International Journal of PhotoenergyVolume 2012 (2012), Article ID 638017, 9 pagesdoi:10.1155/2012/638017

Research Article

Anodization Parameters Influencing the Growth of Titania Nanotubes and Their Photoelectrochemical Response

Ying-Chin Lim,¹ Zulkarnain Zainal,1,2 Wee-Tee Tan,³ and Mohd Zobir Hussein1,2

¹Centre of Excellence for Catalysis Science and Technology and Department of Chemistry, Faculty of Science, Universiti Putra Malaysia, Selangor Darul Ehsan, 43400 Serdang, Malaysia²Advanced Materials and Nanotechnology Laboratory, Institute of Advanced Technology (ITMA), Universiti Putra Malaysia, Selangor Darul Ehsan, 43400 Serdang, Malaysia³Department of Chemistry, Faculty of Science, Universiti Putra Malaysia, Selangor Darul Ehsan, 43400 Serdang, Malaysia

Received 14 September 2011; Revised 19 November 2011; Accepted 19 November 2011

Academic Editor: Jiaguo Yu

Copyright © 2012 Ying-Chin Lim 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.

Abstract.

TiO₂ nanotubes (TNTs) were fabricated by electrochemical oxidation of Ti foil in a standard two-electrode cell-containing NH₄F. The effects of bath temperature, voltage ramp prior to constant voltage held during anodization and present of complexing agent on the crystalline phase, nanotube growth, and dimensional change of TNT were investigated using XRD and FESEM. The results show that tube length decreases with bath temperature attributed to faster chemical dissolution rate at high temperature. However, nanotubes growth rate was enhanced by ~260% with the addition of EDTA as the complexing agent. Meanwhile, the nanotubes diameter was found to be proportionally dependent on bath temperature but independent of the voltage ramp and addition of EDTA. Photoelectrochemical response under illumination was enhanced by using the calcined TNT and is strongly affected by its dimensional changes. Thus, desired properties of TNT can be obtained by tuning the electrochemical condition for a wide-range application.

1. Introduction

Over the past decades, titania has gained much attention compared to other oxide semiconductor due to its remarkable properties including strong oxidizing power, nontoxicity, chemical and biological inertness, and long-term photostability. Thus, it has found enormous application in photocatalysis [1–9], photoelectrochemical water splitting [10, 11], self-cleaning application [12], sensing [13, 14], and photovoltaic cells [15, 16]. In addition, high level biocompatibility nature of titania facilitates its application in biomedical field where TiO₂ layers on Ti or Ti alloys are in direct contact with biological tissue in dental implants and orthopedic applications [17, 18]. Compared with conventional TiO₂ nanoparticles, TiO₂ nanotubes (TNTs) offer some peculiar advantages such as high specific surface area resulting from the hollow channel structure, high mechanical stability, and unique nanoarchitecture with fewer interfacial grain boundaries, which promote charge transport and enhanced electron-hole separation [16].

Thus, considerable studies have been focused on fabricating TNT including sol-gel [19], hydrothermal processes [20, 21], template-assisted synthesis [22], seeded growth [23], and electrochemical anodization [24]. Among the synthetic methodology, electrochemical anodization of Ti in electrolytes containing fluoride provides a relatively simple and effective way of synthesizing nanotubular or porous structures. The synthesized nanotubes are highly ordered, well-defined with high aspect ratios, and are vertically oriented to the substrate. Most importantly, the dimensions of nanotubes could be controlled precisely and modified easily by choosing the suitable electrochemical conditions. Zwilling et al. [25] in 1999 were the first to report on successful anodization of Ti and its alloy (Ti-6Al-4V) which was carried out in chromic acid with and without the addition of hydrofluoric acid. In 2001, Grimes and coworkers [26] have successfully synthesized well-aligned and highly ordered TNT through potentiostatic anodization of Ti in aqueous electrolyte containing hydrofluoric acid. Following this work, TNT with various diameters (22–600 nm), tube lengths (0.2–1000 μm), and wall thicknesses (7–34 nm) has been obtained by controlling the electrochemical conditions. Nanoarchitecturing processes of this material and its unique properties could be obtained from a variety of reports in the literature [27–33], thus making it of considerable interest in scientific community and practical importance.

