Aluminum- and Iron-Doped Zinc Oxide Nanorod Arrays for Humidity Sensor Applications

Abstract

Metal-doped zinc oxide (ZnO) nanorod arrays have attracted much attention due to improvement in their electrical, structural, and optical properties upon doping. In this chapter, we discuss the effects of aluminum (Al)- and iron (Fe)-doping on ZnO nanorod arrays properties particularly for humidity sensor applications. Compared to Fe, Al shows more promising characteristics as doping element for ZnO nanorod arrays. The Al-doped ZnO nanorod arrays showed dense arrays, small nanorods diameter, and high porous surface. The I-V characteristics showed that Al-doped sample possesses higher conductivity. From the humidity sensing performance of the samples, Al-doped ZnO nanorod arrays possess the superior sensitivity, more than two times higher than that of the undoped ZnO nanorod arrays sample, demonstrating great potential of Al-doped ZnO nanorod arrays in humidity sensor applications.

1. Introduction

Zinc oxide (ZnO) has been the subject of extensive investigations for many decades. A stable hexagonal wurtzite structure of ZnO consists of tetrahedrally coordinated four –O or four –Zn atoms, having lattice constant of ɑ = 3.25 Å and c = 5.2 Å with ratio c/ɑ = ~1.60 close to ideal hexagonal cell (1.633) [1]. Figure 1 shows the ball and stick illustration of the hexagonal wurtzite structure of ZnO [1]. The ZnO structure does not have the center of symmetry.

Figure 1.

The illustration of the hexagonal wurtzite structure of ZnO.

ZnO is abundantly available in nature as a mineral zincite, although most of the commercial ZnO samples are prepared through synthetic approaches. Owing to its interesting properties, such as a wide energy band gap of 3.37 eV, large exciton binding energy of 60 meV, good chemical and thermal stabilities, non-toxicity, and high transparency [2–5], ZnO has been applied in various applications such as textiles [6], medicines [7, 8], optoelectronic devices [9], solar cells [10, 11], and sensors [12, 13]. Other promising aspect of ZnO includes its ease of fabrication leading to generation of various kinds of nanostructures such as nanorods [14], nanowires [15], nanoflowers [16], and nanospheres [17]. Among them, one-dimensional (1-D) nanostructures (i.e., nanorods and nanowires) are more favorable in humidity sensor applications due to a higher surface-to-volume ratio, providing direct charge transport along the ZnO arrays and reducing the electron-hole pair recombination possibilities [18, 19]. These characteristics are crucial in fabricating high-performance humidity sensors. The performance of humidity sensor can be enhanced by introducing impurities to ZnO crystal through the doping process. As reported in previous studies, the doping process is capable of altering electrical conductivity, photocatalytic activity, and magnetic properties of ZnO [20–23]. In this chapter, we discuss recent developments in metal-doped ZnO, particularly in relation to the advantages of nanostructure-based humidity sensors. The preparation of Al- and Fe-doped ZnO nanorod array-based humidity sensors using the sol-gel immersion method is also included here followed by characterization of the structural, optical, and electrical properties of the fabricated humidity sensors.

2. Metal-doped ZnO

Doping is a process of introducing extrinsic elements into intrinsic structure for the purpose of improving and altering their basic properties such as structural, optical, and electrical. This process is crucial for various materials especially semiconductors since intrinsic semiconductor is known to possess deficiencies such as low carrier concentrations and lagging change in resistance values for humidity sensing applications [24, 25]. From the literature, ZnO was reported to be doped with numerous kinds of elements [26–29]. For instance, Kim et al. reported on the fabrication of yttrium (Y)-doped ZnO nanorod arrays quantum dot (QD) synthesized solar cell using the chemical bath deposition method [30]. Due to Y-doping, the nanorod diameters were significantly reduced. In addition, the absorption coefficients of the films also improved after doping due to higher QD deposition. The conductivity of the film was improved when the concentration of doping was 50 mM. They also observed that the undoped ZnO nanorod arrays possess poor solar cell characteristics than that of the 50 mM Y-doped ZnO nanorod arrays sample. The substitution of the Y atom in ZnO lattice was expected to affect the transport properties of electrons by blocking the recombination process and increased the carrier concentration.

