Synthesis of Fe-Doped ZnO Nanorods by Rapid Mixing Hydrothermal Method and Its Application for High Performance UV Photodetector

Chey, Chan Oeurn; Masood, Ansar; Riazanova, A.; Liu, Xianjie; Rao, K. V.; Nur, Omer; Willander, Magnus

doi:https://doi.org/10.1155/2014/524530

Journal of Nanomaterials

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Research Article | Open Access

Volume 2014 | Article ID 524530 | https://doi.org/10.1155/2014/524530

Synthesis of Fe-Doped ZnO Nanorods by Rapid Mixing Hydrothermal Method and Its Application for High Performance UV Photodetector

Chan Oeurn Chey,¹Ansar Masood,²A. Riazanova,²Xianjie Liu,³K. V. Rao,²Omer Nur,¹and Magnus Willander¹

Academic Editor: Fathallah Karimzadeh

Received04 Jul 2014

Revised16 Sept 2014

Accepted11 Oct 2014

Published06 Nov 2014

Abstract

We have successfully synthesized Fe-doped ZnO nanorods by a new and simple method in which the adopted approach is by using ammonia as a continuous source of for hydrolysis instead of hexamethylenetetramine (HMT). The energy dispersive X-ray (EDX) spectra revealed that the Fe peaks were presented in the grown Fe-doped ZnO nanorods samples and the X-ray photoelectron spectroscopy (XPS) results suggested that Fe³⁺ is incorporated into the ZnO lattice. Structural characterization indicated that the Fe-doped ZnO nanorods grow along the c-axis with a hexagonal wurtzite structure and have single crystalline nature without any secondary phases or clusters of FeO or Fe₃O₄ observed in the samples. The Fe-doped ZnO nanorods showed room temperature (300 K) ferromagnetic magnetization versus field (M-H) hysteresis and the magnetization increases from 2.5 μemu to 9.1 μemu for Zn_0.99Fe_0.01O and Zn_0.95Fe_0.05O, respectively. Moreover, the fabricated Au/Fe-doped ZnO Schottky diode based UV photodetector achieved 2.33 A/W of responsivity and 5 s of time response. Compared to other Au/ZnO nanorods Schottky devices, the presented responsivity is an improvement by a factor of 3.9.

1. Introduction

Diluted transition metals (TMs) doped ZnO nanomaterials result in changing of the structural, electrical, magnetic, and optical properties of ZnO nanostructures. Transition metal doped ZnO especially is promising material as a room temperature ferromagnetic diluted magnetic semiconductors. Therefore, TMs doped ZnO nanomaterials are of interest in many current and future applications such as nanoelectronics, optoelectronics, photonic devices, spin electronics applications, and sensor devices, for example, spin-based light-emitting diodes, UV sensors, spin transistors, nonvolatile memory, and ultrafast optical switches [1–7]. Among the TMs doped ZnO nanomaterials, Fe-doped ZnO nanorods are of great potential in many applications due to the excellent electronic, magnetic, and optical properties [8]. The doping of semiconductor materials prepared by different methods or by the same method but different preparation processes usually shows different properties. New device applications of Fe-doped ZnO nanomaterials have attracted many researchers to synthetize this material using many different physical and chemical methods. Many methods have been used to synthesize Fe-doped ZnO nanomaterial with different morphologies which has been published in the literature. To mention some, Fe-doped ZnO nanoparticles were prepared by the coprecipitation method [9–11], while Fe-doped ZnO powders and Fe-doped ZnO nanorods array have been synthesized via other high temperature methods [12, 13]; Fe-doped ZnO thin films were deposited by sputtering and spin coated methods [14–23], and Fe-doped ZnO nanorods were grown by the hydrothermal methods [24–27]. Among the different growth methods, the hydrothermal methods are favorable, friendly, and attractive due to simplicity, low cost, being less hazardous, scale-up possibility, and they are performed at low temperature (lower than 100°C). Furthermore, the latest property is advantageous since it can be used to grow ZnO nanostructures on flexible and foldable substrates. Moreover, the morphology and properties of ZnO nanostructures can be controlled by varying the growth conditions such as the temperature, growth time, precursor concentration, and the pH of the growth solution [28, 29].

In this work, Fe-doped ZnO nanorods were synthesized by a modified preparation procedure using the low temperature hydrothermal approach. The Fe-doped ZnO nanorods growth developed here represents a new and simple method which adopted approach by using ammonia as a continuous source of for hydrolysis during the growth instead of hexamethylenetetramine (HMT). Morphology, chemical composition, and structural and room temperature magnetic properties of the Fe-doped ZnO have been investigated. Finally, a simple Au/Fe-doped ZnO Schottky diode based UV photodetector was fabricated and IV characteristic and time-dependent photoresponse have been conducted under on/off UV illuminations. The performance of the UV photodetector based Au/Fe-doped ZnO nanorods Schottky diode with large detection area (1 cm²) has been studied.

