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- Table of Contents
Journal of Nanomaterials
Volume 2012 (2012), Article ID 452407, 6 pages
Effect of Different Seed Solutions on the Morphology and Electrooptical Properties of ZnO Nanorods
1Institute of Nano Electronic Engineering, Universiti Malaysia Perlis, Seriab, Kangar, 01000 Perlis, Malaysia
2Nanotechnology and Catalysis Research Centre, University of Malaya, 50603 Kuala Lumpur, Malaysia
3Department of Electronic Engineering, NED University of Engineering and Technology, Karachi 75270, Pakistan
4NANO-ElecTronic Centre (NET), Faculty of Electrical Engineering, Universiti Teknologi MARA (UiTM), Selangor, 40450 Shah Alam, Malaysia
5Department of Science and Technology, Campus Norrköping, Linköping University, 60174 Norrköping, Sweden
Received 18 May 2012; Revised 27 August 2012; Accepted 27 August 2012
Academic Editor: Gong Ru Lin
Copyright © 2012 M. Kashif 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.
The morphology and electrooptical properties of ZnO nanorods synthesized on monoethanolamine-based seed layer and KOH-based seed layer were compared. The seed solutions were prepared in monoethanolamine in 2-methoxyethanol and potassium hydroxide in methanol, respectively. Zinc acetate dihydrate was as a common precursor in both solutions. The nanorod-ZnOs were synthesized via the spin coating of two different seed solutions on silicon substrates followed by their hydrothermal growth. The scanning electron microscopy (SEM), X-ray diffraction (XRD), photoluminescence (PL), and Raman studies revealed that the ZnO nanorods obtained from monoethanolamine-based seed layer had fewer defects, better crystals, and better alignment than those realized via KOH-based seed layer. However, the current-voltage (I-V) characteristics demonstrated better conductivity of the ZnO nanorods obtained via KOH-based seed layer. The current measured in forward bias was 4 mA and 40 μA for ZnO-nanorods grown on KOH-based seed layer and monoethanolamine-based with the turn on voltage of approximately 1.5 V and 2.5 V, respectively, showing the feasibility of using both structures in optoelectric devices.
Zinc oxide (ZnO) which belongs to II–IV group of semiconducting materials is increasingly getting more and more research interests because of its attractive and fascinating properties such as approximately 3.37 eV of direct wide bandgap and about 60 meV of exciton binding energy. In fact, these properties are suitable for numerous applications in optoelectronic and biomedical devices. For examples micro- and nanostructures ZnO were successfully used in various sensing appliances such as UV sensors, biosensors (protein, DNA, and cancer cell detection) as well as gas sensors [1–5]. In the last few decades, ZnO-nanostructures with many fascinating forms such as nanorods, nano-flakes, nanorings, and nanoribbons, were synthesized [6–9]. To obtain these structures, various methods such as MOCVD, sol-gel, molecular beam epitaxy, thermal evaporation, and site-selective deposition techniques were documented [10–16]. Among these techniques, sol-gel methods have got huge interests because of their reduced growth temperature, reduced cost, and superior simplicity. However, a comparative study of ZnO nanorods synthesized on monoethanolamine-based seed layer and KOH-based seed layer using sol-gel method to realize nanorod-ZnOs has yet to be systematically reported.
In this study, nanorod-ZnOs were synthesized on two different seeded substrates and their morphological, crystalline, and optoelectrical properties were systematically studied using SEM, XRD, Raman, and photoluminescence spectroscopies as well as current-voltage profiler. The study reflected that the seed solution prepared through 2-methoxyethanol route is superior to KOH one to synthesize nanorod-ZnO with less defects, better crystal, and better alignment. On the other hand, the applicability of KOH route was realized to obtain nanostructured ZnO with superior conductivity.
2.1. Preparation of Seed Solutions
All chemicals used in this experiment were of the highest available purity and were purchased from Sigma-Aldrich, USA. ZnO seed solutions were prepared in two different solvents, namely, methanol and 2-methoxyethanol. The first solution (0.01 M) was prepared by dissolving 274 mg of zinc acetate dihydrate in 125 mL of methanol at 60°C. A potassium hydroxide solution of 0.03 M was prepared by dissolving 109 mg of KOH in 65 mL of methanol in a separate beaker. To a 25 mL portion of 0.01 M zinc acetate dihydrate solution heated at 60°C, 13 mL of 0.03 M KOH was added drop-wise under vigorous stirring. The solution was incubated at 60°C for 2 h with continual stirring. In the second solution, the concentration of zinc acetate dihydrate was 0.35 M in 2-methoxyetanol. To the second seed solution which was heated to 60°C, monoethanolamine (MEA) was added drop-wise under vigorous stirring until the molar ratio of MEA to zinc acetate dihydrate was reached to 1 : 1. The second seed solution was also incubated at 60°C for 2 h with continual stirring. The measured pH values for monoethanolamine-based seed solution and KOH-based seed solution were 7.69 and 8.90, respectively.
