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Advances in Materials Science and Engineering
Volume 2013 (2013), Article ID 401392, 6 pages
Properties and Analysis of Transparency Conducting AZO Films by Using DC Power and RF Power Simultaneous Magnetron Sputtering
1Department of Electronic Engineering, Hsiuping University of Science and Technology, Taichung 412-80, Taiwan
2Graduate Institute of Optoelectronic Engineering, National Chung Hsing University, Taichung 402-27, Taiwan
3Graduate Institute of Optoelectronic Engineering and Department of Electrical Engineering, National Chung Hsing University, No. 250, Kuo Kuang Road, Taichung 402-27, Taiwan
Received 15 September 2013; Accepted 2 November 2013
Academic Editor: Shoou-Jinn Chang
Copyright © 2013 Neng-Fu Shih et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.
DC power and RF power were introduced into the magnetic controlled sputtering system simultaneously to deposit AZO films in order to get an acceptable deposition rate with high quality transparency conducting thin film. The resistivity decreases with the RF power for the as-deposited samples. The resistivity of 6 × 10−4 Ω-cm and 3.5–4.5 × 10−4 Ω-cm is obtained for the as-deposited sample, and for all annealed samples, respectively. The transmittance of the AZO films with higher substrate temperature is generally above 80% for the incident light wavelength within 400–800 nm. The transmittance of the as-deposited samples reveals a clear blue shift phenomenon. The AZO films present (002) oriented preference as can be seen from the X-ray diffraction curves. All AZO films reveal compressive stress. The annealing process improves the electrical property of AZO films. A significant blue shift phenomenon has been found, which may have a great application for electrode in solar cell.
High transparent metal oxide semiconductor with band gap larger than the energy of visible light is usually a good insulator at room temperature . Impurities doping is the easy way to increase conductivity. Tin doped indium oxide (ITO) , aluminum doped zinc oxide (AZO) [3, 4], and fluorine doped tin oxide SnO2 : F (FTO)  are quite popular materials as transparent semiconductors. ITO, the best transparent conducting film, is a solid solution of indium (III) oxide (In2O3) and tin (IV) oxide (SnO2), typically 90% In2O3, 10% SnO2 by weight. However, with high cost and limited supplies of indium, alternatives are being sought. Another choice for transparency conducting film is FTO, which is widely used in dye-sensitized solar cell. However, it is very easy for hydrogen plasma to etch FTO, as well as tin oxide. The utilization of FTO and SnO2 in the thin film solar cell application is limited. AZO films are a good candidate as a transparent conductive material, because the materials consist of cheap and abundant element, are readily produced for large-scale coating, allow tailing of ultraviolet absorption, have a high stability in hydrogen plasma, and have low growth temperature . Besides, it is nontoxic and easy to fabricate. The reasons for higher conductivity of Al doped ZnO films can be attributed to extrinsic donor and intrinsic donor [7, 8]. The Al replaces Zn ions to form extrinsic donors, as well as from oxygen vacancies and Zn interstitial atoms to form intrinsic donor [7, 8]. Production of the high conductivity and high transparency AZO films by controlling the intrinsic defects is highly desired for industrial application. Fang et al. deposited AZO film at 320°C by the DC sputtering with postdeposition annealing at 400°C for 2 hours under 10−3 Pa and got the resistivity as low as 1.5 × 10−4 Ω-cm . Park et al. used the RF sputtering method with 500°C high substrate temperature to get the lowest resistivity of 1.30 × 10−4 Ω-cm . Kim et al. used a DC cosputtering method followed by rapid thermal annealing to achieve a low resistivity of 1 × 10−3 Ω-cm . Ohta et al. investigated rapid thermal annealing of sputter-deposited ZnO and AZO films by using a radio-frequency (RF) argon thermal plasma jet at atmospheric pressure, and the lowest resistivity is around 3 × 10−4 Ω-cm . Exarhos et al. used 30% O2/Ar gas mixture and 150 W RF sputtering method, followed by 4% hydrogen in argon 725 K annealing . Chen et al. used 1.5% AZO target and O2/Ar gas mixture sputtering AZO film, followed by vacuum annealing, and analyzed its component with X-ray photoemission spectrum (XPS) and Auger electron spectrum (AES) . Guillen et al.  used DC sputtering at room temperature, annealed it in vacuum at 350°C, and got the best resistivity of 8 × 10−4 Ω-cm. Lee  uses RF sputtering in H2 and Ar mixture which reaches a minimum value of 4.4 × 10−4 Ω-cm at the H2/(H2 + Ar) gas ratio of 2.5%. These AZO films are good choices for high conductivity and high transparency film. The AZO film made by RF sputtering seems to have better electrical property than that made by DC sputtering . However, AZO film made by DC sputtering method has higher deposition rate than that made by RF sputtering method. Few factors will affect the quality, transparency, and conductivity of AZO films, such as grain size, crystallinity, and defects of different types . In this work, we report the results of making AZO films using DC and RF sputtering simultaneous methods both as-deposited and annealed samples, to check their conductivity with acceptable deposition rate.
