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Significance of substrate temperatures on the deposition of ZnGa2Se4 thin films by flash evaporation technique
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1.
International Research Journal
of Engineering and Technology (IRJET) e-ISSN: 2395 -0056 Volume: 04 Issue: 03 | March -2017 www.irjet.net p-ISSN: 2395-0072 © 2017, IRJET | Impact Factor value: 5.181 | ISO 9001:2008 Certified Journal | Page 253 Significance of substrate temperatures on the deposition of ZnGa2Se4 thin films by flash evaporation technique V. D. Dhamecha*1, B. H. Patel1, P. B. Patel1 and V. A. Patel2 1 Department of Electronics, Sardar Patel University, Vallabh Vidyanagar 388120, Gujarat, India 2 SICART-CVM, DST Sponsored Research Centre, Vallabh Vidyanagar 388120, Gujarat, India ---------------------------------------------------------------------***--------------------------------------------------------------------- Abstract - Bulk ZnGa2Se4 was grown by melt-growth technique, using the stoichiometric mixture of constitute elements. The ternarycompoundsemiconductorZnGa2Se4 thin films deposited by flash evaporation technique. The grown material was characterizedbyx-ray diffractiontechnique. The influence of the substrate temperature on the structural, morphological and optical properties of the films has been studied. The films deposited at substrate temperature range 573 K ≤ Tsub ≤ 673 K have been identified to be single phase, stoichiometric and polycrystallinewithhaving(112)and(204, 220) preferred orientations. The topography and the surface roughness of films were studied by Atomic Force Microscopy. Optical analysis of the films revealed that band gap energy increases with increase in the substrate temperatures. Key Words: Flash evaporation, Transmission Electron Microscopy, Stoichiometry, Atomic Force Microscopy, Optical Band gap 1. INTRODUCTION The Zinc tetraselenodigallate (ZnGa2Se4)ismemberoftheII- III2-IV4 group semiconducting compounds. This ternary group have increasing interest because of their wide applications such as memory devices, narrow band optical filters, nonlinear optical devices, schottky diode, ultra – violet photodetectors, etc. [1][2][3][4]. Most of these compounds form in tetragonal type structure [5][6][7]. Polycrystalline ZnGa2Se4 was first synthesized byHahnet al. [8]. Structural and optical properties of the ZnGa2Se4 thin films by thermal evaporation technique was reported by Fadel et al. [9]. ZnGa2Se4 can be used for phase change memories [10]. The current-voltage characteristics of ZnGa2Se4 heterojunction diode was studied by Yahia et al. [11]. Although, to our knowledge the influence of substrate temperatures on the structural and optical properties of ZnGa2Se4 thin films has not yet been reported. In the present investigation, we report in details thestudy of the deposition of ZnGa2Se4 thin films by flash evaporation technique and the significance of substrate temperatureson the structural, morphological and optical characteristicslike orientation of the films, elemental composition and optical band gap. 2. Experimental 2.1 Growth of Material A single phase, polycrystalline ingot of ZnGa2Se4 was grown by direct fusion of stoichiometric amounts of their constituent elements (Zn, Ga, and Se of purity 99.999%) in a sealed evacuated quartz ampoule at high vacuum. Then the ampoule was kept in a programmable rotating furnace. The temperatureof the furnacewasprogrammedwithincreasing rateof 100 K/h until it reach upto the 1423Kmeltingpointof ZnGa2Se4 [12] and was kept constant for 3 hours. During this constant period of time, the ampoule was rotated at the rate of 10 rpm. The rotation for three hours duration by mechanical shaking of the mixture ensures the high homogeneityand quality of the compound. Then,thefurnace was cooled down in steps until it reached the subsequent temperatures 873 K, 773 K and 643 K and kept constantfor1 h at every stage [8]. The ampoule was finally cooled down to the room temperature. The ingotofreddishcolorobtainedby breaking the ampoule which was finely powdered with a mortar for X - ray study. 2.2 Growth of Thin film ZnGa2Se4 thin films were grown by flash evaporation technique. The source material was single phase ZnGa2Se4 with average grain size of ~ 100 µm. The evaporant charge was reduced to the average grain size for complete evaporation of the material effectively to produce stoichiometric compound thin film. A flash evaporation system consists of controllable vibratory feeder system attached with a relay. An electrical pulse applied to the relay will drop the material fromthefeederintothequartzcrucible placed into a tungsten helical wire. The evaporant charge (~ 5 mg) was dropped step by step in to the preheated quartz crucible in order to deposit stoichiometric thin films. The substrates were placed in the middle of thecylindricalheater
2.
