Nowadays, semiconducting organic materials are very important since they have successful application in optical and electronic devices. One of these materials is Phthalocyanines (Pcs); it has significant properties which made it a good alternative for development electronic devices. These materials have been used in the gas sensor and in electronic devices because it possesses many advantageous properties such as thermal, chemical and photochemical stability, excellent film growth and good optical and electronic properties  . Their thermally stable nature makes them suitable for thin film deposition by thermal sublimation. These materials have also shown promise for photoconductive and photovoltaic response  . Phthalocyanines are a class of planar aromatic organic compounds that have attracted a great deal of attention for quite some time because of their unique properties such assemiconductivity, photoconductivity, photochemical reactivity, chemical stability, electrochromism, bio-organic and catalytic activity and their application in the field of colour display technology and gas sensors. The electrical, optical and structural properties of phthalocyanine thin films depend on different parameters such as evaporation rate, substrate temperature and post-deposition annealing   . In addition to their excellent photoconductive properties, Pc-s have the advantages of being very stable against thermal and chemical decomposition and present very intenseoptical absorption in the visible region. These properties similarity to chlorophyll have many applications in solar cell. Also, they have the potential to serve as active material for molecular electronic devices such as electrochromic displays, chemical sensors and optical data storage. Furthermore, interests in Pc compounds have recently been renewed due to the discovery that they form molecular metals after partial oxidation  . The physical properties of thin films materials depend very much on the structure properties; therefore, they have always high priority. The knowledge of the composition of the film is important to understand and predict the nature of the films  . Thin films of Phthalocyanines are chemically and thermally durable and are prepared by vacuum thermal evaporation    . NiPc is thermally stable and its thin film can be deposited by thermal evaporation without dissociation   . A number of analytic techniques are available for the composition characterization of thin films. These include X-ray diffraction studies, AFM and electrical studies. The objective of this paper is to study the effect of thickness on the structural, compositional and electrical studies of Nickel phthalocyanine (NiPc) thin films prepared by vacuum evaporation technique.
Nickel phthalocyanine thin films, with thickness (50, 110, 265 and 350) nm, were deposited on cleaned glass substrate (type corning, China) with dimensions (7.5 × 2.5 × 0.1) cm by thermal evaporation technique (Edwaed coating unit model 306 A) under high vacuum with pressure of (6 × 10−5) mbar with deposition rate of about 20 nm/min. A molybdenum boat was used as a source for the evaporation of the material. Set a distance of 15cm to separate the substrate and the boats. The films were characterized by X-ray diffraction technique using (Philips X-ray diffractometer) with CuK α radiation at wavelength (1.5406) A˚. Atomic force microscopy was used to determine the roughness snd surface morphology of films. Digital electrometer type Keithly 616 and electrical oven have been used for electrical measurements. The Hall coefficient (RH), carrier type and Hall mobility (µH) of films were measured by the circuit contain D.C power supply (0 - 40) V and two digital electrometers (Keithley type 616 to measure the current and voltage
3. Results and Discussion
3.1. X-Ray Diffraction XRD
X-ray diffraction pattern of NiPc thin film with different thickness (50, 110, 265 and 350) nm are shown in Figure 1 respectively. XRD pattern indicates that all the samples are single crystal and that it has β-crystalline phase  . The difference between α- and β-phases is attributed to the tilt angle of b-axis of the unit cell. The structure of the NiPc thin film is determined as tetragonal with preferential orientation along the (100) direction. Well-defined diffraction peaks by (100) give the direction of the preferential orientation as deposited film (JCPDS, file No. 11-0744). The diffraction peaks are agreement with the previous observations  -  . The spacing between the planes (d) has been calculated using the Bragg’s formula:
as shown in Table 1. The d values obtained from diffractogram are in agreement with JCPDS record. The differences in the d values are attributed to higher X-ray absorption, sample purity, particle size, preferred orientation and crystal texture   . Table 1 shows the structure parameters of NiPc films, The full width at half maximum (FWHM) intensity of preferential orientation, shows that the FWHM are reduced with increasing thickness except at thickness 350 nm its increased, which means re arrangement the lattice structure and fill all dangling bind and eliminate the defect    and then its increased due to create a localized state at 350 nm. From the Table 1 it is observed that the grain size increases which intern decreases strain and dislocation density. The grain size D of the film is calculated using the Scherrer relation
where k = 0.94 is a constant, —the wavelength of x-ray, β—the full width half maximum and θ—the diffraction angle, the grain size increases from (20.85 - 33.5 nm) for thickness (50 - 265 nm) and then decreased to 23.2 at 350 nm as in Figure 2, and this may be attributed to enhancement and re-crystallization these films by increasing the thickness. And the decreasing in grain size at 350 may be attributed to create a localized state by increasing thickness. The intensities of other planes have disappeared. The XRD spectra also shows a little shifting towards lower diffraction angle for (100) plane normally which means greater spacement between atoms which according to Brag equation. The sample which has thickness 265 nm is the lowest FWHM which means the greatest grain size according to Scherrer equation.
The dislocation density δ defined as the length of dislocation lines per unit volume of the crystal and can be evaluated from the particle size D by the relation  .