2. Materials and Methods
2.1. Specimen Preparation
Content of the target used in this work is 2 wt. % Al2O3 and 98 wt. % ZnO. A corning 1737 glass was used as a substrate. After cleaning, the target and the substrate were put into a magnetron sputtering system and evacuated to 6.7 × 10−3 Pa. Then Ar gas with 70 cm3/min flow rate was introduced into the reaction chamber. After turning on the DC power supplier and RF power supplier, the target was presputtering for 5 minutes to remove surface contamination. Then open the shutter and sputter for 30 min at the pressures of 2.7 × 10−1 Pa. We have tested 3 different DC power suppliers to check the film quality with 30, 50, and 80 W and found that 80 W was the best choice for the film’s quality. Therefore, the DC power supplier was kept at 80 W, while the RF power was varied from 0 W to 120 W. Five substrate temperatures 225, 250, 275, 300, and 325°C were chosen for deposition. After deposition, one group of substrates was put into a high temperature furnace under a 550°C substrate temperature with 6% H2/Ar annealing for an hour to investigate the improvement of film quality. The thickness of films was measured by a Tencor alphastep 500 surface profiler, and the resistivity of films was measure by an ECOPIA model HMS-200 Hall Effect measurement system.
2.2. Crystalline Size
Crystalline size of AZO film can be evaluated from the FWHM of XRD peak and diffraction angle of the peak by the formula [7, 8] where is the crystalline size, is the full width at half maximum of the diffraction peak, is the incident X-ray wavelength (= 0.154 nm), and is diffraction angle of the peak.
2.3. In-Plane Stress
For hexagonal crystals with a high -axis preferred orientation, the in-plane stress can be calculated based on the biaxial strain model [18–20]: where is the interplaner spacing corresponding to (002) reflex in the XRD pattern, is that in bulk ZnO (0.2603 nm), and is elastic stiffness constants. The values of were calculated using Bragg formula .
2.4. Electrical Considerations
The doping of Al2O3 into ZnO structure is given by the equation [6, 10, 21, 22] where is the substitutional Al, the oxygen vacancy, and is the free electron. For the AZO film annealing under a vacuum process, a considerable increase in conductivity was obtained due to the increase in oxygen defects, which acted as electron donors. In the meantime, the annealing process has the effect of increasing grain size and crystallinity of the film, which therefore results in less grain boundary scattering . On the other hand, loss of oxygen from the crystal will also produce the interstitial zinc atoms according to the reaction [6, 10, 21, 22]: where is the interstitial zinc atoms. It means that the intrinsic donor can be increased by the hydrogen annealing process, thus, increasing the conductivity.
3. Results and Discussion
3.1. Structural Characteristics and Film Stress
Figure 1 illustrates the X-ray diffraction (XRD) patterns for the AZO film. The XRD patterns were measured by the use of a Rigaku XRD model PC-2000. The full width at half maximum of the diffraction peak and diffraction angle of the peak are determined from XRD patterns as illustrated in Figure 1. The diffraction peak intensity increases with the increasing substrate temperature, as can be seen from Figure 1. The increasing diffraction peak intensity of (002) between 225 and 325°C is primarily due to the crystallization of the AZO film.