International Research Journal
of Engineering and Technology (IRJET) e-ISSN: 2395 -0056 Volume: 04 Issue: 03 | March -2017 www.irjet.net p-ISSN: 2395-0072 © 2017, IRJET | Impact Factor value: 5.181 | ISO 9001:2008 Certified Journal | Page 254 to get the homogeneous heating monitored by chromel - alumel thermocouple. 2.3 Experimental Methods The ingot obtained by breaking the ampoule was characterized by X – ray diffractometer (Philips, Model: X’Pert) using CuKα radiation. The elemental analysis was verified by energy dispersive X-ray analysis (Philips, Model: XL 30; ESEM). The films were deposited on to cleaned glass substrate and freshly cleaved NaCl crystals by vacuum coating unit (Hind Hivac-Model 12A4D). The rate of deposition was ~20 nm/s of all the films and residual pressure was ≈ 10-4 Pa. The distance between source and substrate was 18 cm. Film thickness was monitored and controlled by digital thickness monitor (DTM - 101) and it was found to be around 100 nm. The micrographs and its corresponding diffraction patters of ZnGa2Se4 thin film deposited on NaCl crystal were examined by transmission electron microscope (TEM, Model: Tecnai 20). The surface topography and roughness of the thin films were examined by Atomic Force Microscopy (AFM, Model: NT-MDT NTEGRA). The absorbance and transmittance spectra of ZnGa2Se4 thin films deposited at different substrate temperatures were recorded using UV-Vis-NIR spectrophotometer (Perkin Elmer, model: Lambda19)inthe wavelength range of 200 to 1500 nm. 3. RESULTS AND DISCUSSION 3.1 Structural Properties The bulk ZnGa2Se4 material was characterized by X-ray powder diffraction technique using CuKα radiation. The obtained X-raydiffractogramofZnGa2Se4 isshowninfigure1. Table 1 shows the d-values obtained from powder X-ray analysis were indexed using Bragg’s formula nλ = 2dsinθ. Good agreement has been observed from the calculation of the lattice constants of ZnGa2Se4 powder diffraction data were found to be a = 5.48 Å and c = 10.97 Å, with reported values of a = 5.50 Å and c = 10.99 Å (ICDD No. 01-089-4208) [13]. No additional peak other than ZnGa2Se4 was evident in XRD pattern. Figure 1: X-Ray Diffraction pattern of ZnGa2Se4 powder Figure 2 shows that the substrate temperatures have significant influence on the grain size and orientation of thin films deposited at 523 K, 573 K, 623 K, 673 K and 723 K respectively. From the electron micrographsitisevidentthat the grain size increases with increasing substrate temperatures. The d-values have been calculated for all the electron diffractionpatternsandcomparedwiththestandard reported dataasshown in table 1. Attention maybedrawnto the fact that the film grown at substrate temperature 523 K was amorphous in nature. However, the films deposited above 573 K are all polycrystalline in nature. As the further increment in substratetemperaturesat573K,623Kand673 K the electron diffraction patternsrevealedtheimprovement in the sharpness and intensity of (112), (220, 204) planes of the ZnGa2Se4 thin films. The films deposited at these substrate temperatures show (112) preferred orientation of the crystallites. At highersubstratetemperatureof723Kthin film become polyphase. As it is evident from [Figure 2(e)] several additional phases were identified due to the formation of ZnSe and Ga2Se3. 3.2 Morphological Properties Figure3 shows the AFM 2D and 3D images of films deposited at 573 K, 623 K and 673 K substratetemperatures which had different surface morphologies as a result of the substrate temperature variation. Topography of film deposited at 573 K, 623 K and 673 K shows uniformly distributed needle like grains with RMS surface roughness 0.37 nm, 0.46 nm and 1.45 nm respectively. This may be attributedtotheenhanced atomic mobility which could enable granules to grow more, resulting in an increase in the grain size. 3.3 Elemental Properties Figure 4 shows that the elemental weight percent of Zn, Ga and Se depend critically on the substrate temperatures. The films are nearly stoichiometric up to 673 K. The film deposited at 723 K are Zn and Se deficient. The Zn and Se deficiency may be attributed to re-evaporation of the Zn and Se from substrate surface, since both the elements have higher vapor pressure than Ga [14].