In another work, Kim et al. studied the fabrication of hydrophobic Al-doped ZnO nanorod arrays solar cell using the hydrothermal method [31]. In this study, they varied the concentration of Al dopant and controlled the growth period. The average diameters were significantly reduced when doped with Al. In addition, they reported that the undoped sample has higher hysteresis than that of Al-doped samples and the Al-doped ZnO nanorod arrays have a high self-cleaning performance. Meshki et al. fabricated Fe-doped ZnO nanorod arrays for two kinds of drug detection, namely, sulfamethoxazole and sulfamethizole [32]. When the nanorods were doped with Fe, the crystallite size of the ZnO nanorod arrays film was slightly decreased. The Fe-doped ZnO nanorods acquired a larger surface area than undoped ZnO nanorods, which likely led to the enhancement of electron transfer to the electrode surface.

In other research, Anbia and Fard fabricated a cerium (Ce)-doped ZnO nanoporous thin film humidity sensor using the screen printed method [33], in which they reported changes in humidity-sensing performance with doping and different sintering temperature. From their research, the Ce-doped ZnO thin film acquired smaller diameter of nanoparticles with a high porous surface. They also found that the Ce-doped ZnO film has better sensitivity to humidity than that of the undoped ZnO film. Peng et al. fabricated manganese (Mn)-doped ZnO nanopowders for humidity sensing application [34]. Based on their study, the undoped ZnO nanopowders possess larger nanoparticles and have low porosity. Upon Mn doping, the nanoparticle size is reduced with higher porous surface. As the concentration of Mn increased, the sensitivity of the ZnO nanopowders to humidity also increased, clearly higher than the undoped ZnO powder. They expected such behavior to occur due to higher H⁺ ion density on the ZnO nanopowders surface and also higher concentration of defects with associated with oxygen vacancies.

From the above summary of the reported results, it is evident that doping is essential and very important for improving the useful properties of pristine ZnO structure. The improvements such as reduced crystallite size (increase surface area), high-quality surface structure, better photoluminescence properties, lower surface resistance, and high concentration of free carrier enhance the efficiency of the ZnO-based devices.

3. ZnO nanostructure-based humidity sensors

Humidity sensors have an important function in various situations, such as in industrial processing, agriculture, and environmental control since an uncontrolled amount of humidity can be quite damaging to certain materials and processes [35]. Humidity sensors can be based on different sensing techniques, such as resistive, capacitive, optics, field effect transistor (FET), quartz crystal microbalance (QCM), and surface acoustic wave (SAW) [36–40]. Resistive-type humidity sensors are often preferred since they are easy to fabricate, have low cost, and have reliable response [41]. ZnO nanostructures have been widely studied for humidity sensing applications since it is highly sensitive to humidity. For example, Hendi et al. investigated the effect of different concentrations of an Sn-doped ZnO-based QCM humidity sensor [42]. They found that the crystallite sizes decrease when doped with Sn and the performance of the QCM humidity sensor improved when doped with Sn. Zhao et al. [43] have fabricated gallium (Ga)-doped ZnO nanowires piezo-humidity sensor using hydrothermal method. At low concentration of doping, they reported that the nanowires possess a small average diameter and doping with Ga helped to increase the oxygen vacancies and generate more free carriers, which in turn changed the piezoelectric screening effect and improved the water molecules adsorption. These results showed that Ga-doped ZnO nanowires yielded higher response to humidity compared to undoped ZnO nanowires.

The nano-scale structure in ZnO is very important in humidity detection due to larger surface-to-volume ratio and chemically reactive surface. According to Hsu et al. [44], the nanostructured surface of ZnO consists of high concentrations of oxygen vacancies, which provides highly active sites for water molecules adsorption. In their study, they fabricated ZnO dandelion-like nanostructures using a two-step thermal oxidation method, reporting increment in oxygen vacancies as the deposition temperature increased, which in-turn led to enhancement of humidity sensitivity.

High surface area is one of key factors that determines the high performance of a humidity sensor. The basic mechanism of a humidity sensor involves water molecules getting attached to the ZnO surface following the Grotthuss chain reaction [45]:

$2{\text{H}}_{\text{2}}\text{O}\to {\text{H}}_{\text{3}}{\text{O}}^{\text{+}}+{\text{OH}}^{-}$ E1

${\text{H}}_{\text{3}}{\text{O}}^{+}\to {\text{H}}_{\text{2}}\text{O}+{\text{H}}^{+}$ E2

The source of charge carriers is from the protonic transfer (H⁺) among hydronium ions (H₃O⁺) which is known by the term proton hopping. A higher surface area offers more surface reactions between the sensing element and water molecules leading to a greater number of carriers. This behavior was observed by Hong et al. when preparing ZnO nanorod arrays on top of the gallium (Ga)-doped ZnO seed layer film through the hydrothermal method [46]. They suggested that the increment concentrations of Ga in the ZnO seed layer film increased the thickness but reduced the nanorod diameter, resulting in an increased surface area of the nanorod arrays film and hence higher sensitivity for humidity detection.