The solid squares in Figure 2(a) give the thickness for the sputtered AZO films versus incident RF power. The thicknesses of the sputtered films are around 963–1412 nm. Obviously, the thickness increases with incident RF power for RF power ≤ 80 W but decreases with the incident RF power when RF power > 80 W. The increase of the thickness for RF power ≤ 80 W is primarily due to the increasing total incident power. That increases the ionization rate of the introduced Ar gas. The decrease of the thickness with the incident RF power, when RF power > 80 W, could be because positive cycle of the incident RF power is larger than the negative biased DC power (= 80 W). That decreases the ionization rate of the introduced Ar gas. The deposition rates for RF power = 0, 30, 50, 80, 100, and 120 W are 0.54, 0.59, 0.72, 0.79, 0.77, and 0.75 nm/s, respectively. The crystalline sizes of AZO films are also given in Figure 2(a), where the open squares indicate as-deposited samples and open triangles annealing samples.
The crystalline sizes of AZO films are 37.5, 42.2, 44.0, 42.2, 44.0, and 37.5 nm for RF power is 0, 30, 50, 80, 100, and 120 W, respectively. The crystalline sizes of the films generally are kept around 43 nm, except when RF is 0 W or 120 W. The crystalline sizes of AZO films are 37.5, 37.5, 39.0, 40.5, and 42.2 nm for the substrate temperature varies from 225, 250, 275, 300, to 325°C, respectively. The crystalline sizes increase with the substrate temperature.
The solid squares in Figure 2(b) give the thickness versus substrate temperature. The deposition rate of AZO film is 0.60, 0.68, 0.68, 0.66, and 0.59 nm for substrate temperature of 225, 250, 275, and 300 and 325°C, respectively. The AZO film has the highest deposition at 250°C substrate temperature and then, decreases with the substrate temperature.
Figure 3(a) gives the in-plane stress for the AZO as deposited at 325°C with various RF power; the stress generally increases with the RF power. Figure 3(b) shows the in-plane stress for the AZO as deposited at 225, 250, 275, 300, and 325°C, respectively. The results of Figure 3 are calculated from (2), where C11 = 208.8 × 109 N/m2, C33 = 213.8 × 109 N/m2, C12 = 119.7 × 109 N/m2, and C13 = 104.2 × 109 N/m2 were used [17–19]. 80 W DC power and 30 W RF power were used during sputtering. The minus sign indicates the compressive stress. The stress generally increases with the RF power and increases to 1.41 × 109 N/m2 from 225 to 250°C substrate temperature and then decreases to 0.40 × 109 N/m2.
The total film stress contains thermal stress and intrinsic stress. The thermal stress comes from thermal mismatch between AZO thin films and glass substrate. The generation mechanism of the intrinsic stress was caused by the growth process itself. Since the thermal stress is very small, film stress is mainly caused by the growth process itself . Comparing Figures 2 and 3, we conclude that higher deposition rate makes the film stress higher.
3.2. Electrical Characteristics
Figure 4 shows electrical property of the sputtered AZO film versus substrate temperature, where the dash lines indicate the resistivity, solid lines the electron concentration, and the dot lines the electron mobility, respectively. The squares indicate the as-deposited samples and the triangles the annealed samples, respectively.
The electron mobility for the annealed samples increases with the substrate temperature and is larger than that of the as-deposited samples, which could be due to the recrystallization of the annealed samples that increases the grain size which increase the electron mobility. The electron concentration of the annealed samples decreases with the increasing substrate temperature. For the as-deposited samples, both electron mobility and electron concentration increase with the increasing substrate temperature. Heating the AZO film, a considerable increase in conductivity was obtained due to the increase in oxygen defects, which increase the electron concentration in the film [9, 10]. In the meantime, the thermal process has the effect of increasing grain size and crystallinity of the film, which results in less grain boundary scattering [6, 9, 10]. These combined actions increase the conductivity. Therefore, the resistivity decreases with the increasing substrate temperature except for the annealed samples, since the resistivity is reciprocal to the product of electron concentration and electron mobility. The resistivity of annealed samples, although decreasing with the increasing substrate temperature, was kept around 3.5–4.5 × 10−4 Ω-cm. This could be due to the decrease of electron concentration at higher substrate temperature. Hydrogen annealing process introduces the hydrogen into the AZO film, resulting in a shallow donor in AZO film .