2. Experiment Procedure

2.1. Growth of Fe-Doped ZnO Nanorods

Zinc nitrate hexahydrate (ZnNO₃·6H₂O), iron (II) chloride tetrahydrate (FeCl₂·4H₂O), and iron (III) chloride hexahydrate (FeCl₃·6H₂O) were used as precursors. All chemicals were purchased from Sigma Aldrich and were used without further purification. The growth solution was prepared by the mixing of 0.075 M of zinc nitrate hexahydrate anda specific concentration of the iron source prepared by Iron (II) chloride tetrahydrate and Iron (III) chloride hexahydrate with the ratio ([Fe⁺²] : [Fe⁺³] = 1 : 2) in deionized water. Then the growth solution was subsequently stirred with a magnetic stirrer at room temperature for one hour and then ammonia solution is added dropwise to the growth solution at room temperature, resulting in an orange solution with a pH = 9.3. This solution was kept under magnetic stirring for one hour at room temperature. The substrates were cleaned with isopropanol in an ultrasonic bath and then spin coated three times with a seed solution containing zinc acetate at 2500 rpm for 30 s; then the samples were annealed at 120°C for 10 minutes. Finally, the substrates were placed horizontally in the growth solution and kept in a preheated oven at 90°C for 6 hours. After the growth duration is completed, the samples were collected and washed with deionized water and dried at room temperature for further characterization. We believe that synthesis of high quality of Fe-doped ZnO nanorods can be useful for nanotechnology applications. In this adopted approach, ammonia was used to tailor pH of the growth solution and to facilitate ZnO nanocrystals growth. Ammonia reacts with water to provide continuous source of OH⁻ required for hydrolysis and aid precipitation of final products. Furthermore, ammonia can generate a large amount of zinc ammine complexes immediately in the solution and these complexes are absorbed on the six side planes of ZnO nanorods, which can facilitate the growth of ZnO nanorods structure by slowing down the growth velocity of the side surfaces [30]. By increasing the ammonia content in the growth solution, the nuclei of ZnO nanocrystals can rapidly form on the substrates, which produces dense and long ZnO nanorods over a large area [31, 32]. Therefore, high ammonia contents as additive to hydrolyze in the growth solution provide Fe ions doped in ZnO nanorods without morphology deformation.

2.2. Characterization Process

The field emission scanning electron microscope (FESEM), EDX, XPS, and XRD are used to characterize the surface morphology, chemical composition, and crystal structural of the grown samples, while the room temperature ferromagnetic properties were investigated by superconducting quantum interference device (SQUID) measurements.

2.3. Device Fabrication Process

For the fabrication of the Au/Fe-doped ZnO nanorods UV photodetector, transparent FTO film was taped on the top of the Fe-doped ZnO nanorods grown on gold coated glass substrate. The schematic diagram of the simple UV photodetector based on large area Au/ZnO nanorods/FTO Schottky diode is shown in Figure 1. In a UV photodetector, large Schottky barrier height at metal semiconductor interface results in improved responsivity and improved photocurrent to dark current ratio [33, 34]. Therefore, Au with high work function was used to form a large Schottky barrier height on Fe-doped ZnO nanorods. The conducting FTO film was used as the ohmic contact due to its transparency and it also provides almost ideal ohmic contact with n-ZnO [35]. The current-voltage (I-V) curves of the fabricated diodes under dark and under UV illumination were measured by Agilent 4155B Semiconductor Parameter Analyzer. In this experiment, a constant UV illumination of 2 mW/cm² emitting at 365 nm was used as the excitation source.

3. Results and Discussion

3.1. Morphology and Chemicals Composition

The surface morphology of the grown Fe-doped ZnO nanorods under different doping concentration has been performed by using SEM. Figures 2(a) and 2(b) show the SEM images of the 1% and 5.0% Fe-doped ZnO nanorods, respectively. The Fe-doped ZnO nanorods have hexagonal shapes with diameters varying between 100 and 300 nm. The chemical composition of the grown Zn_0.99Fe_0.01O was measured by using EDX which is shown in Figure 2(c). The EDX data revealed that the Fe’s peaks were at 0.705 keV, 6.404 keV, and 7.058 keV. This indicates the Fe ions were presented in the Fe-doped ZnO nanorods samples.

