INTRODUCTION
Zinc oxide (ZnO) is a viable semiconductor compound due to its unique piezoelectric and transparent conducting properties along with high conductivity and better transparency in the visible region, making it a versatile substance. [1]. In addition, ZnO has a wide band gap (3.37 eV) at room temperature and a large exciton binding energy (60 meV), low toxicity, cost-effective, and high conductivity [2-6]. ZnO is an ideal candidate in many energy conversion and optoelectronics applications such as photovoltaics, laser diodes, photo-electrocatalytic, water oxidation, and photocatalytic degradation of organic dyes [7-9]. 
For solar cell applications, various transparent conducting oxides (TCOs) have been identified and utilized over the years due to their suitability. However, the most frequent oxides in the PV area are TCOs, ZnO [10], Indium tin oxide (ITO) [11], and SnO2 [12]. ZnO is considered the most effective TCO material due to its properties and cost-friendly [13]. Further, for the fabrication of ZnO films, several deposition techniques have been successfully employed such as spray pyrolysis [14, 15], chemical bath deposition (CVD) [16], and RF sputtering [17] atomic layer deposition [18]. However, in the past few years, the electrostatic spray deposition (ESD) technique has emerged as a leading method for preparing a variety of functional metal oxide thin films [19-24]. Electrostatic spray coating (ESC) is efficient in the deposition of nanoparticles due to its uniqueness to uniformly charge particles with the same electric polarity, which repels the particles and reduces the chances to form clusters. In addition, ESC offers the benefits of depositing on large surfaces, coating parts with complex geometries, high deposition rate, and can be easily scaled up [25]. In this fabrication technique, the morphology and thickness of the deposited layers can be facilely controlled [26, 27]. 
Electrostatic spray deposition is more advantageous than other conventional mechanical atomizers because of the smaller size of the droplets that can be in range of nanometers. The standard deviation of droplets size helps the formation of uniform layers. Additionally, due to electrical repulsion, the charged droplets are self-dispersing and resulting in the reduction of coagulation. With the help of electric field gradients, the flow of charged droplets can be focused/dispersed on the substrate. As a result, the deposition capacity of charged spray is higher than uncharged droplets such as spin coating, hence, the waste of raw materials will be reduced. Another benefit of ESD is its lower cost than chemical vapor deposition, physical vapor deposition, and sputtering [28, 29]. Similarly, the formation of droplet or spray size obtained using the ESD technique is smaller than other atomization methods which results in a narrower size distribution [30] due to its unipolar charged properties and devoid of aggregation. On the other hand, the relative growth rate of the thin film using ESD is higher than other techniques i.e. CVD or Physical Vapor Deposition (PVD) [28]. This method is also highly reproducible due to the absence of a vacuum apparatus which otherwise can cover a large area [31].
The direct heating of the substrates is one of the main drawbacks of the ESD technique because a set up to heat large substrates consumes more energy, hence decreasing its overall energy efficiency [32]. Further, many researchers deposited ZnO films using EDS in which the substrate’s temperature was recorded as more than 300 ˚C [33-36]. Consequently, due to the heating of the substrate, it has to endure high-temperature deposition processes, while depositing thin films at lower temperatures ensures the maintenance of substrate at a low temperature making its usage possible as a flexible substrate [37]. 
In the present study, an effective and economically viable technique for the fabrication of ZnO thin film at room temperature is investigated. In the precursor solution, because of some limitations on controlling the stoichiometry and high deposition temperatures, a stabled nano colloid was employed for the deposition process. In such studies, the substrate heated up to 400-500 °C. Furthermore, when the heating temperature exceeds 400 °C, oxidation of the film increases in an open atmosphere. Additionally, in this process, green and polar solvents i.e. polyol solvents which are considered green, biocompatible, biodegradable, and sustainable substances, were used to synthesize ZnO nanoparticles by the thermolysis method. In like manner, these solvents allow for excellent control of particle size, size distribution, and agglomeration [38]. In the next step, ethanol was used to prepare nano-colloids by stabilizing nanoparticles in this polar media, while Chen et al. claimed it is difficult to obtain nanostructured thin films by ESD using an alcoholic solution [39]. This high vapor pressure solvent (ethanol) could evaporate at room temperature that is cost-effective and controllable in larger scales or industrial sections. Hence, to achieve this objective, the colloid of nanoparticles was sprayed onto the electrically conductive substrate, which provides a polar interface between ZnO and the substrate to overcome the use of extreme heat during the process with aid of green and low toxic solvents.

