Growth and optical properties of ZnO nanorod arrays on Al-doped ZnO transparent conductive film
© Lin et al.; licensee Springer. 2013
Received: 28 January 2013
Accepted: 21 March 2013
Published: 8 April 2013
ZnO nanorod arrays (NRAs) on transparent conductive oxide (TCO) films have been grown by a solution-free, catalyst-free, vapor-phase synthesis method at 600°C. TCO films, Al-doped ZnO films, were deposited on quartz substrates by magnetron sputtering. In order to study the effect of the growth duration on the morphological and optical properties of NRAs, the growth duration was changed from 3 to 12 min. The results show that the electrical performance of the TCO films does not degrade after the growth of NRAs and the nanorods are highly crystalline. As the growth duration increases from 3 to 8 min, the diffuse transmittance of the samples decreases, while the total transmittance and UV emission enhance. Two possible nanorod self-attraction models were proposed to interpret the phenomena in the sample with 9-min growth duration. The sample with 8-min growth duration has the highest total transmittance of 87.0%, proper density about 75 μm−2, diameter about 26 nm, and length about 500 nm, indicating that it can be used in hybrid solar cells.
KeywordsZnO nanorod Al-doped ZnO films Catalyst-free growth Optical properties 81.07.-b 61.46.Km 78.67.-n
ZnO, one of the most important metal oxides, has a wide bandgap of 3.37 eV and a high exciton binding energy of 60 meV at room temperature. One-dimensional nanostructures have a high aspect ratio and surface area, and can provide a direct conduction path for electrons. Accordingly, a wide range of ZnO nanostructures  such as nanowires (NWs), nanorods (NRs), and nanonails are extensively studied for their applications in various optoelectronic devices, e.g., gas sensors , UV photodetectors [3, 4], lasers [5, 6], electron field emitters , solar cells [8–12], and nanogenerators .
For most photovoltaic devices, the light is coupled in devices through transparent conductive oxide (TCO) substrate, so tailored well-aligned ZnO nanorod arrays (NRAs) grown on TCO substrate are of particular interest because they can improve the device performance . Previously, ZnO NRAs and NWs on different TCO substrates have been synthesized by various growth methods including chemical bath deposition [8, 10, 11], electrochemical deposition [9, 12, 14], and thermal vapor-phase deposition [15, 16]. Among these methods, the vapor-phase growth method has many advantages such as excellent crystalline quality of the nanostructures , low cost, and simplicity . Generally, ZnO NRs in dye-sensitized solar cells or hybrid solar cells are used to extract the carriers from an organic material and transfer the carriers toward the electrode . Moreover, the density, diameter, length, and crystalline performance of NRs have a significant influence on the efficiency of solar cells [9, 15, 16]. A larger nanorod diameter will reduce spacing between NRs, which contributes to a reduction in the amount of solar absorber. Longer ZnO NRs do not improve the solar efficiency due to the lower short-circuit current . Therefore, it is important to synthesize ZnO NRAs on TCO substrate with the suitable nanorod diameter, length, and density for their applications in hybrid solar cells. However, there are few reports on the growth and optical properties of ZnO NRAs on a TCO substrate by the vapor-phase deposition [15, 16].
In this paper, we focus on the growth and optical properties of ZnO NRAs, which were grown by a solution-free, catalyst-free, vapor-phase synthesis method at a temperature of 600°C. This method can grow ZnO NRAs on Al-doped ZnO (AZO) films, and the performance of AZO does not degrade after the growth of NRAs. AZO has the advantage of being indium free and can be produced on a large scale. The effect of growth duration on the morphology and optical properties of NRAs has been investigated.