(a)

(b)

(c)

In order to verify the substitutions of the Fe ions in the nanorods, XPS measurements were performed. Figure 3(a) shows the XPS spectra of O 1s peaks of both ZnO nanorods and Fe-doped ZnO nanorods. For ZnO nanorods, the O 1s spectrum centered at 530.9 which belongs to O²⁻ in the wurtzite structure of a ZnO monocrystal and at 532.3 eV is attributed to the presence of loosely bound oxygen on the surface [15, 17]. In Fe-doped ZnO nanorods, the XPS spectra of the O²⁻ were slightly shifted to the higher binding energy value and the shoulder peaks are broader in comparison to the pure ZnO nanorods. This result indicates that the Fe ions indeed influence the optical properties of the ZnO nanorods. The chemical shift of the O 1s of the doped ZnO has also been revealed in the previous works [22, 27]. As we know, the binding energy of Fe 2p signals was between 700 and 740 eV and some of Zn Auger peaks are also presented in this region. Therefore, the XPS measurements were conducted for both ZnO nanorods and nanorods. As it is known, the FeO has a peak position of Fe 2p_1/2 at 722.3 eV and Fe 2p_3/2 at 709.3 eV and Fe₂O₃ at 724.9 eV and at 710.5 eV, respectively. In this study, the XPS signals at binding energy from 695 eV to 735 eV for pure ZnO and Fe-doped ZnO are shown in Figure 3(b). From this figure, the Fe related signal in the Zn_0.99Fe_0.01O nanorods is not resolved from the Zn Auger because it is relatively small. This is a very similar case for the Fe-doped ZnO in the previous works [20, 26]. However, the Fe 2p core level photoemission spectrum for Zn_0.95Fe_0.05O nanorods is clearly observed, from which Fe 2p_1/2 and Fe 2p_3/2 peaks located at 725.47 and 711.7 eV can be found. These Fe 2p peak positions are almost the same as values which have been reported in many previous works [15, 17, 19–24, 26, 27]. These obtained binding energies are larger than Fe³⁺; it is suggested that Fe is incorporated into the ZnO lattice in a state close to Fe³⁺. Furthermore, the investigated spectra of Fe 2p showed that the spin-orbit split energy difference between Fe 2p_1/2 and Fe 2p_3/2 is 13.77 eV. These results suggested that there is no possibility of existence of Fe²⁺ or Fe⁰ in the samples because the energy difference of metallic ion and the FeO should be 13.10 eV and 13.4 eV, respectively [20].

(a)

(b)

3.2. Structural Characterization

The XRD patterns of the undoped ZnO nanorods, Zn_0.99Fe_0.01O and Zn_0.95Fe_0.05O nanorods, are shown in Figure 4(a). The high diffraction peaks at 002 direction are an indication of the hexagonal wurtzite structure with single crystalline nature and they indicate that the Fe-doped ZnO nanorods grow along the c-axis of the ZnO consistent with the JCPDS number 36-1451 file. No evidence of any other secondary phase such as FeO or Fe₃O₄ has been observed. In Figure 4(b), we observed that the peaks position at 002 direction was shifted towards higher diffraction angle with the increasing of the Fe concentration and their full width at half maximum (FWHM) were also becomes larger while increasing the Fe concentration. The shift of the peaks positions and the relatively larger FWHM clearly indicated that the Fe ions replaced the Zn sites in the ZnO nanorods crystal matrix. These observations were also evident in similar samples grown by other techniques reported elsewhere [10, 11, 14, 17–20, 24, 25].

3.3. Magnetic Property

Superconducting quantum interference device (SQUID) measurements have been performed to investigate the room temperature ferromagnetic behavior of our Fe-doped ZnO nanorods samples. Figure 5 shows the magnetic hysteresis (M-H) curves measured from −10 to 10 kOe at 300 K of Fe-doped ZnO samples. From these M-H curves, the room temperature ferromagnetic hysteresis loops are clearly observed. According to theory, Fe-doped ZnO possesses ferromagnetic property at room temperature and the magnetic moments observed are due to the Fe 3d orbitals and the observed magnetization value increases with the increase of the Fe concentration [15–17, 20, 22, 24, 25]. This supports our experimental results since we observed magnetic hysteresis at room temperature and the magnetization values observed increase from 2.5 to 9.1 for Zn_0.99Fe_0.01O and Zn_0.95Fe_0.05O, respectively. This M-H loop is higher than the results reported in [21, 36]. As we see from the EDX spectra, XPS spectra, and XRD patterns of our samples, it is clearly shown that there was not any other secondary phase of Fe or Fe oxides that has been observed. Therefore, the observed room temperature ferromagnetism in our Fe-doped ZnO nanorods originates from the Fe ions substituting the Zn ions in the ZnO nanorods matrix.