Figure 1. X-ray diffraction of the NiPc thin films with deferent thicknesses.
Figure 2. Grain size with thickness of NiPc thin films.
Table 1. X-ray diffraction parameters of the NiPc thin films with deferent thicknesses.
where n is a factor, when equal unity giving minimum dislocation density. The microstrain is related to the lattice misfit, which in order depends on the deposition conditions. The microstrain ε is calculated using the relation  :
Figure 2 and Figure 3 represent the grain size and dislocation density δ and the microstrain ε of prepared thin films evaporated with different thicknesses on glass substrates. It was observed that the dislocation density and microstrain exhibit a decreasing trend with the deposition thin film thickness (except at 350 nm) which represents better lattice quality.
3.2. Surface Morphology
Atomic Force Microscope
This section of studies includes the effect of thickness on the morphology of prepared films were determined by Atomic Force Microscope with different thickness (50, 110, 265 and 350) nm taken in an area of 10 × 10 μm2 as shown in Figure 4. It is observed from the figure that the morphology of these films was uniform surface with clear grain boundaries and growth of crystal and the grain size increases from 48.33 - 203.28 nm with increasing thickness from 50 - 265 nm except at thickness 350 nm its decreased to 91.25 nm as in Figure 4 and Table 2, and it's decreased at 350 nm and this is agreement with the results of XRD. Also the typical topography of a polycrystal is observed, where each grain can be clearly individualized. Differences in the height of the grains can also be observed, as well as a visible dispersion of the grain size. It is observed that at 350 of thickness, the grains are somewhat smoothed out. The roughness (rms) of films at different thickness is given in Table 2. It is observed that the roughness increase with thickness increase, and this is agreement with other researchers    .
Figure 3. δ and ε with thickness of NiPc thin films.
Figure 4. 3-D AFM images of NiPc thin films with different thicknesses.
Table 2. Grain size and average roughness of NiPc thin films by AFM technique.
The electrical conductivity of NiPc thin films was performed to determine the thermal activation energy. Measurements were carried out in the temperature range 303 to 473 K for films with different thickness ranging from 50 to 350 nm. The temperature dependence of the conductivity can be expressed by Arrhenius equation.  :
where ΔE is the thermal activation energy and kB is the Boltazmann’s constant. A plot of against (1000/T) yields a straight line whose slope can be used to determine the thermal activation energy of the film. Figure 5 shows the dependence of the dark electrical conductivity of as-deposited NiPc films of different thickness on the temperature. Film thickness is one of the most important parameters which affects the physical properties of the films. As seen from the
Figure 5. Lnσ as a function of (1000/T) of NiPc thin films for different thicknesses.
figure, there are three semiconductor distinct linear parts, which correspond to three activation energies ΔE1, ΔE2 and ΔE3. ΔE1 corresponds to extrinsic region and represents transition process for carriers within localized states in the energy gap and this suggests the existence of high density of localized states in the energy gap, and ΔE2 and ΔE3 corresponds to intrinsic region and represents the carriers transport across the grain boundaries by thermal excitation. The change in the slope and hence the activation energy is interpreted as a change from extrinsic to intrinsic conduction  . The value of the thermal activation energy ΔE1, ΔE2 and ΔE3 is shown in Table 3, which is in good agreement with those obtained by other workers   . The room temperature conductivity increases as the thickness increases and this is attributed to the change in the degree of crystallinity. Also, as given in Figure 6, the activation energy varies as the thickness increases and this is because of the improved crystallinity with the increase of the grain size.
3.3. Hall Effect
Carrier concentration and Hall mobility have been determined from Hall measurements for NiPc thin films, having different thicknesses which were deposited on glass substrates at 300 K. The Carrier concentration (n) is determined for all film thicknesses and it is of p-type. Hall coefficient (RH) was calculated, then carrier concentration has been calculated for each thickness and it was of p-type. Carrier mobility was determined for each thickness. All these parameters are shown in Table 4. It can be inferred from the Table that carrier mobility increases with the decrease of the carrier concentration and varies with the increase of film thickness. This is consistent with the work of researchers  .
Table 3. Values of activation energies and conductivity for NiPc thin films with different thicknesses.
Table 4. Values of carrier concentration and carrier mobility for NiPc thin films with different thicknesses.
Figure 6. Effect of NiPc thin films thickness on activation energy.
Thin films of Ni-Pc were prepared by the thermal evaporation method on glass substrates with different thickness successfully. From the x-ray diffraction studies, it is observed that the structure is single crystalline β-phase film-oriented preferentially (100) plane for all thickness. The structure properties are found to be very sensitive to the thickness of thin film. The grain size increases with increasing thickness. The change in grain size shows that the properties of NiPc are controlled by its structure and morphology depending on increases the thickness. The surface morphology of prepared films and the crystal morphology vary with thickness. From the electrical properties measurements, there are three semiconductor distinct linear parts, which correspond to three activation energies ΔE1, ΔE2 and ΔE3. ΔE1 corresponds to extrinsic region and ΔE2 and ΔE3 correspond to intrinsic region. Hall effect measurements show that all the films are p-type. The carrier mobility increases with the decrease of the carrier concentration and varies with the increase of film thickness.