INTRODUCTION 
Several technologies are currently used to reduce materials into nano-sizes and nano-thickness, resulting in the emergence of new and unique behaviors [1-5]. There are several ways that thin films differ from bulk materials with the same chemical composition due to their high surface-to-volume ratios [6-8]. It should be noted that all materials, such as thin films, are either amorphous or polycrystalline depending on the preparation conditions and material characteristics [9, 10]. Thin films consist of two parts: the layer under the film and the substrate [11]. Many electronic devices rely on semiconductor materials, which include silicon, gallium arsenide, and cadmium sulfide [12-15]. A strong absorption in Cadmium Sulphide has attracted researchers because it is used in the fabrication of optoelectronic and photoconductive devices. The band gap of CdS is about 2.42 eV to 2.5 eV at room temperature [16, 17]. It is possible to grow CdS films in both hexagonal (wurtzite) and cubic (zinc blende) phases [18, 19]. Cadmium sulfide thin films are suitable for the window layer of CdTe/CdS heterojunction solar cells. Highly efficient solar cells require uniform and transparent CdS thin films [20-22]. Among the properties that depend on size are: melting point at 400 °C at 2.5 nm, phase transformation at a high pressure from wurtzite to rock salt cubic phase.  CdS thin films have been prepared through a variety of methods, including chemical bath deposition, vacuum evaporation, thermal evaporation, RF sputtering, electron beam evaporation, and pulsed laser deposition. Scientists conduct research on doped CdS thin films because of their significant merits with regard to self-quenching, sufficient thermal and photochemical features, and larger Stokes shift [16, 23].
F.T. Munna et al. prepared zinc-doped cadmium sulfide thin films via chemical bath deposition-grown. Thiourea (NH2SCNH2) and N-methylthiourea (NH2CSNHCH3) were applied as a sulfur source. The impact of Zn2+ doping on as-grown CdS films was investigated. The optical transmittance increases as the zinc content rises, according to the findings. As a sulphur source, thiourea has an optical bandgap of 2.35 eV to 2.45 eV, and N-methylthiourea has a bandgap of 2.2 eV to 2.4 eV [24]. 
In another work, the CdS thin films were prepared by close spaced sublimation at a temperature of 550°C under vacuum for varying periods of time. For Cu doping of as-deposited thin films, copper nitrate solution was immersed in an 80 ± 5 °C solution for various durations. It is found with increasing copper immersion time, copper transmittance falls from 80% to 30% [25].
In this study, copper doped CdS thin films  was synthesized via  pyrolysis procedure strategy. The morphological, optical and electrical properties of the as-prepared thin films  were characterized comprehensively. The effect of copper on the physical properties of cadmium sulfide thin film was investigated. 
 
 MATERIALS AND METHODS 
    Cu-doped CdS was grown using the simple and fast chemical procedure. Cadmium chloride (CdCl2) (Supplied from BDH Chemicals, UK) and thiourea [(NH2)2 CdS] (provided from Merck Chemicals, India) were dissolved in distilled water to prepare CdS  thin films  grown on glass substrate and then heated at 450 oC. The copper chloride (provided from TCI Chemicals, India) was added to this system with 2% and 4% as a dopant for providing CdS:Cu thin film. The optimum conditions were applied as following; spraying rate was 5 ml/min, distance between spout and substrate was around 29 cm, showering rate was adjusted 9 s followed by 2 min hold back to maintain a strategic distance from over the top substrate cooling and transporter gas was Nitrogen. The got films were adherent, free  from pinholes and with sensible film homogeneity.  Films thicknesses were measured by gravimetric strategy and was in the scope of 325 ± 30 nm. The basic properties of CdS:Cu thin films were done utilizing X-ray  diffractometer. Surface geography of the as kept films was acquired by AFM (AA 3000 Scanning Probe Microscope). The UV–Vis spectrophotometer (SHIMADZU UV-2450) was utilized to investigation the optical properties at the range of 200–800 nm.

