The inorganic nanoparticles doping into the polymer matrix can provide high-performance novel materials that find applications in many industrial fields. As a result of the development in nanotechnology, inorganic nanostructured materials have been designed/discovered and fabricated with important cooperative physical phenomena such as super paramagnetism, size-dependent band-gap, ferromagnetism, electron and phonon transport. Yet, they typically suffer from high manufacture expense, and the shaping and further processing of these materials is often difficult and demanding or impossible .
Polymers, on the other hand, are flexible lightweight materials and can be produced at a low cost. They are also known to allow easy processing and can be shaped into thin films by various techniques such as dip-coating, spin-coating, film-casting, and printing. Polymers are already widely used in the optoelectronics industry and are playing important roles in various applications.
Therefore, the drawbacks of using inorganic nanostructured materials can be overcome by employing a polymer matrix to embed a relatively small content of inorganic nanoparticles. The integration of inorganic nanoparticles into a polymer matrix allows both properties from inorganic nanoparticles and polymer to be combined/ enhanced and thus advanced new functions can be generated to the polymer-inorganic nanocomposites PINCs. The PINCs are one kind of composite materials comprising of nanometer-sized inorganic nanoparticles, typically in the range of 1-100 nm, which are uniformly dispersed in and fixed to a polymer matrix. Nanoparticles filled polymers provide advantages over micron-filled polymers because they provide resistance to degradation  and improvement in thermo-mechanical properties without causing a reduction in dielectric Strength. Also, recently published results for electrical voltage endurance in these new materials indicate that very substantial improvements in voltage endurance can be demonstrated. These improvements in dielectric properties observed for nano-filled polymers could be due to several factors: (i) the large surface area of nanoparticles which creates a large 'interaction zone' or region of altered polymer behavior , (ii) changes in the polymer morphology due to the surfaces of particles , (iii) a reduction in the internal field caused by the decrease in size of the particles, (iv) changes in the space charge distribution [5-6], and (v) a scattering mechanism. It should also be recognized that this technology also results in characteristic changes in non-electrical properties . In this way, the inorganic nanoparticles are acting like 'additives' to enhance polymer performance and thus are also termed 'nano-fillers' or 'nano-inclusions' [8-9]. Twenty years ago, the term 'nanocomposites' was not popular and 'hybrid' or 'molecular composite' were used instead . In that time, inorganic fillers had already been used as additives for polymers to enhance mechanical, thermal, and chemical stability. However, traditional fillers were often in micron size and did not possess the superior properties of nanoparticles.
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Recently, the polymer inorganic nanocomposites with high dielectric permittivity have been considered to be potential candidates for integration into electronic devices. Owing to the continuous development towards the miniaturization of electronics, newer dielectric materials were sought which would enable to achieve high energy density for capacitor applications. Ceramics possessing very high dielectric permittivity are being used as voltage capacitors due to their high breakdown voltages. However, they are brittle, suffer from poor mechanical strength and hence cannot be exposed to high fields. Polymer films such as polyester, polycarbonate, polypropylene, polystyrene, polyethylene sulphide and recently polyvinyl acetal  are being used in the fabrication of low leakage capacitors. Though polymers possess relatively low dielectric permittivity, they can withstand high fields, are flexible and easy to process. By combining the advantages of both, one can fabricate new hybrid materials with high dielectric permittivity, and high breakdown voltages to achieve high volume efficiency and energy storage density for applications in capacitors as electric energy storage devices [12-19]. This study aims the achievement of ZnO nanostructures in the reaction temperature of 70Â°C by the solochemical method using zinc nitrate hexahydrate (Zn(NO3)2.6H2O) and sodium hydroxide (NaOH). The product obtained was characterized by X-ray diffraction (XRD) technique method. The morphology and size of the ZnO was investigated with AFM and SEM. Among the nanomaterials with industrial relevance stands out zinc oxide (ZnO), an n type semiconductor that displays a hexagonal crystalline wurtzite-type structure, with space group P63 mc and lattice parameters of a = b = 0.3250 nm and c = 0.5207 nm . The importance of ZnO is due to its unusual physical properties such as high conductance, chemical and thermal stability, wide and direct band gap of 3.37 eV , and a high excitation binding energy of 60 M eV  Moreover, it has good radiation resistance , and is harmless to the environment . The ZnO nanostructures has great potentiality for being used in preparing solar cell, acoustic, electrical and optical devices, chemical sensors , catalysts, pigments, cosmetics, varistors and gas sensors .