4. Synthesis of zinc oxide nanorod arrays

For the synthesis of ZnO nanorod array films, a number of approaches have been reported. For instance, Ye et al. synthesized the sodium (Na)-doped ZnO nanorods on silicon (Si) substrate using the chemical vapor deposition method [14] and studied the effects of Na concentrations on the ZnO nanorod properties. The growth of ZnO nanorods was done at 1000°C and 1800 Pa of temperature and pressure, respectively. Based on their report, the synthesized nanorods have a small diameter but they are not well aligned. In the report by Li et al. [47], the nanorod film was prepared with different dopants (Ga and Indium (In)) using the hydrothermal method on top of the ZnO seed layer-coated glass substrate. The purpose of their study was to investigate the influence of hydrogen annealing on the structural and luminescence properties of the ZnO nanorods. Through the preparation process, the nanorods were grown on the substrate with poor orientation and not aligned. According to them, the roughness of nanorods surface was increased due to thermal decomposition of the unstable surface status of polar and nonpolar faces of the ZnO structure. In the work by Son et al [48], the chemical bath deposition method was used to study the effect of seed layer thickness which was sputtered on Si substrate to the nanorod growth. Their results showed that the nanorods grew in a nonuniform manner in that the thickness and diameters of the nanorods were not uniform. However, higher thickness of the seed layer film produced nanorod arrays with better uniformity and alignment on the substrate.

From a review of the above-cited examples, it is evident that an ideal preparation of high-quality nanorod arrays does not necessarily depend on high-applied temperature and pressure. Therefore, a simpler, lower cost, and low-energy consumption method would be preferable. In our study, the synthesis of Al- and Fe-doped ZnO nanorod arrays was accomplished using a simple sol-gel immersion method. The nanorod arrays were grown on top of glass substrate with Al-doped ZnO as a seeded catalyst layer. For the preparation of the ZnO seeded layer catalyst, 0.4 M zinc acetate dehydrate (Zn(CH₃COO)₂⋅2H₂O; 99.5% purity; Aldrich) was used as a precursor, 0.4 M mono-ethanolamine (MEA, H₂NCH₂CH₂OH; 99.5% purity; Aldrich) as a stabilizer, 0.004 M aluminum nitrate nonahydrate (Al(NO₃)₃.9H₂O; 98% purity; Analar) was used as a dopant source and 2-methoxyethanol as the solvent. The materials were mixed and then stirred on a hot plate stirrer at 80°C for 3 h and then aged for 24 h at room temperature to obtain a homogeneous solution. The prepared solution was spin coated at 3000 rpm for 1 min. The samples with coated film were then heated at 150°C for 10 min to dry and annealed at 500°C for 1 h.

The major interest of this study is the effect of Al and Fe doping on the intrinsic properties of ZnO. For the preparation of an undoped, Al-, and Fe-doped ZnO nanorod array film, 0.1 M zinc nitrate hexahydrate (Zn(NO₃)₂⋅6H₂O; 98.5% purity; Schmidt) was used as a precursor, 0.1 M hexamethylenetetramine (HMT, C₆H₁₂N₄; 99% purity; Aldrich) as a stabilizer, and 0.001 M of aluminum nitrate dehydrate (Al(NO₃)₃⋅9H₂O; 98% purity; Analar) and 0.001 M iron (III) nitrate nonahydrate (Fe(NO₃)₃⋅9H₂O; 98% purity; Merck) as dopant sources. The reagents were mixed and dissolved in 500 ml of deionized water and then sonicated at 50°C for 30 min before being stirred on a magnetic hot plate stirrer at room temperature for 3 h to age the solutions. After the ageing process, the solutions were poured in a Schott bottle placed with seed layer-coated glass substrates. The seed layer-coated glass substrates were immersed in a water bath immersion tank at 95°C for 2 h. Then, the sample was cleaned and heated at 150°C for 10 min before being annealed at 500°C for 1 h.