RESULT AND DISCUSSION
Fig. 1, displays the XRD of the prepared films. A peak situated at 36.79o attributed to the (101) plane of the hexagonal structure. With additional expanding in the statement at doping in 2% and 4% CdS: Cu, the peak identified with the plane (101) became better and extreme. These outcomes in concurrence with the standard CdS X-ray diffraction information document [No. 43-089 JCPDS prevalent]. The hexagonal particular direction (101), as for our situation, has been accounted for CdS thin films grown by pyrolysis. 
The crystallite size (D) was determined utilizing Debye-Scherrer formula:

(1)
  
 
(2)

(3)

while, the separation thickness boundary diminished from 2.69 to 2.32, the strain (%) boundary diminished from 6.02 to 4.49 with Cu fixation as recorded in Table. 1 
Fig. 2  shows the FWHM, Grain size, Dislocation thickness and Strain of the prepared films. The crystallite sizes were increased via increasing Cu content in prepared thin films.
Fig. 3 shows three dimensional AFM micrograph of the CdS  thin films. The images show all around characterized molecule like highlights with granular morphology and demonstrate the presence of little translucent grains. The AFM analysis additionally revealed a homogeneous structure of films with no breaks and is constant with all around associated grains. Table 2 shows the estimations of normal harshness and root mean square surface roughness  (RMS) of as kept and strengthened films. The results were in good agreement with Hasoon et. al. [48]. As can be seen the Cu doping can be have a significant effects on the roughness average and RMS. The surface morphology of the samples has been studied by utilizing nuclear power magnifying lens (AFM). The grain size of the nanoparticles was showed in the scope of 66.26, 57.11 and 56.52 nm for the (CdS, CdS :2% Cu, CdS :4% Cu) respectively. The Rrms estimation of 3.86 nm for as kept CdS thin films diminished to 1.66 nm by diminished of doping, Ra roughness  boundaries as a component of dopant fixation were given in Fig. 3 (a3, b3,and c3) separately. Table 2 represents the estimations of AFM parameters.
The transmission spectra of as-obtained products have  appeared in Fig. 4. It was revealed that the transmission shifted from 80 to 95% in visible region. Accordingly, CdS is considered as a glass material for the obvious just as the infrared region. 
The absorption  coefficient (α) was determined from equation  : 
α = (2.303×A)/t (4)

Where (t) is film thickness, A is absorbance. Fig. 5 confirmed that α diminished with an increasing at 2% or 4% doping. 
  The optical band gap was calculated for pure CdS and doped thin films by: 

(αhν)=A(hν-Eg )(1/2)    (5)

 Where A is constant, Eg is the energy  gap , hν is photon energy. The optical band gap  can be acquired by extra plotting the direct bit of the plot (αhν)2 versus hν. The bandgap estimation was estimated from the plot (αhν)2 against hν as appeared in Fig. 6. As well as shown, the optical band gap were determined as 2.42, 2.36, and 2.31 eV for pure CdS, 2%Cu-doped CdS, and 4%Cu-doped CdS respectively.
 
CONCLUSION 
In this work, the CdS films were prepared via various Cu dopants via simple and fast chemical route. XRD analysis confirmed that obtained thin films have hexagonal structure with the particular direction along the plane (101). structural examinations demonstrated that normal grain size increased from 12.88 nm to 14.92 nm with increment in Cu content in thin films (CdS, CdS :2% Cu, CdS :4% Cu). The surface morphology has been studied by utilizing nuclear power magnifying lens (AFM). The grain size of the nanoparticles were calculated 66.26, 57.11, and 56.52 nm for the CdS, CdS :2% Cu, CdS :4% Cu respectively.  The transmittance spectra have been recorded, which indicated that the absorption edges of CdS  thin film  varied at various Cu doping. The calculated optical band gap has been decreased from 2.42 to 2.31 eV via Cu doping.

ACKNOWLEDGMENTS 
   This work was supported by Mustansiriyah University (www. uomustansiriyah.edu.iq), College of Education, Baghdad, Iraq. 

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