filled with nonfunctionalized (a), GPS functionalized (b), and MPS functionalized (c) alumina whiskers.
(a)
(b)
(c)At higher filler contents, instead, the situation appears to be reversed with the permittivity that becomes greater than the base polymer probably because, in this case, as the volume of filler material increases, the individual permittivity of the nanofillers may give its fundamental contribution. Inhomogeneous dispersion and the formation of clusters can also explain such an increase [48].As concerns the influence of functionalization on the changes of relative permittivity with respect to the unfilled polymer, it can be observed that the spread between the lower and the maximum value ofεr′ is greater in the nonfunctionalized samples, thus confirming that the connection of dipolar groups to the nanoparticle surface can be in this case highly variable, while functionalization makes it much more stronger and stable [49].In all specimens, the permittivity decreases monotonically with frequency since it becomes more difficult for larger dipolar groups to orient themselves, and their contribution to polarization tends to disappear with frequency.The frequency response of dissipation factor (tgδ) is shown in Figure 7 for all the different varieties of nanocomposites. Losses in the nanocomposites do not differ much if compared with the unfilled polymer. Lower values in the whole frequency range were shown by composites with low filler content (1% and 3%), while the 10% specimen always exhibited the highest tgδ values. The lower losses can be attributed to a restriction of side chains in proximity of the nanofillers. A broad loss peak at high frequencies (in the MHz range) is always present and testifies the presence of relaxation phenomena in the polymer.Dissipation factor (tanδ) as a function of the applied frequency (f) for systems filled with nonfunctionalized (a), GPS functionalized (b), and MPS functionalized (c) alumina whiskers.
(a)
(b)
(c)The dissipation factor takes into account both conduction and polarization losses. In our case, considering the relatively low value of the applied electric field intensity, the increase in electrical resistivity with filler content does not sensibly contribute to a reduction oftgδ values with respect to the neat polymer, probably because the effects of deeper trap bands are high-field phenomena. Dissipation factor increases with frequency as shown in Figure 5 since the main contribution is given by polarization losses that are due to molecular friction. The differences at various filler contents are almost negligible.Also in thetgδ spectra we can observe the effects of functionalization which, by stabilizing the adhesion between the filler and the polymer matrix, ensures a more stable behavior of the dissipation factor, with marginal differences among the values measured at different filler content.


## 3.1. Morphology

All investigated composites were systematically investigated by morphological point of view to verify the actual distribution of the alumina particles within the polymer matrix.As an example, Figures1, 2, and 3 compare micrographs, at equal magnification, of systems containing 1, 5, and 10% by weight of alumina whiskers, respectively. Pictures clearly highlight in all cases the existence of a uniform distribution of dots. Holes which appeared in case of nonfunctionalized samples are probably just related to the expulsion of included particles during the fracture of samples. Instead, expectedly, dots appeared to be linked to the host matrix in case of functionalized systems for which the fracture step induced a certain yielding behaviour of the polyester matrix just in correspondence of alumina particles.SEM micrographs of fracture surfaces of samples containing 1% by weight of alumina whiskers as received (a), functionalized with GPS (b), and functionalized with MPS (c).
(a)
(b)
(c)SEM micrographs of fracture surfaces of samples containing 5% by weight of alumina whiskers as received (a), functionalized with GPS (b), and functionalized with MPS (c).
(a)
(b)
(c)SEM micrographs of fracture surfaces of samples containing 10% by weight of alumina whiskers as received (a), functionalized with GPS (b), and functionalized with MPS (c).
(a)
(b)
(c)The nature of these dots was verified by an EDS elemental analyses. At this purpose, punctual sampling of the dots gave rise to typical spectra shown in Figure4. The analysis of characteristic peaks with the aid of suitable data banks confirmed the attribution of dispersed dots to alumina fillers.Elemental EDS analysis of fracture surfaces. Punctual sampling in (a) gives rise to the spectra reported in (b).
(a)
(b)


## 3.2. DC Volume Resistivity

The data presented in the paper are an average value of five samples; three measurements were made for each sample, taking care that between two consecutive measurements the sample was held between grounded electrodes until the short circuit currents fell below the noise level.Results indicated both an influence of filler functionalization and filler content on DC volume resistivity, as highlighted by the picture shown in Figure5. The volume resistivity is higher than that in the unfilled resin; in particular, the introduction of a small amount of filler (less than 1% by weight) increased the DC volume resistivity value (ρv) of about 4 orders of magnitude for the functionalized (MPS and GPS) samples and of about 3 orders of magnitude for the nonfunctionalized samples (NOf). When increasing the filler content, resistivity slightly decreases and in the nonfunctionalized samples we find a sudden drop at 10% alumina content.Figure 5
Volume resistivity versus alumina content: comparison among nonfunctionalized and functionalized systems.With respect to this latter behavior, it is worth to note that, generally, the introduction of inorganic fillers into the matrix can increase the DC conductivity since nanofiller particles, modifying the relaxation of the matrix at the interface, act as ion scavenger which becomes a possible source of ionic carriers to increase the conductivity [44]. The increase in resistivity, instead, may be attributed to the creation of new trap bands, deeper than the original trap band of the base polymer. In fact, the nanoparticle surface creates a change in the polymer structure which can become dominant as the size of filler is reduced and, due to such a structural change, new band can be originated by the surface interaction between the nanofillers and the base polymer, which reduces carrier mobility and increases volume resistivity. The decrease of resistivity with filler content probably indicates that a critical interfacial area has been reached, which corresponds to a minimum of charge carriers mobility and energy and to a strong and stable bonding between the nanofiller surface and the polymer matrix. If the nanocomposite is not functionalized, for high filler contents such an effect disappears and at 10% filler content the composite is similar to the unfilled material. Experiments are underway to investigate the dielectric behavior in case of nanofiller contents lower than 1% by weight.


