From these observations, we conclude that doping can be considered to be the main factor that would cause the lattice distortion of the crystals, for it is usually different from the atomic radius of different elements. As the ZnO is doped with Cs2CO3, the shoulder peak position (the E 2 (high) mode) shifts to 435 cm−1 from 433 cm−1 as shown in Figure 4b. Figure 4c shows the XRD patterns of the ZnO and ZnO:Cs2CO3 thin films deposited on ITO substrates. It is found that the ZnO and ZnO:Cs2CO3

thin layers show peaks corresponding to (100), (002), and (101) planes. All detected peaks match the reported values of the hexagonal ZnO structure with lattice constants a = 3.2374 Å and c = 5.1823 Å; the ratio c/a ~1.60 and this value is indeed Selleck Belinostat in agreement with the ideal value for a hexagonal cell (1.633). The intensity of the peak corresponding to the (002) Selleckchem Semaxanib plane is much stronger than that of the (100) and (101) plane in the pure ZnO as well as ZnO:Cs2CO3 layers. This suggests that the c axis of the grains become uniformly perpendicular to the substrate surface. The XRD pattern of ZnO:Cs2CO3 layer is dominated by the (002) plane, with very high intensity. The highest intensity of the XRD peaks obtained from ZnO:Cs2CO3 film indicates a better crystal quality. One possible reason for such a high intensity is probably the possibility

of heterogeneous nucleation, which is facilitated with the presence of Cs ions in the ZnO structure. It is evident that as the Cs2CO3 doping concentration increases, the lattice parameters ‘a’ and ‘c’ RNA Synthesis inhibitor slightly increase (data not shown). Figure 4d shows the PL spectra of the ZnO and ZnO:Cs2CO3 films excited by 325-nm Xe light at room temperature. The PL spectra of Edoxaban ZnO contain a strong UV band peak at 326 nm and a weak and broad green band located from 400 to 450 nm. The UV emission peak is originated from excitonic recombination, which is related

to the near-band-edge emission of ZnO. Additional weak broad green peak located from 400 to 450 nm refers to a deep-level or trap state emission. The green transition is designated to the singly ionized oxygen vacancy in ZnO and the emission results from the radiative recombination of electron occupying the oxygen vacancy with the photo-generated hole [58]. The strong UV and weak broad green bands imply good crystal surface. The blue shift of the UV emission peak position of ZnO:Cs2CO3 (330 nm) thin film with respect to the ZnO layer is probably caused by the band-filling effect of free carriers. A strong quenching of the UV emissions also indicates that the crystalline ZnO:Cs2CO3 layer contains a large numbers of defects that can trap photogenerated free electron and/or holes. Table 1 tabulates the electrical resistivity of ZnO and ZnO:Cs2CO3 thin films. As shown in Table 1, the resistivity increased from 2.2 × 10−3 to 5.7 × 10−2 ohm cm. ZnO is known as an n-type metal-oxide semiconductor due to the excess Zn or O vacancies.