The configuration of doped and undoped ZnO nanorod array-based humidity sensors was completed by depositing gold (Au) metal contact using sputter coater on top of the samples as the electrode. The structural properties of the samples were characterized using field emission scanning electron microscopy (FESEM; JEOL JSM-7600F) and X-ray diffraction measurement (XRD; PANalytical X’Pert PRO). The optical properties of the samples were tested using a ultraviolet-visible-near-infrared (UV-vis-NIR; Varian Cary 5000) spectrophotometer. The electrical properties of the samples were characterized using two-point probe current-voltage (I-V; Advantest R6243) measurement. The performance of the humidity sensor of the fabricated sensors was analyzed using a humidity sensor measurement system (ESPEC-SH261). The schematics of preparation of doped and undoped ZnO nanorod array-based humidity sensors are shown in Figure 2.

Figure 2.

Schematics of the preparation of doped and undoped ZnO nanorod array-based humidity sensors.

5. Effects of aluminum and iron doping

The surface morphology, thickness, and the elemental analysis of the ZnO nanorod arrays were investigated using field emission electron scanning microscopy (FESEM) and energy-dispersive X-ray spectroscopy (EDS) as shown in Figure 3. Figure 3(a–c) shows the surface morphology of undoped and doped ZnO nanorod arrays taken at 30,000× magnification. It is observed that all samples produced have a hexagonal nanorod structure. The undoped sample has the largest average diameter of nanorod arrays of about 100 nm while Al- and Fe-doped ZnO-produced nanorod arrays have average diameters of 65 and 90 nm, respectively. Besides, the Al-doped ZnO nanorod array film is observed to possess higher porosity compared to undoped and Fe-doped samples. The reduction of nanorods size due to Al and Fe doping may be due to the smaller ionic radius of Al³⁺ (0.54 Å) and Fe³⁺ (0.64 Å) ions substituting the Zn²⁺ (0.74 Å) ion sites [49, 50]. The cross-sectional images of Al- and Fe-doped ZnO nanorod arrays are shown in Figure 3(d–f). The thickness of undoped, Al-, and Fe-doped ZnO nanorod arrays films was estimated to be 1.1, 0.67, and 0.75 μm, respectively. A slight decrement in thickness of doped samples may be due to difference in the ionic radius as mentioned earlier. From the EDS spectrum in Figure 3(g and h), it is evident that the doping elements of Al and Fe appeared in each sample. The atomic ratio of Zn, Al, and O is expected to be 54.93:0.71:44.86, respectively, while the atomic ratio of Zn, Fe, and O is 53.60:0.21:46.18, respectively.

Figure 3.

Surface morphology of (a) undoped, (b) Al-, and (c) Fe-doped ZnO nanorod array films that are prepared using sonicated sol-gel immersion. Cross-sectional images of (d) undoped, (e) Al-, and (f) Fe-doped ZnO nanorod array films. EDX spectrum of (g) Al- and (h) Fe-doped ZnO nanorod array films.

The XRD patterns of the undoped, Al-, and Fe-doped ZnO nanorod arrays for the 2θ range of 20–60° in Figure 4 show the four main peaks with Miller indices of (100), (002), (101), and (102). The dominant (002) peak indicates that the growth is along c-axis orientation. In addition, it is also noticed that the diffraction peak at (002) orientation for doped samples is slightly decreased, which indicated that the doping elements are successfully substituting the ZnO structure. The degradation in peak intensities for doped samples was expected due to the difference in ionic radii of Al³⁺ and Fe³⁺ than that of Zn²⁺ ions. The position of the (002) peak for the undoped, Al-, and Fe-doped ZnO nanorod arrays occurs at 2θ = 34.38, 34.49, and 34.44°, respectively, which can be used to determine the lattice constant c using the following equation valid for hexagonal structure [51, 52]:

Figure 4.

The XRD patterns of the undoped, Al-, and Fe-doped ZnO nanorod arrays.

$c=\frac{\lambda }{\sin \theta }$ E3

Here, λ = 1.54 Å is the X-ray wavelength of CuKα radiation. For the undoped, Al-, and Fe-doped ZnO nanorod arrays, c = 5.2108, 5.1947, and 5.2020 Å, respectively, was determined. The crystallite sizes, D of the undoped, Al-, and Fe-doped ZnO nanorod arrays, were calculated using the Scherrer formula [53]:

$D=\frac{K\lambda }{\beta \cos \theta }$ E4

Here, K is a constant (0.94), and β is the full-width at half-maximum (FWHM) in radians. The (002) peak was used for the calculation of D for which the values of β of the undoped, Al-, and Fe-doped ZnO nanorod arrays are 0.2831, 0.3045, and 0.3037°, respectively. The D values of the undoped, Al-, and Fe-doped ZnO nanorod arrays were estimated to be 30.7, 28.5, and 28.6 nm, respectively. Thus, the values of c and D of the undoped ZnO nanorod arrays are lowered when doped with Al and Fe. According to Khuili et al. [54], lattice parameters ɑ and c of Al-doped ZnO are smaller than those for undoped ZnO due to substitution of smaller Al³⁺ ions into ZnO lattice, which is also confirmed by the simulated supercell structure. Yue et al. noted that the shrinkage of lattice constant and crystallite size when doped with Fe was due to the smaller ionic radius of Fe³⁺ compared to that of Zn²⁺ ions [50]. Bai et al. also found that the diffraction peak positions of ZnO have shifted to higher angles when doped with Fe, which might lead to reduction of lattice constant and crystallite size [55].

The optical properties of undoped and doped ZnO nanorod arrays were determined using UV-Vis-NIR spectrophotometer measurements between 350 and 800 nm at room temperature. Figure 5 shows the transmittance properties of undoped, Al-, and Fe-doped ZnO nanorod arrays. The transmission decreases significantly at approximately 380 nm, which is attributed to the intrinsic ZnO band gap because of the direct transition of electrons between the edges of the valence band to the conduction band. From the spectra, average transmittances of undoped, Al-, and Fe-doped ZnO nanorod arrays were estimated to be 78.59, 76.96, and 75.10%, respectively. All doped samples exhibit a decrement in transmittance compared to the undoped sample. Previous studies reported that the transmittance decreased with Al and Fe doping [56, 57]. Such behavior occurred due to reduction of crystalline properties, which can be observed from the XRD data, and also due to enhancement of optical scattering by grain boundaries [57].

Figure 5.

Transmittance properties of the undoped, Al-, and Fe-doped ZnO nanorod arrays.

Figure 6 shows the I-V characteristics of undoped, Al-, and Fe-doped ZnO nanorod arrays. The I-V curves indicate that the nanorod arrays exhibit ohmic behavior, and the current increases with increasing voltage supplied for the nanorod arrays. The conductivity of the film, σ, was determined using the following equation [51]:

Figure 6.

I-V plot for the undoped, Al-, and Fe-doped ZnO nanorod arrays.

$\sigma =\frac{1}{\rho }\mathrm{ },$ E5

where ρ is the resistivity that can be expressed as

$\rho =\left(\frac{V}{I}\right)\frac{wt}{l}\mathrm{ },$ E6

where V is the supplied voltage, I is the measured current, t is the film’s thickness, w is the electrode width, and l is the length between the electrodes. The active area of the thin films is 3 × 10⁻⁶ m². The conductivity of undoped, Al-, and Fe-doped ZnO nanorod arrays is 0.08, 0.80, and 0.64 S cm⁻¹, respectively. It is observed that the conductivity of the nanorod array film significantly increased after doping. When ZnO was doped with Al³⁺ ions, the generation of free carriers is as follows [58]:

${\text{Al}}_{\text{2}}{\text{O}}_3\to {\text{Al}}_{\text{Zn•}}+2{\text{O}}_{\text{o}}+\frac{1}{2}{\text{O}}_{\text{2}}+2e^{\prime }$ E7

where Al_Zn^• represents one positive charge of Al that stayed in zinc lattice and act as donor. O_o is the oxygen ion in the inherent lattice. On the other hand, when ZnO was doped with Fe³⁺ ions, the generation of free carriers is as follows [55]:

${\text{Fe}}_{\text{2}}{\text{O}}_{\text{3}}\to 2{\text{Fe}}_{\text{Zn}}^{\text{•}}+3{\text{O}}_o^x+2e^{\prime }$ E8

where Fe_Zn^• represents one positive charge of Fe that stayed in zinc lattice and act as donor. O_o is the oxygen ion in the inherent lattice while “x” represents the neutrality of O_o. Substitutions of two Fe atoms in the ZnO structure have induced two free electrons. This theory supports the enhancement of conductivity from Al- and Fe-doped samples compared to undoped ZnO nanorod arrays.