3.
International Research Journal
of Engineering and Technology (IRJET) e-ISSN: 2395 -0056 Volume: 04 Issue: 03 | March -2017 www.irjet.net p-ISSN: 2395-0072 © 2017, IRJET | Impact Factor value: 5.181 | ISO 9001:2008 Certified Journal | Page 255 Figure 2: Transmission electron micrographs and its corresponding electron diffraction patterns of ZnGa2Se4 thin films deposited on NaCl crystal at substrate temperatures of (a) 523 K, (b) 573 K, (c) 623 K, (d) 673 K and (e) 723 K (magnification 19000X). * Indicates the d-valuematchingwithZnSe.**Indicatethe d-values matching with Ga2Se3. Figure 3: 2D and 3D AFM image (1.5 x 1.5 µm2) profiles of ZnGa2Se4 thin films deposited at (a) 573K, (b) 623K and (c) 673K substrate temperature, respectively. Table 1: Comparison between the reported and observed diffraction data for bulk ZnGa2Se4 and thin films. Reported d-values (Å) Observed d-values (Å) hkl Bulk d – spacing values from electron diffraction patterns Int. d-values Ts=573 K Ts=623 K Ts=673 K Ts=723 K 3.4300 a) - - 3.4105 b) 100 e) 3.1729 100 3.1650 3.1609 3.1595 3.1682 3.1765 112 2.7480 2.65 2.7327 - - - - 004, 200 1.9430 56.50 1.9266 1.9343 1.9475 1.9440 1.9343 204,220 1.9190 c) - - - - - 1.9115 d) 220 e) 1.6570 33.94 1.6503 - 1.6500 - - 116, 312 1.3740 9.56 1.3624 1.3642 1.3718 1.3690 - 008, 400 1.2526 10.92 1.2537 1.2582 1.2505 1.2461 - 235, 413 1.1218 - - - 1.1207 - - 228, 424 Ts= Substrate Temperature, a) Standard d-values for ZnSe, b) d-values matching with ZnSe, c) Standard d-values for Ga2Se3, b) d-values matching with Ga2Se3, e) Indicates additional indices. (a) 523 K (b) 573 K (c) 623 K (d) 673 K (e) 723 K (a) 573 K (b) 623 K (c) 673 K
4.