2. Experimental Section
2.1. Synthesis of ZnO nanoparticles:
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All the reagents used in this experiment, NaOH and Zn(NO3)â‚‚.6H2O, were of analytical grade from Aldrich and were used without any further purification. In two liter beaker NaOH was dissolved in deionized water to a concentration of (1.0 M, 250mL) and the resulting solution was heated, under constant stirring, to the temperature of 70Â°C. After achieving this temperature, one milliliter from commercial dodecyl sulfate anionic surfactants added and then from a burette the solution of (0.5 M, 100mL) Zn(NO3)â‚‚.6H2O was for 120 minutes dripped into the two liter beaker containing the NaOH aqueous solution under continual stirring. In this procedure the reaction temperature was constantly maintained in 70Â°C. The suspension formed with the dropping of 0.5 M Zn(NO3)â‚‚.6H2O solution to the alkaline aqueous solution was kept stirred for two hours in the temperature of 70Â°C. The material formed was filtered and washed several times with deionized water . The washed sample was dried at 65Â°C in oven for several hours. The yield of the ZnO nanostructures by this method is about 92%. The dry ZnO nanoparticles examined with XRD (Shimadzu XRD-6000) with copper radiation (Cu KÎ±, 1.5406 Å), the prepared nanoparticles size and morphology were also observed with Atomic Force Microscopy (AFM) and Scanning Electron Microscope (SEM).
2.2 Synthesis of Poly 4-methyl benzyledene vinyl alcohol (poly (vinyl acetal)) compound:
All chemicals used in the preparation are from Sigma-Aldrich. The preparation procedure of poly (vinyl acetal) compound was based on the work of Ichiro Sakurada . PVA (Mw. = 12000 g, 0.5g) and 4-methyl benzaldehyde (10 m mol, 12g) was dissolved in mixture of benzene (24 mL) and ethanol (6 mL) with 2 drops of HCl. the reaction mixture was left stirring vigorously at (40-50Â°C) for 24 h. the solution was poured into excess of methanol (100 mL) containing equimolar amount of NaOH, the product was separated by filtration and then washed with methanol and dried in vacuum. The yield of the product was 80%.
Poly 4-methyl benzyledene vinyl alcohol
2.3. Poly 4-methyl benzyledene vinyl alcohol -PVA with ZnO nanocomposites film fabrication:
Four polymer composite films were prepared and the composition percentage are shown in table (1), each portion dissolved in 20 mL DMF and mixed completely under constant stirring for one hour while the mixture was heated up till 50Â° C then the mixture was let to cool down to room temperature (24Â°C) with stirring of the mixture was carried out to ensure a homogenous composition.
The obtained Poly (vinyl acetal) / PVA composition was mixed ultrasonically with ZnO nanoparticles as shown in table (1) for (15-25) minutes. To cast the films, the above mixtures were poured in a casting glass plate 5x5 cm and let it dry at room temperature for 140 hours. At the expiry of this time, the films were ready which were peeled off the casting glass plate.
2.4. Dielectric constant measurements:
The above fabricated films were cut into 2x1.5 cm pieces to fit a homemade silver electrode for characterization by measuring dielectric properties using Precision LCR meter HP 4274 A connected with HP 4275 A and Test Fixture HP 16047 A at frequency range 100 Hz to 10âµ Hz .
Table1. The compositions of the prepared films
Poly(vinyl acetal) g/film
ZnO g% /film
3. Result and Discussion
3.1.Poly 4-methyl benzyledene vinyl alcohol characterization:
The IR spectrum of Poly 4-methyl benzyledene vinyl alcohol show an absorption band in the region ( 3200-3500) cmË‰Â¹ due to the stretching vibration of unacetalized (OH) group of (PVA), absorption band at (3050)cmË‰Â¹ and at (2950-2850)cmË‰Â¹ attributed to (C-H) aliphatic and aromatic stretching vibration and absorption band in the region (1250-1150) cmË‰Â¹ for (C-O-C cyclic ether ) stretching vibration .A medium absorption band at (840)cmË‰Â¹ attributed to the out of plane bending vibration of 1,4-substituted benzene ring is also appeared. The melting point was 385Â°C which investigated with a hot stage polarizing microscope (Olympus BX51M).