2.2. Synthesis of ZnO Nanorods
The ZnO-nanorods were synthesized on silicon substrates through a spin-coating method. Prior to coating, the silicon substrates were nicely cleaned with RCA1 and RCA2  followed by buffered oxide etching (BOE) to remove the native oxide layer. The seed solutions were then spin coated on the cleaned silicon substrates at a spin speed of 3000 rpm for 30 s. After successive coating of each layer, the substrates were dried at 60°C for 10 min and 250°C for 20 min to remove the organic residuals. Finally, the thin films were annealed at 550°C for 2 h. The growth solution was prepared by mixing zinc nitrate hexahydrate (0.025 M) and hexamethyltetramine (0.025 M) in 150 mL DI water. The growth solution was transferred to a 250 mL beaker under vigorous stirring for 20 min and then the precoated substrates were immerged horizontally inside the beaker containing the growth precursors. After that, the beaker was directly inserted in a preheated oven at 93°C for 6 hours to induce the growth of nanorods. After the growth induction time, the oven was ramped down to room temperature, and the substrates were washed with deionized water to remove any residual salts and were dried under nitrogen flow. The ZnO nanorods obtained from KOH-based seed layer and monoethanolamine-based seed layer were categorized as sample 1 and sample 2.
2.3. Characterization of Nanostructured ZnO
The morphological characterization of nanostructured ZnO was performed using a scanning electron microscope (SEM, JSM JEOL 6460 LA) whereas the cross-sectional images were collected from Hitachi S3400n SEM instrument. The crystallinity of the ZnO-nanorods was studied using an X-ray diffraction (XRD) with a CuK () window. The optical properties were analyzed with a photoluminescence spectroscopy (HR800, Horiba Jyobin) excited by He-Cd laser at a wavelength of 325 nm with a power of 20 mW. Raman spectra of ZnO nanorods were collected with an argon (Ar+) laser excited at 514 nm with an incident power of 20 mW (Horiba Jyobin). For electrical characterization, circular silver electrodes were deposited on the top of ZnO nanorods using Auto306 vacuum thermal evaporator. Current to voltage (I-V) characterization was carried out using Keithley 2400 source meter interfaced with Lab tracer 2.0 software.
3. Results and Discussion
The SEM images of ZnO nanorods obtained on sample 1 and sample 2 are shown in Figures 1(a) and 1(b). The morphology of ZnO nanorods grown on sample 1 is demonstrated in Figure 1(a). The silicon substrate was densely covered with the ZnO nanorods. However, the synthesized nanorods were not orderly aligned to the substrate. This was reflected in the cross-sectional SEM image as shown in Figure 1(c) and its magnified view (inset of Figure 1(c)). The morphology of ZnO nanorods grown on sample 2 is shown in Figure 1(b). Here the silicon substrate was found to be densely covered with the perpendicularly grown well-aligned ZnO nanorods. This was confirmed from the cross-sectional SEM image (Figure 1(d)) and its magnified view (inset).
The various morphologies for the sol-gel using KOH-based seed layer and monoethanolamine-based seed layer-derived ZnO nanorods can be attributed (i) to the different physiochemical properties of the monoethanolamine-based and KOH-based seed solutions of zinc acetate dihydrate in 2-methoxyethanol and methanol, respectively. The monoethanolamine-based seed solution was thicker than the KOH-based seed solution. MEA and KOH components probably provided the required basicity to the seed solutions. The monoethanolamine-based seed solution was more homogeneous and stable than that of KOH-based seed solutions when left for long time. This might be due to the limited solubility of both zinc acetate dihydrate and KOH in methanol. The longer stability and homogeneity of the 2-methoxyethanol solution was probably due to the stabilizing property of monoethanolamine. The different thickness of the two seed solutions produced different type of crystal and thus different ZnO nanorods on silicon substrates. (ii) When the quantity of alkali was small, fewer particles were appeared as reported in the literature . Due to the coordination effect of OH− ions to Zn2+ ions, it is possible that OH− ions are adsorbed at the circumference of Zn ions of the ZnO nuclei. Due to the spatial hindrance, ZnO grew only along certain directions . The ZnO seed crystals in monoethanolamine-based solution were bigger and more oriented than those in KOH-based seed solutions. Moreover, the diameter of grown ZnO nanorods can be determined from the size of the crystal grains of seeded ZnO . It was also reported earlier that growth of ZnO nanorods was dependent on the roughness and thickness of the seed layers. The seed layer with more rough surface and higher length can provide conditions to form the nuclei easily .