Humidity sensor responses of the prepared sensors in ambient with various RH (relative humidity) levels are shown in Figure 7. The measurements were conducted with 5 V DC-biased source at room temperature. During the adsorption process (40–90% RH), current signal increased steadily with increasing RH. On the other hand, during the desorption process (90–40% RH), current signal rapidly dropped until the signal recovers back to its initial current value. Response and recovery times are among the most imperative elements for evaluating the performance of humidity sensors. It is noted that the time taken by a sensor to achieve 90% of the total current change is defined as the response time in the case of adsorption or the recovery time in the case of desorption. The response/recovery times of the undoped, Al-doped, and Fe-doped ZnO nanorod arrays were measured to be 252/360, 270/90, and 243/108 s, respectively. Response and recovery behavior of sensor is dependent on large surface-to-volume ratio, where it helps to increase the adsorption of water molecules on the sensing element surface. Besides, with the availability of 1-D nanostructures (nanorod), it provides a large length-to-diameter ratio which can accelerate water molecules transfer to and from the interaction region as well as enhancing electron transfer along them [59].

Figure 7.

Humidity sensor response of (a) undoped, (b) Al- doped, and (c) Fe-doped ZnO nanorod array-based humidity sensors.

Another important element of the humidity sensor is the sensitivity of the sensor. The sensitivity of undoped and doped ZnO nanorod array-based humidity sensors was estimated by using resistance data obtained from the response curve. Sensitivity was calculated by using the following relation [60, 61]:

$S=\frac{R_a}{R_{\text{rh}}}$ E9

where S is sensitivity, R_a is the resistance of the sensor under exposure to the initial humidity level, and R_rh is the resistance of the sensor at the maximum humidity level. The values of resistance were obtained using Ohm’s law on the basis of a fixed bias voltage of 5 V, shown as follows:

$V=IR$ E10

where V is the bias voltage, I is the measured current, and R is the resistance. The values of R_a/R_rh for undoped, Al-doped, and Fe-doped ZnO nanorod array-based humidity sensors were calculated to be 5.56 × 10⁹/4.17 × 10⁹, 2.66 × 10⁷/8.33 × 10⁶, and 2.08 × 10⁸ Ω/1.19 × 10⁸ Ω, respectively. From R_a and R_rh values, the sensitivities of undoped, Al-doped, and Fe-doped ZnO nanorod array-based humidity sensors were calculated to be 1.33, 3.19, and 1.75, respectively. All doped samples show an improved performance in humidity sensing compared to the undoped sample. Zhu et al. also noticed the improvement of humidity sensing capabilities when they fabricated the piezoelectric-based ZnO nanowires humidity sensor [62]. In other report, Hendi et al. reported the response/recovery time of the ZnO-based QCM humidity sensor was improved when they doped ZnO with Sn [42]: this was attributed to easy diffusion of water molecules between ZnO nanopowders.

Zhu et al. reported that the doping process can increase the concentration of oxygen vacancies when the doping elements substituted the ZnO lattice which improved the performance of humidity sensor [62]. In addition, the substitution of Al³⁺ and Fe³⁺ ions has increased the charge density and offering more surface reaction with water molecules. This statement is supported by increase in conductivity and E_g values as discussed earlier. Furthermore, the superior performance of Al-doped ZnO nanorod arrays is likely related to the higher porosity of its surface as observed from FESEM image.

6. Concluding remarks

In this chapter, advantages of doping of zinc oxide (ZnO) nanostructures have been reviewed along with changes in their properties upon doping, particularly in relation to humidity sensing applications. Compared to Fe-doping, Al-doping shows more useful changes in properties for ZnO nanorod arrays for sensor applications. From the FESEM images, the Al-doped ZnO nanorods showed dense arrays with an average diameter of 65 nm, and higher porosity of the surface as compared to the Fe-doped sample which has an average diameter of 90 nm. No significant changes to the optical properties of doped samples were observed while the I-V characteristic of those doped samples possess a significant increment in conductivity compared to undoped ZnO nanorod arrays. Regarding the humidity-sensing performance of the samples, Al-doped ZnO nanorod arrays showed superior sensitivity, more than two times higher than that of the undoped ZnO nanorod array sample. These results show that Al-doped ZnO nanorod arrays has a promising future in humidity sensor applications.

Acknowledgments

This work was supported by the Fundamental Research Grant Scheme 600-RMI/FRGS 5/3 (57/2015) from the Ministry of Education Malaysia. The authors also would like to thank the Faculty of Electrical Engineering, NANO-ElecTronic Centre (NET), NANO-SciTech Centre (NST), Research Management Centre (RMC) of UiTM and the Ministry of Higher Education of Malaysia for their funding, laboratory equipment, and support of this research.