AZO films were deposited on quartz substrates using a radio-frequency (RF) magnetron sputtering system at room temperature. The quartz substrates, 0.5 mm thick, 2.5 cm × 2.5 cm, were cleaned in acetone and ethanol several times before deposition. The target, 60-mm diameter, was a commercial ZnO and Al2O3 mixture (97:3 wt.%) of ≥99.99% purity. The sputtering was performed in an Ar atmosphere with a target-to-substrate distance of 5 cm. The base pressure in the chamber was 4.0 × 10−4 Pa. The Ar flux determined using a mass flow-controlled regulator was maintained at 50.0 sccm, and the sputtering pressure was 0.5 Pa. The RF power was 300 W, and deposition time was typically 10 min. A typical sheet resistance of AZO film, about 480 nm thick, was about 60 Ω/sq.
ZnO NRAs were grown by a vapor-phase method in a horizontal tube furnace . The substrates, polycrystalline AZO films on quartz substrates, were cleaned in acetone and ethanol before the NRA growth. Commercial zinc (99.99% purity) powder in a ceramic boat was used as the zinc vapor source. The ceramic boat and AZO substrate were placed in a long quartz tube, and the quartz tube was then put into the furnace. An AZO substrate was placed 5 cm downstream from the sources at the heat center of the furnace. After evacuating the system to a base pressure of 12 Pa, the furnace temperature was ramped to 600°C at 20°C min−1. A 100-sccm Ar and 10-sccm oxygen mixed gas was introduced into the furnace only when the maximum temperature was reached. The growth pressure was 110 Pa. The temperature was kept at 600°C for several minutes, and then the furnace was cooled down to room temperature. Changing the growth duration, several samples had been synthesized. For simplicity, the samples with growth durations of 3, 6, 8, 9, and 12 min were defined as samples S1, S2, S3, S4, and S5, respectively.
Morphological and structural properties of the grown nanostructures were analyzed using a JSM-7500LV scanning electron microscope (SEM) and a JEM-2010 high-resolution transmission electron microscope (TEM) (JEOL Ltd., Akishima-shi, Japan). For the latter, the samples were prepared by mechanically scraping NRs from the substrate, dispersing them in ethanol, and depositing a drop of the dispersion on a circular copper grid covered by a thin holey carbon film. The crystal structure and orientation were investigated using an X-ray diffractometer (XRD; Y-2000, Rigaku Corporation, Shibuya-ku, Japan) with monochromated Cu Kα irradiation (λ = 1.5418 Å). The surface morphology of the AZO film was observed using an atomic force microscope (AFM; CSPM 4000, Benyuan Co. Ltd., Guandong, China) under ambient conditions. The sheet resistance was measured by the van der Pauw method .
Room-temperature photoluminescence (PL) spectra of the samples were obtained on a Fluorolog 3–22 fluorescence spectrophotometer (Horiba Ltd., Kyoto, Japan) using a Xe lamp with an excitation wavelength of 325 nm. The total transmittance and diffuse transmittance of the samples were measured using a double-beam spectrophotometer (PerkinElmer Lambda 950, Waltham, MA, USA) equipped with an integrating sphere. In the measurement, the light propagation path was air/quartz/AZO/air or air/quartz/AZO/NRAs/air, and the reflection at the quartz/air interface was not removed.
Results and discussion
Density and average NR dimensions (diameter, length, and aspect ratio) of the samples
Density (per μm2)
Average NR diameter 2r(nm)
Average NR length L(nm)
Aspect ratio L/r
40 ± 8
28 ± 7
250 ± 50
61 ± 6
25 ± 6
420 ± 40
75 ± 2
26 ± 4
500 ± 20
82 ± 2
28 ± 4
550 ± 20
In previous research reports, it was found that the characteristic of ZnO NWs strongly depends on the crystallinity, type, and surface roughness of the growth substrate . The crystallinity, surface roughness, and thickness of the ZnO seed layer also have an important influence on ZnO NR growth . We speculate that two main reasons contribute to the not well vertically aligned NRAs in our samples. First is that the AZO film was deposited on the amorphous quartz substrate, which results in a polycrystalline AZO film as discussed below. Figure 1h is a typical AFM surface image of an AZO film. AFM results indicate that the root-mean-square surface roughness and the average surface particle size are 10.2 and 140 nm, respectively. The second reason, therefore, is that the polycrystalline AZO film deposited by RF sputtering has large surface roughness and surface particle size.