Figure 5 shows electrical property of the sputtered AZO film versus RF power with substrate temperature 325°C, where the dash lines indicate the resistivity, solid lines the electron concentration, and the dot lines the electron mobility, respectively. The squares indicate the as-deposited samples, and the triangles indicate the annealed samples, respectively. The resistivity of the as-deposited samples decreases with the RF power. The electron concentration increases slightly with the incident RF power for the as-deposited samples; however, the mobility of AZO film decreases slightly with the incident RF power.
3.3. Optical Properties
The transmittance was measured by the use of a Jasco model V-670 UV-VIS spectrophotometer. Figure 6 gives the transmittance of the as-deposited films for different substrate temperatures, where solid squares indicate 225°C, open circles 250°C, solid upper triangles 275°C, open down triangles 300°C, and solid diamonds 325°C. The transmittance for the AZO film with 325°C substrate temperature is above 80% within the visible light region, and transmittance with 275 and 300°C substrate temperatures is around 80% for the incident wavelength around 400 nm and is above 80% for the incident wavelength longer than 450 nm. The transmittance for substrate temperatures of 225 and 250°C is around 60% for the incident wavelength near 400 nm and is also above 80% for the incident wavelength longer than 450 nm. This wider transmittance spectrum for high substrate temperature samples implicated the more absorption efficiency for the solar cell application. Particularly, the transmittance of the as-deposited samples reveals a clear blue shift phenomenon. This is primarily due to the Burstein-Moss shift effect [12, 23]. Burstein-Moss shift is calculated by using the following equation: where is the electron effective mass, the Fermi level, the conduction-band edge, and the carrier concentration, respectively . The insertion of Figure 5 gives optical band gap versus carrier concentration and reveals a good linear relationship between optical band gap and carrier concentration . Therefore, we deduce that the blue shift of the transmission within 350–390 nm could be due to the Burstein-Moss shift effect.
4. Summary and Conclusions
AZO films were deposited by a magnetic control sputtering system using DC power and RF power simultaneously under different sputtering conditions. The AZO films present (002) oriented preference. The deposition rates for RF power = 0 W to 80 W increase from 0.54 nm/s to 0.79 nm/s which are good for mass production. In-plane stress for all AZO films reveals compressive stress. The stress increases with the RF power, increases to 1.41 × 109 N/m2 from 225 to 250°C substrate temperature, and then decreases to 0.40 × 109 N/m2. The transmittance for the film with higher substrate temperature is generally above 80% in the 400 nm~800 nm visible light region. The electron mobility for the annealed samples is larger than that of the as-deposited samples due to the recrystallization of the annealed samples that increase the grain size, resulting in the increasing electron mobility. The lowest resistivity for the annealed samples is 3.5 × 10−4 Ω-cm which is the best result ever reported by using DC and RF sputtering simultaneously. Furthermore, the sample with higher deposition temperature revealed a significant blue shift phenomenon which may have a great application for electrode in solar cell.
Conflict of Interests
The authors hereby declare that there is no conflict of interests with any financial organization regarding the material discussed in the paper.
This work was supported by the National Science Council Taiwan, under Grant NSC100-2221-E-164-004.
- J. L. Vossen, “Transparent conducting films,” Physics of Thin Films, vol. 9, pp. 1–64, 1977.
- L. Davis, “Properties of transparent conducting oxides deposited at room temperature,” Thin Solid Films, vol. 236, no. 1-2, pp. 1–5, 1993.
- H. W. Lehmann and R. Widmer, “Preparation and properties of reactively co-sputtered transparent conducting films,” Thin Solid Films, vol. 27, no. 2, pp. 359–368, 1975.
- H. S. Randhawa, M. D. Matthews, and R. F. Bunshah, “SnO2 films prepared by activated reactive evaporation,” Thin Solid Films, vol. 83, no. 2, pp. 267–271, 1981.
- E. Shanthi, A. Banerjee, V. Dutta, and K. L. Chopra, “Electrical and optical properties of tin oxide films doped with F and (Sb+F),” Journal of Applied Physics, vol. 53, no. 3, pp. 1615–1621, 1982.
- G. Fang, D. Li, and B.-L. Yao, “Fabrication and vacuum annealing of transparent conductive AZO thin films prepared by DC magnetron sputtering,” Vacuum, vol. 68, no. 4, pp. 363–372, 2002.