## 3.3. Dielectric Spectroscopy

Tests were performed using standard equipment and, also in this case, the reported data are mean values of 3 measurements for sample. Each specimen, prior to the measurement, was kept in an oven at a controlled temperature of 30°C.We were interested in the real partε′ of complex permittivity ε* of the material and in the dissipation factor tgδ which, respectively, are related to the energy stored in the medium and to losses in the dielectric. Firstly we used the instrumentation to measure the capacitance C and the dissipation factor of each specimen and then the real part of the complex permittivity was obtained by the geometry of the samples.Regarding the real part of permittivity, this dielectric parameter is generally increased if the base polymer is filled with microsized particles since the filler have higher permittivity than unfilled polymers and cause interfacial polarization phenomena of the Maxwell-Wagner-Sillars type by blocking of charges at the interfaces. On the contrary, in the case of nanosized fillers, as reported in Figure6, our results showed a slight decrease of relative permittivity εr′ with a filler content up to 3% wt, a result which is in accordance with many experimental observations [45]. Lower permittivity values can be considered as a sign of a good nanocomposite. This reduction, in line with previous considerations, is probably ascribed to the restriction of polymer chain movement by nanoparticles, due to the modified molecular structure and chain dynamics which cause a strong surface interaction between the filler and the polymer matrix [46]. The multilayered core model proposed by Tanaka [47] takes into account this phenomenon by introducing a tightly bonded first layer between the nanofiller and the polymer matrix. Such bonding leads to restricted mobility of polymer chains and to lower permittivity values.Relative permittivity (ε) as a function of the applied frequency (f) for systems filled with nonfunctionalized (a), GPS functionalized (b), and MPS functionalized (c) alumina whiskers.
(a)
(b)
(c)At higher filler contents, instead, the situation appears to be reversed with the permittivity that becomes greater than the base polymer probably because, in this case, as the volume of filler material increases, the individual permittivity of the nanofillers may give its fundamental contribution. Inhomogeneous dispersion and the formation of clusters can also explain such an increase [48].As concerns the influence of functionalization on the changes of relative permittivity with respect to the unfilled polymer, it can be observed that the spread between the lower and the maximum value ofεr′ is greater in the nonfunctionalized samples, thus confirming that the connection of dipolar groups to the nanoparticle surface can be in this case highly variable, while functionalization makes it much more stronger and stable [49].In all specimens, the permittivity decreases monotonically with frequency since it becomes more difficult for larger dipolar groups to orient themselves, and their contribution to polarization tends to disappear with frequency.The frequency response of dissipation factor (tgδ) is shown in Figure 7 for all the different varieties of nanocomposites. Losses in the nanocomposites do not differ much if compared with the unfilled polymer. Lower values in the whole frequency range were shown by composites with low filler content (1% and 3%), while the 10% specimen always exhibited the highest tgδ values. The lower losses can be attributed to a restriction of side chains in proximity of the nanofillers. A broad loss peak at high frequencies (in the MHz range) is always present and testifies the presence of relaxation phenomena in the polymer.Dissipation factor (tanδ) as a function of the applied frequency (f) for systems filled with nonfunctionalized (a), GPS functionalized (b), and MPS functionalized (c) alumina whiskers.
(a)
(b)
(c)The dissipation factor takes into account both conduction and polarization losses. In our case, considering the relatively low value of the applied electric field intensity, the increase in electrical resistivity with filler content does not sensibly contribute to a reduction oftgδ values with respect to the neat polymer, probably because the effects of deeper trap bands are high-field phenomena. Dissipation factor increases with frequency as shown in Figure 5 since the main contribution is given by polarization losses that are due to molecular friction. The differences at various filler contents are almost negligible.Also in thetgδ spectra we can observe the effects of functionalization which, by stabilizing the adhesion between the filler and the polymer matrix, ensures a more stable behavior of the dissipation factor, with marginal differences among the values measured at different filler content.


## 4. Conclusions

Composite systems based on PBT, containing alumina nanowhiskers, were prepared by batch melt compounding and characterized in terms of morphology and dielectric behavior.Results have confirmed the importance of filler functionalization and distribution within the hosting matrix [50].From a dielectric point of view measurements made by now have indicated that(1)
besides the type of filler functionalization the introduction of a small amount of filler induces a relevant increase of the DC resistivity higher than that in nonfunctionalized systems and essentially ascribed to the creation of new trap bands, deeper than the original trap bands of the base polymer; this behaviour fades by increasing the filler content;(2)
dielectric permittivity is reduced with filler contents up to 3% wt because of usual restrictions of polymer chain movement induced by nanoparticles; it increases at higher filler loadings for the high permittivity of dispersed particles and the onset of interfacial polarization phenomena showing effects ever more pronounced by increasing the applied frequency;(3)
the dissipation factor has minor differences if compared to neat polymer; in any case, it is reduced with respect to the neat matrix for systems with low filler loadings and increases with frequency thus showing a relaxation phenomenon;(4)
functionalization by enhancing the bonding between the nanofillers and the polymer matrix ensures a more stable behavior of the composites as a function of the filler content.



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*Source: 150589-2014-04-02.xml*