International Research Journal
of Engineering and Technology (IRJET) e-ISSN: 2395 -0056 Volume: 04 Issue: 03 | March -2017 www.irjet.net p-ISSN: 2395-0072 © 2017, IRJET | Impact Factor value: 5.181 | ISO 9001:2008 Certified Journal | Page 256 Figure 4: Elemental weight percent of Zn, Ga and Se with the different substrate temperature for ZnGa2Se4 films. The dashed lines represent the stoichiometric ZnGa2Se4 compound elemental weight percent. 3.4 Optical Properties The variation of the absorbance (A) and transmittance (T %) spectra with wavelength range from 200-1500 nm for the ZnGa2Se4 thin films deposited at different substrate temperatures shown in figure 5. It is clearly observed that as the wavelength increases the absorbance from the films decreases. In the transmittance spectra the change was not considerable up to wavelength value of 300 nm. However, with further increasing the wavelength above 500 nm changes with oscillatory behavior. The average higher transmittance of around 70% - 80% was observed. Figure 5: (a) Absorbance, A and (b) Transmittance, T% Spectra of ZnGa2Se4 thin films deposited at different substratetemperatures. The optical absorption coefficient for allowed transition in a semiconductor near to the gap obtained by using αhʋ = A(hʋ - Eg)n Where Eg is the optical energy gap, A is a constant, hʋ is the photon energy and n is the exponent to characterizes the nature of the transition. Figure 6 shows the plot of (αhʋ)2 versus hʋ, photon energy for ZnGa2Se4 films deposited at different substrate temperatures with the equal thickness of 100 nm. The straight lines extrapolated upto the photon energy axis indicate that ZnGa2Se4 is direct band gap semiconductor. The directenergygap,Egarefoundtobe2.42 eV, 2.45 eV, 2.47 eV and 2.56 eV forthe filmsdepositedat573 K, 623 K, 673 K and 723 K, respectively. It has been noted that the band gap energy increases as the substrate temperatureincreases. It is observed fromthestructuraland morphological analysis that the grain size increases with the increase in the substrate temperature. As the film deposited at lower substrate temperature, the grain size are lower and grain boundaries are highly disordered which give high absorption for the films, whereas the films deposited at higher substratetemperatures resulting the growthoflarger grain sizes and strong orientation of the crystallites giving a less contribution to the absorption [15]. The energy gap values of the films deposited at 573 K to 673 K are found to be more or less equal to that of the reported value[16]. At higher substrate temperature 723 K, the higher value of energy gap can be explained duetothepresenceofadditional phase in the film.
5.
International Research Journal
of Engineering and Technology (IRJET) e-ISSN: 2395 -0056 Volume: 04 Issue: 03 | March -2017 www.irjet.net p-ISSN: 2395-0072 © 2017, IRJET | Impact Factor value: 5.181 | ISO 9001:2008 Certified Journal | Page 257 Figure 6: Plot of (αhʋ)2 versus hʋ for ZnGa2Se4 films deposited at 573 K, 623 K, 673 K and 723 K. 4. CONCLUSIONS The ZnGa2Se4 thin films deposited by flash evaporation technique in the temperature range 573 K ≤ Tsub ≤ 673 K are single phase, polycrystalline and stoichiometric in nature. Below the substrate temperature of 573 K the films are amorphous and above Tsub = 673 K the films are of polyphase. The AFM images were investigated to know the surface roughness and the effect on the topography of the films deposited at different substrate temperatures. The optical analysis showed that the direct band gap increases with increasing the substrate temperature. [1] N. V. Joshi, J. Luengo and F. Vera; “Optical activity in