- B. D. Cullity and S. R. Stock, Elements of X-Ray Diffraction, Prentice-Hall, 3rd edition, 2001.
- A. L. Patterson, “The scherrer formula for X-ray particle size determination,” Physical Review, vol. 56, no. 10, pp. 978–982, 1939.
- J. H. Park, J. M. Shin, S.-Y. Cha et al., “Deposition-temperature effects on AZO thin films prepared by RF magnetron sputtering and their physical properties,” Journal of the Korean Physical Society, vol. 49, no. 2, pp. S584–S588, 2006.
- Y. Kim, W. Lee, D.-R. Jung et al., “Optical and electronic properties of post-annealed ZnO:Al thin films,” Applied Physics Letters, vol. 96, no. 17, Article ID 171902, 2010.
- N. Ohta, D. Ohba, S. Sato, Z. Tang, H. Shimizu, and H. Shirai, “Rapid thermal-plasma annealing of ZnO:Al films for silicon thin-film solar cells,” Thin Solid Films, vol. 519, no. 20, pp. 6920–6927, 2011.
- G. J. Exarhos, A. Rose, and C. F. Windisch Jr., “Spectroscopic characterization of processing-induced property changes in doped ZnO films,” Thin Solid Films, vol. 308-309, no. 1–4, pp. 56–62, 1997.
- M. Chen, X. Wang, Y. H. Yu et al., “X-ray photoelectron spectroscopy and auger electron spectroscopy studies of Al-doped ZnO films,” Applied Surface Science, vol. 158, no. 1, pp. 134–140, 2000.
- C. Guillén and J. Herrero, “Optical, electrical and structural characteristics of Al:ZnO thin films with various thicknesses deposited by DC sputtering at room temperature and annealed in air or vacuum,” Vacuum, vol. 84, no. 7, pp. 924–929, 2010.
- J.-H. Lee, “Effects of hydrogen incorporation and heat treatment on the properties of ZnO:Al films deposited on polymer substrate for flexible solar cell applications,” Current Applied Physics, vol. 10, no. 3, pp. S515–S519, 2010.
- W. Yang, Z. Wu, Z. Liu, A. Pang, Y.-L. Tu, and Z. C. Feng, “Room temperature deposition of Al-doped ZnO films on quartz substrates by radio-frequency magnetron sputtering and effects of thermal annealing,” Thin Solid Films, vol. 519, no. 1, pp. 31–36, 2010.
- K. H. Ri, Y. B. Wang, W. L. Zhou, J. X. Gao, X. J. Wang, and J. Yu, “The effect of SiO2 buffer layer on the electrical and structural properties of Al-doped ZnO films deposited on soda lime glasses,” Applied Surface Science, vol. 257, no. 13, pp. 5471–5475, 2011.
- T. B. Bateman, “Elastic moduli of single-crystal zinc oxide,” Journal of Applied Physics, vol. 33, no. 11, pp. 3309–3312, 1962.
- Y.-Y. Chen, P. W. Wang, J.-C. Hsu, and C.-Y. Lee, “Post-annealing properties of aluminum-doped zinc oxide films fabricated by ion beam co-sputtering,” Vacuum, vol. 87, pp. 227–231, 2013.
- L. Li, L. Fang, X. M. Chen et al., “Influence of oxygen argon ratio on the structural, electrical, optical and thermoelectrical properties of Al-doped ZnO thin films,” Physica E, vol. 41, no. 1, pp. 169–174, 2008.
- J. F. Chang, W. C. Lin, and M. H. Hon, “Effects of post-annealing on the structure and properties of Al-doped zinc oxide films,” Applied Surface Science, vol. 183, no. 1-2, pp. 18–25, 2001.
- N. F. Shih, C. C. Lin, and C. Y. Kung, “Effect of oxygen contents on the properties of Al-Doped ZnO films prepared by low temperature magnetic controlled DC sputtering,” Japanese Journal of Applied Physics, vol. 52, no. 1, Article ID 01AC07, 2013.
- B. E. Sernelius, K.-F. Berggren, Z.-C. Jin, I. Hamberg, and C. G. Granqvist, “Band-gap tailoring of ZnO by means of heavy Al doping,” Physical Review B, vol. 37, no. 17, pp. 10244–10248, 1988.