In a hybrid solar cell, ZnO NRs play the roles to extract carriers from the absorber and provide a fast and direct path for these carriers. The efficiency of a solar cell strongly relies on the crystallinity, density, diameter, and length of ZnO NR [9, 15]. Conradt et al.  have reported that short NRs in the range of 100 to 500 nm are of particular interest for hybrid solar cells. A smaller NR diameter will enhance the spacing between NRs and increase the solar absorber amount and the efficiency of a solar cell . NR in sample S3 has a suitable length about 500 nm and a small diameter about 26 nm. Accordingly, we suggest that sample S3 is interesting for application in hybrid solar cells.
ATT, ADT, and SR of the AZO film and samples
An AZO film must have a low resistance for use as a transparent conductive electrode in optoelectronic devices . The electrical properties of an AZO film may be changed after thermal treatment at high temperature, and especially our NR growth temperature is 600°C. So, the sheet resistance (SR) of the sample was measured. The NRs at electrode positions were removed to enable good contact of the electrodes before the resistance measurement, and the results are shown in Table 2. All the sheet resistances of the samples are lower than that of the AZO film (60 Ω/sq), indicating that the electrical performance of the AZO film does not degenerate after the NR growth. We speculate that there are two mechanisms that induce the reduction of the sheet resistances. One is that the resistance of the AZO film after the thermal treatment declines, which had been confirmed experimentally [16, 28]. The other is, as indicated in Figure 1f,g, the result of a ZnO buffer layer between NRAs and AZO film after NR growth. ZnO is naturally an n-type semiconductor due to the presence of intrinsic defects such as oxygen vacancies and zinc interstitials . The resistance of a ZnO film will decline as the oxygen vacancies increase because each oxygen vacancy can generate two conductive electrons. The NRAs and ZnO buffer layer in sample S1 have the most oxygen vacancies, as confirmed by PL measurement, so it has the lowest sheet resistance (17 Ω/sq).
A solution-free, catalyst-free, vapor-phase growth method was used to synthesize ZnO nanorod arrays on AZO films, which were deposited on quartz substrates by RF magnetron sputtering. The sheet resistance of the sample declines after ZnO NRA growth at 600°C. TEM results show that the NRs are the single-crystal ZnO with wurtzite structure. As the growth duration increases from 3 to 8 min, the oxygen vacancies and diffuse transmittance of the samples decrease, while the crystallinity, aspect ratio, near-band-edge emission, and total transmittance enhance. ZnO NR self-attraction in the sample with 9-min growth duration has been observed, and two possible NR self-attraction models are proposed. NRs in the sample with 12-min growth duration are disordered, which has the largest diffuse transmittance and a relatively strong deep-level emission. The sample with 8-min growth duration has a density about 75 μm−2, diameter about 26 nm, and length about 500 nm, which can be used in a hybrid solar cell.
This work was financially supported by the Natural Science Foundation of China (no. 11074041) and the Natural Science Foundation of Fujian Province of China (2012J01256).