Figure 1: IR spectrum of poly-4-methyl benzyledene vinyl alcohol.
3.2. ZnO nanoparticles characterization:
3.2.1. Structural Properties study:
Atomic Force Microscope (AFM) and Scanning Electron Microscope (SEM):
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The Atomic Force Microscope (AFM) figure (2: a-b) show two and three dimensional histogram respectively, represent ZnO nanoparticles, their typical diameter was less than (41.7 nm). The particle size histogram was performed and shown the particles which are to a large extent well-separated from one another throughout the field of the micrograph and agreed with SEM micrograph Figure (2: C)and show spherical ZnO nanoparticles.
Figure2:A. Represent the AFM 2-D image with maximum high (40 nm) of the ZnO nanoparticles.
Figure2: B. Represent the AFM 3-D image with maximum high (40.7 nm) of the ZnO nanoparticles.
Figure 2: C. Represent the Scanning Electron Micrographs of the synthesized ZnO nanoparticles.
X- Ray Diffraction (XRD):
The XRD spectra of ZnO nanoparticles are shown in Fig. 3, a series of characteristic peaks: 2.8112(100), 2.5996(002), 2.4702(101), 1.9092(102), 1.6239(110), 1.4763(103), 1.4060(200), 1.3777(112) and 1.3590(201) are observed, and they are in accordance with the ZnO (International Center for Diffraction Data, JCPDS 5-0664). No peaks of impurity are observed, suggesting that the high purity ZnO was obtained. In addition, the peak is widened implying that the particle size is very small according to the Debye-Scherrer formula :
Where K is the Scherrer constant taken as 0.94, Î» the X-ray wavelength (CuKÎ± = 0.15406 nm), B the peak width of half-maximum, and Î¸ is the Bragg diffraction angle. The average crystallite size D is 41Â±1 nm calculated using the Debye-Scherrer formula.
Figure 3: XRD pattern of ZnO nanoparticles powder.
3.3. Dielectric Permittivity Study:
The dielectric parameter as a function of frequency is described by the complex permittivity
Where the real part and imaginary partâ€³ are the components for the energy storage and energy loss, respectively, in each cycle of the electric field. The measured capacitance, C was used to calculate the dielectric constant, using the following expression.
Where d is the thickness between the two electrodes, A is the area of the electrodes, âˆ˜ is permittivity of the free space, âˆ˜ = 8.85x 10Ë‰Â¹Â² F/m and is the angular frequency;
is applied frequency, where d is sample thickness and A is surface area of the sample.
Whereas for dielectric loss, " and is tangent delta :
Figure 4: Relative permittivity of PVA- poly vinyl acetal composite at different concentration of ZnO nano particles.
The electric modulus is the reciprocal of the permittivity in complex form  was found using
eq. No. (5):
Where MÂ´ and M" are the real and imaginary part of dielectric modulus and it was calculated by Eq. No. (6and 7):
From the imaginary part of electrical modulus, M", the relaxation time Ï„ of the orientation of
Dipoles can be obtained. The peak for angular frequency, can be obtained from the graph
M" versus log frequency .
In figure 4. the real permittivity slope variations with respect to frequency can be considered to be very minimal since the nanocomposite permittivity slope is almost the same as that of pure of PVA-Acetal composite polymer films in frequency rang more than 3,5x10Â³ Hz, but at frequencies less than 3.5x10Â³ Hz, there is a noticeable change in the permittivity slope, this observation of the steepness in the permittivity slope at frequencies lower than 3.5x10Â³ Hz is due to the influence of ZnO filler nanoparticles.