MATERIALS AND METHODS
ZnO nanoparticles were synthesized by mixing zinc acetate dihydrate (Zn(O2CCH3)2(H2O)2, Ethylene glycol (EG) (CH2OH)2, 99 %) as the solvent, and polyvinylpyrrolidone (PVP) ((C6H9NO)n, 99.99 %) as the surfactant. Zinc acetate (1.75 mmol) was dissolved in 20 ml of EG with 2% w/v PVP for about 15 minutes at room temperature. In the next step, the transparent solution was stirred at 60 ˚C for 1 hour to form Zinc acetate-PVP complex. With a heating rate of 5 ˚C/min, the solution was heated up to 150 ˚C and was kept for an hour at this temperature.
For the preparation of nano-colloid, 0.0375 g of synthesized nanoparticles dispersed in 10 ml of ethanol. Then the ultrasonication was used for 4 hours to reduce the agglomeration of the nanoparticles. The ZnO nano-colloid was deposited by the electrostatic spray deposition process onto an FTO glass substrate at room temperature (Table 1) for 30 minutes. At 500 ˚C, the thin films were annealed for 30 minutes after the deposition.
Powder X-ray diffraction (XRD) was performed on a GNR X-Ray Explorer with the use of Cu-Kα (1.541 Å) radiation. Dynamic light scattering (DLS) experiment was conducted on Malvern Zetasizer ZS-ZEN3600 red badge. FTIR spectra were conducted Nicolet 6700 FT-IR spectrometers from Thermo scientific. Thermogravimetric analysis (TGA) of ZnO nanoparticles was carried out by using Linseis TGA PT1600. The microstructures and morphologies of the deposited thin films were studied using the TESCAN Vega Model scanning electron microscope. The optical properties of the studied films were determined at room temperature, using a Shimadzu UV-2550 spectrometer. A clean glass substrate was used as a reference for absorption measurements.

RESULTS AND DISCUSSION
Fig. 1. Shows the XRD pattern of synthesized ZnO nanoparticles, which clearly depicts that the hexagonal wurtzite structure with all the diffraction peaks of the formed ZnO nanoparticles can be indexed. It well matches the standard JCPDS Card No. 1-1136 [40]. It is important to note that in the XRD pattern of the synthesized ZnO nanoparticles no impurity phase was detected when this spectrum was compared with the ZnO reference card [41]. The purity of the sample was indicated owing to high sharp intensities in the diffraction pattern and the presence of Miller indices (100), (002) and, (101) [42].
Debye–Scherrer’s equation 1 [43] was used to calculate the average size of crystallite. The normal crystallite dimensions of ZnO were found at the approximate range of 17 nm from the above calculations. 