- Jiang P, Zhou JJ, Fang HF, Wang CY, Wang ZL, Xie SS: Hierarchical shelled ZnO structures made of bunched nanowire arrays. Adv Funct Mater 2007, 17: 1303–1310. 10.1002/adfm.200600390View ArticleGoogle Scholar
- Chien FSS, Wang CR, Chan YL, Lin HL, Chen MH, Wu RJ: Fast-response ozone sensor with ZnO nanorods grown by chemical vapor deposition. Sens Actuators B: Chem 2010, 144: 120–125. 10.1016/j.snb.2009.10.043View ArticleGoogle Scholar
- Zhang X, Han X, Su J, Zhang Q, Gao Y: Well vertically aligned ZnO nanowire arrays with an ultra-fast recovery time for UV photodetector. Appl Phys A 2012, 107: 255–260. 10.1007/s00339-012-6886-6View ArticleGoogle Scholar
- Dhara S, Giri PK: Enhanced UV photosensitivity from rapid thermal annealed vertically aligned ZnO nanowires. Nanoscale Res Lett 2011, 6: 504. 10.1186/1556-276X-6-504View ArticleGoogle Scholar
- Liu XY, Shan CX, Wang SP, Zhang ZZ, Shen DZ: Electrically pumped random lasers fabricated from ZnO nanowire arrays. Nanoscale 2012, 4: 2843–2846. 10.1039/c2nr30335cView ArticleGoogle Scholar
- Huang MH, Mao S, Feick H, Yan H, Wu Y, Kind H, Weber E, Russo R, Yang P: Room-temperature ultraviolet nanowire nanolasers. Science 2001, 292: 1897–1899. 10.1126/science.1060367View ArticleGoogle Scholar
- Chen ZH, Tang YB, Liu Y, Yuan GD, Zhang WF, Zapien JA, Bello I, Zhang WJ, Lee CS, Lee ST: ZnO nanowire arrays grown on Al:ZnO buffer layers and their enhanced electron field emission. J Appl Phys 2009, 106: 064303. 10.1063/1.3213091View ArticleGoogle Scholar
- Seol M, Ramasamy E, Lee J, Yong K: Highly efficient and durable quantum dot sensitized ZnO nanowire solar cell using noble-metal-free counter electrode. J Phys Chem 2011, 115: 22018–22024.Google Scholar
- Chen JW, Perng DC, Fang JF: Nano-structured Cu2O solar cells fabricated on sparse ZnO nanorods. Sol Energy Mater Sol Cells 2011, 95: 2471–247. 10.1016/j.solmat.2011.04.034View ArticleGoogle Scholar
- Zhang J, Que W, Shen F, Liao Y: CuInSe2 nanocrystals/CdS quantum dots/ZnO nanowire arrays heterojunction for photovoltaic applications. Sol Energy Mater Sol Cells 2012, 103: 30–34.View ArticleGoogle Scholar
- Lee SH, Han SH, Jung HS, Shin H, Lee J, Noh JH, Lee S, Cho IS, Lee JK, Kim J, Shin H: Al-doped ZnO thin film: a new transparent conducting layer for ZnO nanowire-based dye-sensitized solar cells. J Phys Chem C 2010, 114: 7185–7189. 10.1021/jp1008412View ArticleGoogle Scholar
- Wang L, Zhao D, Su Z, Shen D: Hybrid polymer/ZnO solar cells sensitized by PbS quantum dots. Nanoscale Res Lett 2012, 7: 106. 10.1186/1556-276X-7-106View ArticleGoogle Scholar
- Wang ZL, Song J: Piezoelectric nanogenerators based on zinc oxide nanowire arrays. Science 2006, 312: 242–246. 10.1126/science.1124005View ArticleGoogle Scholar
- Lee HK, Kim MS, Yu JS: Effect of AZO seed layer on electrochemical growth and optical properties of ZnO nanorod arrays on ITO glass. Nanotechnology 2011, 22: 445602. 10.1088/0957-4484/22/44/445602View ArticleGoogle Scholar
- Conradt J, Sartor J, Thiele C, Flaig FM, Fallert J, Kalt H, Schneider R, Fotouhi M, Pfundstein P, Zibat V, Gerthsen D: Catalyst-free growth of zinc oxide nanorod arrays on sputtered aluminum-doped zinc oxide for photovoltaic applications. J Phys Chem C 2011, 115: 3539–3543. 10.1021/jp111824dView ArticleGoogle Scholar