3.4. UV Sensor Based Au/Fe-Doped ZnO Schottky Diode

The I-V characteristics for both the undoped ZnO and the Fe-doped ZnO Schottky diodes were investigated under dark and UV illumination. Figure 6(a) shows I-V characteristics of undoped ZnO and Zn_0.95Fe_0.05O Schottky diodes under dark. It was observed that both Schottky diodes have good rectifying characteristics. However, the Au/Zn_0.95Fe_0.05O Schottky diode has smaller leakage current, smaller turn on voltage with higher current at forward bias voltage than Au/ZnO Schottky diode. Without UV illumination, the observed dark current was approximately 1.62 mA and 3.56 mA at bias of 5 V for the Au/ZnO Schottky and the Au/Zn_0.95Fe_0.05O, respectively. This high dark current indicated that the Fe-doped ZnO nanorods have intrinsic donor defects which generates many free electrons and enhanced the dark conductance [37]. Figures 6(b) and 6(c) show the dark and UV illuminated I-V characteristics of the Au/Zn_0.95Fe_0.05O Schottky diode and Au/ZnO Schottky diode, respectively. The responsivity () of the photodetector is given by [38–41] where is the photocurrent and is the incident optical power at a given wavelength (). The responsivity values calculated at 5 V forward bias are 0.60 A/W for Au/ZnO Schottky diode and 2.33 A/W for Au/Zn_0.95Fe_0.05O Schottky diode. The responsivity value of Au/Zn_0.95Fe_0.05O is also higher than the commercial GaN UV detector (0.1 A/W) and other photodetectors reported in [38–43] and it is comparable to the UV photodetector reported [44]. The responsivity ratio between Au/Zn_0.95Fe_0.05O Schottky diode and Au/ZnO Schottky diode is equal to 3.9 and it is given by where and are the responsivity of the Au/Zn_0.95Fe_0.05O Schottky diode and Au/ZnO Schottky diode, respectively. The device based Au/Zn_0.95Fe_0.05O gives higher responsivity because when Fe ions incorporated into the ZnO lattice, it acts as a donor which contributes to carriers and consequently improve its optical property, which possesses more electron-hole pairs generated under UV excitation. Therefore, the incremental mobility of the Zn_0.95Fe_0.05O nanorods exhibits higher values compared to ZnO nanorods. Figures 6(d) and 6(e) show 5 s and 7 s of rising time response for Au/Zn_0.95Fe_0.05O Schottky and Au/ZnO Schottky diodes, respectively. While the decaying time is approximately 29 s for both devices, the rising time response is defined as the times required for the photocurrent reaching 63.3% of its saturated photocurrent and the decaying time response is refereed to 36.7% of its saturated photocurrent.

(a)

(b)

(c)

(d)

(e)

4. Conclusion

In summary, a series of high quality single crystalline of Fe-doped ZnO nanorods has been successfully synthesized using a modified hydrothermal method. A systematic study was performed to investigate the morphology and structural and magnetic properties of the Fe-doped ZnO nanorods. Finally, the grown Fe-doped ZnO was used to fabricate high performance UV photodetector. SEM results show that the Fe-doped ZnO nanorods have hexagonal shapes and the EDX data revealed that the Fe peaks were presented in the Fe-doped ZnO nanorods samples and the XPS results suggested that Fe³⁺ is incorporated into the ZnO lattice. The XRD analysis showed that by increasing the concentration of the Fe in the growth solution the 002 peak position and the FWHM were shifted to higher angle and become relatively larger, respectively. It is also shown that the Fe ions replaced Zn sites and were incorporated into the ZnO matrix with no secondary phases or clusters of FeO or Fe₃O₄ observed in the grown samples. The substitution of the Fe ions in the ZnO nanorods matrix significantly was manifested in a clear ferromagnetic behavior at room temperature (300 K) and the magnetization magnitude was observed to increase from 2.5 to 9.1 for Zn_0.99Fe_0.01O and Zn_0.95Fe_0.05O, respectively. Moreover, the fabricated Au/Fe-doped ZnO nanorods UV photodetector device achieved both high photoresponse and fast time response. Compared to Au/ZnO nanorods Schottky device, an improvement by a factor of 3.9 was achieved.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgment

We wish to thank project grants from Carl Tryggers Stiftelsen, and Hero-M Vinnova center of Excellence at KTH. We wish also to thank ISP, Uppsala University.

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Copyright © 2014 Chan Oeurn Chey 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.

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