Figures 2(a) and 2(b) show the XRD patterns of the ZnO nanorods obtained from sample 1 and sample 2. It consisted of several peaks at (0 0 2), (1 0 1), (1 0 2), (1 0 3) and (1 1 2) planes. All the diffraction peaks were indexed to the hexagonal structure of the ZnO according to JCPDS card No. 036-1451. The lattice constants were calculated using the following relations: The values for “” were calculated using the following relation: whereas the particle size was calculated by using the Scherer’s equation as follows: The calculated values for lattice constant, planner distance and crystallite size at “0 0 2” peaks are tabulated in Table 1.
The strongest peak (0 0 2) at and 34.57° with full-width half-maximum (FWHM) of 0.1246° and 0.172° for sample 1 and sample 2, respectively, showed good quality crystals oriented at -axis. The approximately 10 times lower intensity magnitude of nanorod ZnOs for sample 1 over that of sample 2 suggested that the sample 2 produced better quality crystal structures.
No other peaks of impurities such as zinc nitrate hexahydrate and hexamethyltetramine were observed in the spectra. The possible enhancement in the crystal quality of nanorod ZnOs using monoethanolamine-based seeded layers might be due to strain relaxation. It was found that first 10 to 40 min was the deciding factor for the ultimate diameter of nanorod ZnOs. The interface free energy of the seed grains and growth solution was less than the crystal-vapour interface which might occur during the growth of rods. The high-interface free energy of the crystal-vapour interface could be due to the residual strains which are correlated to the heating history of growth process . It is the strain relaxation which was responsible for the increased diameter of the nanorods.
Figure 3 shows the Raman scattering spectra of the nanorod ZnOs produced on sample 1 and sample 2. The spectra were collected by exciting laser line at 488 nm with excitation power of 20 mW.
One sharp peak at 520 cm−1 and two weak peaks at 302 cm−1 and 620 cm−1 can be conferred to the TO phonon mode originating from silicon substrate . The peak which appeared at 438 cm−1 with significantly high intensity is a typical characteristic of hexagonal wurtzite ZnO. The intensity of this peak was increased in both the cases but the intensity is higher in comparison to the sample 1. This peak was assigned to the Raman active optical phonon of E2H mode . A weak peak that appeared at 327 cm−1 was assigned to multiphonon scattering process (E2H-E2L) . Raman analysis also satisfied the XRD results, confirming the better quality of ZnO crystals in sample 2.
To study the optical characteristics of nanorod ZnOs, photoluminescence spectroscopy was carried out on both the samples at room temperature. The typical spectra for the photoluminescence for both the samples are shown in Figure 4. The photoluminescence spectra demonstrated a strong UV emission at 382 nm and a visible emission at 567 nm. This UV band was due to the recombination of free excitons through an exciton-exciton collision process. It was documented that deep-level emissions are associated with the singly ionized oxygen vacancy in ZnO and results from the recombination of a photogenerated hole with the singly ionized charge state of this defect .
Usually, the visible emission from ZnO is attributed to different defects such as oxygen vacancies (VO), zinc vacancies (VZn) or a complex defect involving interstitial zinc (Zni), and interstitial oxygen (Oi) . The intensity of visible peak of sample 2 is lower as compared to the intensity of sample 1. The decrement in the intensity of visible region as well as higher UV/Vis ratio for sample 2 suggests that sample 2 has good crystallinity. The photoluminescence results satisfied the above results of XRD and PL that sample 2 has better crystallinity than that of sample 1.
Figure 5 shows the current to voltage (I-V) characteristic curves of nanorod ZnOs for sample 1 and sample 2. It was observed that sample 1 has higher conduction as compare to sample 2. This was conferred to the higher polarity of potassium hydroxide over monoethanolamine. The turn on voltage for sample 1 was approximately 1.5 volts whereas that for sample 2 was around 2.5 volts, suggesting that both the structures can be used for the optoelectronic devices with some differences in power ratings. For faster switching and less operating voltages, sample 1 was better performing, suggesting its applications in low power-consuming devices.
Nanorod ZnOs of two different morphologies and opto-electric properties were successfully synthesized on two different seeded layered silicon substrates. While the better crystal quality, fewer structural defect and better aligned ZnO nanorods were obtained through monoethanolamine-based sol-gel method, better electrical conductivity was found in nanorod ZnOs derived through KOH-based sol-gel methods. Thus KOH-based sol-gel method should be selected for synthesizing nanorod-ZnOs for power-saving optoelectrical devices. On the other hand, better aligned, better crystalline, and fewer defects in monoethanolamine-based sol-gel derived nanorod-ZnOs suggest their potential applications in optoelectronic devices of higher longitivity and stability.
The author would like to acknowledge the financial support for the FRGS Grant number (9003-00276) from Ministry of higher education (MOHE). The author would also like to thank the technical staff of Institute of Nano Electronic Engineering and School of Microelectronic Engineering, Universiti Malaysia Perlis for their kind support to smoothly perform the research.
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