- Calestani D, Pattini F, Bissoli F, Gilioli E, Villani M, Zappettini A: Solution-free and catalyst-free synthesis of ZnO-based nanostructured TCOs by PED and vapor phase growth techniques. Nanotechnology 2012, 23: 194008. 10.1088/0957-4484/23/19/194008View ArticleGoogle Scholar
- Liu P, Li Y, Guo Y, Zhang Z: Growth of catalyst-free high-quality ZnO nanowires by thermal evaporation under air ambient. Nanoscale Res Lett 2012, 7: 220. 10.1186/1556-276X-7-220View ArticleGoogle Scholar
- Zhuang B, Lai F, Lin L, Lin M, Qu Y, Huang Z: ZnO nanobelts and hollow microspheres grown on Cu foil. Chin J Chem Phys 2010, 23: 79–83. 10.1088/1674-0068/23/01/79-83View ArticleGoogle Scholar
- Lai F, Lin L, Gai R, Lin Y, Huang Z: Determination of optical constants and thickness of In2O3:Sn films from transmittance data. Thin Solid Films 2007, 515: 7387–7392. 10.1016/j.tsf.2007.03.037View ArticleGoogle Scholar
- Ho ST, Chen KC, Chen HA, Lin HY, Cheng CY, Lin HN: Catalyst-free surface-roughness-assisted growth of large-scale vertically aligned zinc oxide nanowires by thermal evaporation. Chem Mater 2007, 19: 4083–4086. 10.1021/cm070474yView ArticleGoogle Scholar
- Li C, Fang G, Li J, Ai L, Dong B, Zhao X: Effect of seed layer on structural properties of ZnO nanorod arrays grown by vapor-phase transport. J Phys Chem C 2008, 112: 990–995. 10.1021/jp077133sView ArticleGoogle Scholar
- Han X, Wang G, Zhou L, Hou JG: Crystal orientation-ordered ZnO nanorod bundles on hexagonal heads of ZnO microcones: epitaxial growth and self-attraction. Chem Commun 2006, 212: 212–214.View ArticleGoogle Scholar
- Wang X, Summers CJ, Wang ZL: Self-attraction among aligned Au/ZnO nanorods under electron beam. Appl Phys Lett 2005, 86: 013111. 10.1063/1.1847713View ArticleGoogle Scholar
- Liu J, Xie S, Chen Y, Wang X, Cheng H, Liu F, Yang J: Homoepitaxial regrowth habits of ZnO nanowire arrays. Nanoscale Res Lett 2011, 6: 619. 10.1186/1556-276X-6-619View ArticleGoogle Scholar
- Convertino A, Cuscunà M, Rubini S, Martelli F: Optical reflectivity of GaAs nanowire arrays: experiment and model. J Appl Phys 2012, 111: 114302. 10.1063/1.4723567View ArticleGoogle Scholar
- Versteegh MAM, Van der Wel REC, Dijkhuis JI: Measurement of light diffusion in ZnO nanowire forests. Appl Phys Lett 2012, 100: 101108. 10.1063/1.3692741View ArticleGoogle Scholar
- Lai F, Li M, Wang H, Hu H, Wang X, Hou JG, Song Y, Jiang Y: Optical scattering characteristic of annealed niobium-oxide films. Thin Solid Films 2005, 488: 314–320. 10.1016/j.tsf.2005.04.036View ArticleGoogle Scholar
- Wimmer M, Ruske F, Scherf S, Rech B: Improving the electrical and optical properties of DC-sputtered ZnO:Al by thermal post deposition treatments. Thin Solid Films 2012, 520: 4203–4207. 10.1016/j.tsf.2011.04.102View ArticleGoogle Scholar
- Hwang DK, Oh MS, Lim JH, Park SJ: ZnO thin films and light-emitting diodes. J Phys D: Appl Phys 2007, 40: R387-R412. 10.1088/0022-3727/40/22/R01View ArticleGoogle Scholar
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