The dielectric properties of materials are mainly determined by their polarizabilities at a given frequency. For multicomponent systems, when free charge carriers migrate through the material, space charges build up at the interfaces of the constituents owing to the mismatch of the conductivities and dielectric constants of the materials at the interfaces. This is called interfacial polarization
Figure 5: Imaginary permittivity of PVA- poly vinyl acetal composite at different concentration of ZnO nano particles
The interfacial polarization in polymers having structural inhomogeneities (e.g., nanoparticles) can be identified by low-frequency ( 10Â²-10âµ Hz) dielectric measurement based on Maxwell-Wagner-Sillar's polarization and the changes in the permittivity values as a function of frequency are attributed to dielectric relaxations. These are more pronounced at low frequencies due to micro-Brownian motion of the whole chain (segmental movement), which exists in heterogeneous dielectric materials and is produced by the traveling of charge carriers [32, 33]. In order to study the frequency and the different concentrations of fillers dependence of relaxation processes, effective permittivity was used Figure (4and 5) shows the real and imaginary part of permittivity respectively obtained through Equations (1-3).
The dielectric permittivity as depicted in figure 4 and figure 5 decreases with the increasing of frequency. This may be attributed to the tendency of dipoles in polymeric samples to orient themselves in the direction of the applied field. However at the frequency range (4x10â´- 1x10âµ), no decrease seems as compared for lower frequency region. This trend is observed for these graphs for different concentration of dopants. It could be explained by dipoles orientation, which difficult to rotate at high frequency range. On the other hand, the high value of â„‡Ë‰ at low frequency might be due to the electrode effect and interfacial effect of the sample [34, 35]. Moreover, PVA exhibits flexible polar side groups with polar bond as the bond rotating having intense dielectric transition. and the electrical modulus was used Figures No. (6 and 7) shows the real and imaginary parts of the electrical modulus respectively obtained through Equations No.(5-7) as a function of frequency . The value at frequency region (below 4x10Â³ Hz for real modulus and 0.4x10Â³ Hz for imaginary modulus) indicates the removal of electrode polarization , and the two figures show the calculated value of real and imaginary part of electrical Modulus respectively for composite films at different concentration of dopants. In figure No.(7) the peaks were shifted-up to higher frequency with the increasing of ZnO nanoparticles concentrations, it also shows that the height of the peaks proportional to the ZnO nanoparticles concentration and as relaxation time decreases. Note that the frequency at the maximum of the peak of M" show the the relaxation frequency,( as tabulated in the inset figure No. (7)). Table 2 shows the relaxation time, Ï„ for poly (vinyl acetal)/PVA composite doped with ZnO nanoparticles at different concentration of the dopants. The relaxation times were obtained (eq.No.8). From the whole data, one can conclude that with the increasing amount of the ZnO nanoparticles, the relaxation time is relatively reduced. These results confirm the explanation for the dielectric constant and dielectric loss characteristics as relaxation times decreases with the increasing composition of the ZnO nanoparticles, which were effected on interfacial polarization, since relaxation processes were influenced by the interfacial polarization effect which generated electric charge accumulation around the ZnO nanoparticles and the displacement of peak as the particle content increased and this is identify with work of Tsangaris G, et.al .
Figure 6: Real dielectric modulus of PVA- poly acetal composite at different concentration of ZnO nano particles.
Figure 7: Imaginary dielectric modulus of PVA - Acetal composite polymer films at different ZnO nanoparticles.
Table 2: Relaxation time, Ï„ for Poly 4-methyl benzyledene vinyl alcohol -PVA composite polymer with ZnO nanoparticles films
ZnO concentration %
Ï„ relaxation time ( Hz )
1.28 x 10Ë‰â¸
7.81 x 10Ë‰â¹
1.75 x 10Ë‰â¸
1.33 x 10Ë‰â¸
The present communication shows that the ZnO nanoparticles composition has great influence on the trend and magnitude of dielectric properties. The results also show that the Poly 4-methyl benzyledene vinyl alcohol/PVA composite polymer films have both electric and electronic properties. The composite polymer films exhibit the combination of intrinsic dielectric anisotropy as a result of the competition of free charges. Relaxation times become shorter as the composition of ZnO nanoparticles is increased indicates that multiple path of the system to be relaxed due to high availability of free charges.
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