ZnGa2S4”, Materials Letters, 61 (8-9), 2007, pp. 1926- 1928. DOI: 10.1016/j.matlet.2006.07.177 [2] T. Ouahrani, A. H. Reshak, R. Khenata, B. Amrani, M. Mebrouki, A. Otero-de-la-Roza, V. Luana; “Åb-initio study of the structural, linear and nonlinear optical properties of CdAl2Se4 defect-chalcopyrite”, Journal of Solid State Chemistry, 183, 2010, pp 46–51. DOI:10.1016/j.jssc.2009.09.034 [3] D. K. Dhruv, A. Nowicki, B. H. Patel and V. D. Dhamecha; “Memory switching characteristics in amorphous ZnIn2Se4 thin films”, Surface Engineering, Vol. 31, Issue 7, 2015, pp. 556-562. DOI: 10.1179/1743294415Y.0000000001 [4] D. K. Dhruv and B. H. Patel; “Fabrication and electrical characterization of Al/p-ZnIn2Se4 thin film Schottky diode structure”, Materials Science in Semiconductor Processing, 54, 2016, pp. 29-35. http://dx.doi.org/10.1016/j.mssp.2016.06.012 [5] S. I. Radaustan, Å. N. Georgobiani and I. M. Tiginyanu; “II - III2 - VI4 Compounds: Properties and trends for applications”, Progress in Crystal Growth and Characterization, Vol. 10, 1980, pp. 403-412. DOI:10.1016/0146-3535(84)90064-9 [6] D. Errandonea, Ravhi S. Kumar, F. J. Manjon, V. V. Ursaki and I. M. Tiginyanu; “High-pressure x-ray diffraction study on the structure and phase transitions of the defect-stannite ZnGa2Se4 and defect-chalcopyrite CdGa2S4”, Journal of Åpplied Physics, Vol. 104, 2008, pp. 063524. http://dx.doi.org/10.1063/1.2981089 [7] S. Meenakshi, V. Vijayakumar,A.Eifler,H.DHochheimer; “Pressure-induced phase transition in defect Chalcopyrites HgAl2Se4 and CdAl2S4”, Journal of Physics and Chemistry of Solids, Vol. 71, 2010, pp. 832-835. DOI:10.1016/j.jpcs.2010.02.007 [8] H. Hahn, G. Frank, W. Klingler, A. Dorothee, Storger and G. Storger; “Uber ternare ChalkogenidedesÅluminiums, Galliums und Indiums mit Zink, Cadmium und Quecksilber”, Zeitschrift fur anorganische und allgemeine Chemie, Vol. 279, 1955, pp. 241-348. DOI: 10.1002/zaac.19552790502 [9] M. Fadel, I.S. Yahia, G.B. Sakr, F. Yakuphanoglu, S.S. Shenouda; “Structure, optical spectroscopy and dispersion parametersofZnGa2Se4 thinfilmsatdifferent annealing temperatures”, Optics Communications, Vol. 285, 2012, pp. 3154-3161. DOI: 10.1016/j.optcom.2012.02.096 [10]I. S. Yahia, M. Fadel, G. B. Sakr, S. S. Shenouda; “Memory switching of ZnGa2Se4 thin films as a new material for phase change memories (PCMs)”, Journal of Ålloys and Compounds, Vol. 507, 2010, pp. 551-556. DOI:10.1016/j.jallcom.2010.08.021 [11]I. S. Yahia, M. Fadel, G. B. Sakr, F. Yakuphanoglu, S. S. Shenouda, W. Å. Farooq; “Ånalysis of current-voltage characteristics of Al/p-ZnGa2Se4/n-Si nanocrystalline heterojunctiondiode”, Journal ofÅlloysandCompounds, Vol. 509, 2011, pp. 4414-4419. DOI:10.1016/j.jallcom.2011.01.068 [12]A. N. Georgobiani, B. G. Tagiev, G. G. Guseinov, T. G. Kerimova, O. B. Tagiev and S. G. Åsadullaeva; “Structure and Photoluminescence of ZnGa2Se4:Eu2+”, Inorganic Materials, Vol. 46, Issue 5, 2010, pp. 456-459. DOI: 10.1134/S0020168510050031 [13]International Centre for Diffraction Data, Card No. 01- 089-4208. [14]D. K. Dhruv and B. H. Patel; “Growth of flash evaporated ZnIn2Se4 thin films”, International Journal of Applied Science and Engineering Research, Vol. 3, Issue 1, 2014, pp. 121-128. DOI: 10.6088/ijaser.030100013 [15]A. H. Clark, in: Polycrystalline and amorphous thin films and devices, ed. L. L. Kazmerski (Academic Press, New York), p. 135, 1980. [16]W. T. Kim, C. S. Chuang, Y. G. Kim, M. S. Jin and H. G. Kim; “Optical absorption of ZnGa2Se4:Co2+ single crystal”, Physical Review B, Vol. 38, Issue3,1988,pp.2166-2168. DOI: https://doi.org/10.1103/PhysRevB.38.2166 REFERENCES
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