          
D is the crystallite size, k is the crystallite-shape factor (0.9), λ depicts the X-ray wavelength of 1.5421 Å, β and refer to the width (full-width at half-maximum) of the X-ray diffraction peak in radians and θ is the Bragg’s angle. 
To study the morphology of ZnO nanoparticles, the concentration of PVP is changed. PVP, due to the strong interaction between the O and N atoms in the pyrrolidone and surface of nanoparticles is used as a capping agent [41]. The product sizes and morphologies are impacted by the presence of PVP on different crystallographic planes of nanocrystals [44]. With the increase of PVP on various crystallographic surfaces, a shell forms by PVP around the particles which prevent their aggregation and subsequent increase in size, the diameter of ZnO nanoparticle is reduced because the growth units cannot be deposited on the crystallographic surfaces [45]. The orbitals of the metal ions may be occupied by the polar group of PVP. Further, as the PVP and Zn+2 form a coordinate bond, hence diminishing the concentration of Zn+2 and smaller crystal sizes are obtained [46].
The steric effect of PVP covers the surface of the ZnO nanoparticles via physical and chemical bonds restricting particle-particle contact that prevents agglomeration of nanoparticles inside the spherical aggregates [47].
Fig. 2. shows a structural model for PVP-capped ZnO nanoparticles, the structural models and the orientation are significant factors in determining the conditions under which a stable nano-colloid can be obtained. Three different conditions have been considered to understand the importance of capping agent amounts to prepare a stable colloid. Firstly, in Fig. 2a it observed that in the presence of lesser amounts of capping agent, it would not prevent the ZnO nanoparticles agglomeration because the coating of PVP is not sufficient to rise steric stabilization. According to Fig. 2b to obtain a stable colloid and raise repulsive force between the surfaces the optimum concentration of PVP is required while more than the optimum amount (Fig. 2c) can cause the attraction among their polymeric chains due to the osmotic pressure difference [48].
In this study, the sample with 2% w/v PVP was the most stable colloid because this nano-colloid showed no participation after 21 days based on the observation method. Therefore, the colloid in Fig. 3. is used in the deposition process.
A particle size analyzer was used for obtaining the particle size distribution and the average size of zinc oxide nanoparticles. Fig.4. shows the result for the ZnO nanoparticles sample obtained by DLS According to the graph, at a synthesis temperature of 150 ˚С, the average particle size for the synthesized ZnO was about 60 nm, as shown in Fig. 4. The sizes of the nanoparticles ranged between 50-70 nm.
There are two possibilities based on the calculation of the particle size of ZnO samples using DLS. Firstly, the size of ZnO nanoparticles even after agglomeration was small enough to be in the range of 60 nm. Secondly, the aggregation of nanoparticles prevented by the steric hindrance effect of PVP and stabilized to remain in nano sized.
The size calculated by the DLS test known as hydrodynamic diameter shows the particle’s size in the surrounding dispersant. The Stokes-Einstein equation was used to calculate the size of the particle [49]:

Where: d(H) = hydrodynamic diameter
T= absolute temperature
η= viscosity
D= translational diffusion coefficient
Hydrodynamic diameter value is dependent on the particle core, surface modifications to the particle and the surrounding ions present in the solvent Apart from hydrodynamic diameter and PVP-capped ZnO nanoparticles, the reported ZnO nanoparticles size in this technique is larger due to the bias of the technique toward the measurement of larger particles (or even aggregates). [49-51]. As shown in the Stokes-Einstein equation in low viscosity solvents such as ethanol hydrodynamic diameter will be increased. 
The FTIR spectra of ZnO nanoparticles in Fig. 5. and Table 2 shows absorption peaks at 3388, 2926 cm−1 could be appointed to hydroxyl (OH) groups and CH2 vibration modes of residue EG, not completely removed after the washing procedure [52], 1292 is related to CH2 wagging and C–N stretching peaks of PVP and 1590 cm-1 could correspond to the C=O stretch of PVP [53, 54]. Moreover, the medium to weak bands for pure ZnO at ZnO polymeric hybrid at 889 cm-1 are assigned to the vibrational frequencies due to the change in the microstructural Zn–O lattice. For the presence of C–O, and C–H vibration modes of PVP the peaks were sited at 1050 cm-1 and 1092 cm-1 for ZnO, which acts as a capping agent in the synthesis of nano zinc oxide. The remaining peaks around 1661 cm-1 and 1423 cm-1 for ZnO characteristic peaks are as a result of polymeric O–H stretching vibration of the H2O small amount inside the ZnO nanocrystals [55-57].
The decomposition in the pure PVP can be categorized and divided into two stages. Evident from the differential thermal gravimetric (DTG) Curve shown in Fig. 6. First, one with slight weight loss and lies between 30 and 100 °C can attribute to the evaporation of physically trapped moisture [58, 59]. The burning of organic species present in the precursor powders (organic mass remained from PVP) and the thermal events associated with the chemically bound water which corresponds to a 28% weight loss in the second step shows a significant weight loss that takes place from 100 to 450 °C. Above 500 °C, no further loss in weight and no significant thermal effect were observed, which means that any higher temperature prevents further decomposition [60].
The UV–visible absorbance spectrum is an important technique to evaluate the optical properties of the ZnO nanoparticles. Tauc’s equation [1] was used to measure the optical band gap energy (Eg) of ZnO for direct bad gap semiconductors:

                                                                                  
 
Where absorption coefficient is represented by α, hν indicates the incident photon energy, and A is a constant. These properties have shown in Fig. 7. The spectrum indicates a strong absorption band located at 375 nm and the average band gap estimated from the intercept of the linear portion of the (αhν) 2 vs. hν plots on hν axis [61]. By the extrapolation of the straight-line portion of the plot to the zero absorption coefficient, the band gap energy (eV) is obtained.  As shown in Fig. 7, the band gap value was found to be ~3.28 eV.  
In depositing nano-colloids, the ESD processing parameters have a significant role in thin film formation, the ZnO thin films are prepared at different conditions according to Table 1. based on Fig. 8. At the at a flow rate of 3 μl / min, 8 cm distance from the substrate the SEM image of ZO-L1 showed a relatively smooth surface in comparison with ZO-L2 and ZO-L3, so stable con-jet forms at the voltage of 26 kV, while larger particles were observed on the film surface at the voltages of 24 and 28 kV. As shown in Fig. 9. by increasing the flow rate (ZO-L3>ZO-L4>ZO-L5) from 1 to 3 μl/min, and keeping other processing parameters constant, at the voltage of 26 kV and nozzle to substrate distance of 8cm, the uniformity of the deposited layers has increased. Fig. 10. indicates increasing the nozzle to substrate distances from 6 cm (ZO-L6) to 8 cm (ZO-L1) decreases agglomeration of particles and crack formation on the surface while increasing this distance from ZO-L1 to 10 cm (ZO-L7) larger particles have formed on the film surface.
Fig. 11. represents energy-dispersive X-ray spectroscopy (EDS) of ZnO thin film. As shown in Fig. 11b, the elements in the deposited thin film were confirmed by EDX. With regards to the atomic mass (Fig. 11a), the elemental composition of Zn, O, Au, and Sn in the thin film was 10%, 65%, 14.18%, and 9.99%, respectively. Gold has been used as a conductive coating of the sample as indicated by the presence of Au in the peak, while the presence of Sn is related to the FTO glass.
Cross sections of ZO-L1 and ZO-L7 are shown in Fig. 12. According to this figure, there is a difference in roughness between ZO-L1 and ZO-L7. It shows that the roughness of ZO-L1 is lower than that of ZO-L7. However, it is observed that the thickness of the deposited thin films is less than 400 nm in both conditions.The spectroscopy features of ZnO nanoparticles were measured using UV–visible absorption spectrophotometer. Fig. 13 shows the ZnO thin film’s optical properties prior to and after the heat treatment at 500 ˚C. This reveals that the films have good quality with a sharp absorption edge. The absorption edges for the ZO-L1 and ZO-L7 are located at 360 and 370 nm respectively, which have shifted to 345 and 355 nm for the annealed samples. It is also noticeable after annealing at 500 ˚C shows maximum absorption of the thin films at a larger wavelength is higher because the surfaces became homogenous and defects density decreased [62].

CONCLUSION
As from the above discussions and observations, the hexagonal wurtzite structure with a high degree of crystallinity was shown by the XRD pattern of synthesized ZnO nanoparticles along. Based on DLS results at a synthesis temperature of 150 ˚C, the average particle size for the synthesized ZnO nanoparticles was 60 nm. According to SEM characterizations of the deposited thin films, the voltage of 26 kV, the flow rate of 3 μl/min, and nozzle to substrate distance of 8 cm were observed as optimized deposition conditions. The ZnO nanoparticle’s direct optical band gap was around 3.28 eV as shown by the UV visible absorption spectroscopy. In the wavelength larger than 345-350 nm, the maximum absorption of the annealed thin films has blue shifts because of the homogenous surface and low defect density.

CONFLICT OF INTEREST
The authors declare that there is no conflict of interests regarding the publication of this manuscript.