To date, the mechanistic model for nanotubes formation is believed to be the formation of pits by F⁻ which later develops into pores and transform into cylindrical nanotubular structures. Also, the nanotubes growth inward the Ti occurs at the bottom of nanotubes (tube tip) followed by oxidation at that region. Both the oxidation and dissolution rate of the tube tip are affected by several anodization conditions including bath temperature, electric field across the oxide layer, and the amount of F⁻ present. However, few studies have been carried out to study the effect of this important anodization conditions (e.g., bath temperature) on the morphology, nanotube growth, and photoelectrochemical properties of TNT [34, 35].

In this work, we accomplished the systematic study of the anodization conditions by expanding our investigation on the effect of bath temperature, voltage sweeping rate and addition of complexing agent on the formation and growth of TNT using previously optimized conditions [36]. Even though Banerjee et al. [37] has investigated the use of complexing agent on the growth of TNT, however, organic electrolyte with pH ≈ 6.4 was being used in their work. To the best of our knowledge, this is the first report on the effect of complexing agent in aqueous electrolyte on the dimensional change of the TNT. As the photo-induced processes are strongly dependent on the morphology, microstructures, and anodization conditions, study on the photoelectrochemical properties of TNT synthesized under different experimental conditions was investigated and discussed.

2. Experimental

2.1. Preparation of TiO₂ Nanotubes

Sheets of Ti foil (0.127 mm, 99.7%, Sigma Aldrich) were first cut into small rectangular size of 10 mm × 25 mm. Prior to anodization, they were degreased by sonicating in acetone, isopropanol, and deionized (DI) water, followed by chemically etched in 6 M HNO₃ for 10 minutes. Then, they were rinsed with excess DI water and dried in air. Electrochemical anodization of Ti was carried out in a homemade designed two-electrode cell with clean Ti foil as the working electrode and a high density graphite electrode as the counter electrode. All anodization experiments were conducted at room temperature (~27°C except when studying the effect of bath temperature) in 0.15 M NH₄F adjusted to pH 4 using H₂SO₄. Anodization was carried out by applying a constant voltage with no ramp (except when studying the effect of voltage ramp) using a DC power supply (Consort Mini, Cleaver Scientific Ltd). To investigate the effect of EDTA in the formation of TNT, 0.2 M (Na₂[H₂EDTA]) and NH₄F were mixed together at pH 4.5. The resultant TNT is hereinafter designated as TNT/EDTA. To facilitate comparison, another TNT sample was also synthesized without the addition of EDTA under similar experimental condition (pH 4.5). From our previous work [34], it is known that anodization of less than 10 V resulted in ring-like structure while highly-ordered and well-defined nanotubes were obtained at a voltage of 10 V and above. Employing higher voltage yielded a nanoporous at 30 V and nodule-like structure at 40 V. Hence, in this study, applied voltage was limited to 20 V to synthesize all the TNT films. The anodized samples were immediately rinsed with deionized water and subsequently dried in air. Calcination of films was carried out in a Thermolyne 21100 furnace at 500°C in open air atmosphere with a heating rate of 2°C/min for 2 h.

2.2. Characterization of As-Anodized and Calcined TiO₂ Nanotubes

The crystallinity of the as-anodized and calcined TNT films was determined by X-ray diffraction (XRD@Shimadzu D6000) using a diffractometer with Cu Kα radiation (λ = 1.5406 Å). The surface morphology of the films was acquired by a field-emission scanning electron microscope, FESEM (Zeiss SUPRA 40 VP, Germany) operating at electron beam voltage of 5 kV. Quantitative measurements of the geometrical features of TNT were done using image analysis software; Image J. About 100 measurements of tube diameter and wall thickness were taken per sample from three different locations to ensure the measurements were representative. In order to obtain the thickness of the nanotube layer, direct cross-sectional micrographs were taken from mechanically bent samples. At least five measurements of the cross section were taken from different areas on each sample to ensure the measurements reflected the actual tube length. Photoelectrochemical current response measurements were performed in a conventional three-electrode cell equipped with a flat quartz window. It consisted of a synthesized TNT working electrode, a platinum wire counter electrode, and an Ag/AgCl reference electrode. The photocurrent was measured with a scanning potentiostat (μ-III AUTOLAB) under chopped irradiation from 120 V 300 W halogen lamp during a potential sweep from +2.0 to −0.2 V with a sweep rate of 20 mV/s. The TNT films were irradiated from the front side through the quartz window in a 10 ppm methyl orange solution with 0.1 M KCl as the supporting electrolyte.

3. Results and Discussion

3.1. Effect of Bath Temperature

Figure 1 depicts the XRD patterns of as-anodized (at 35°C) and calcined TNT. It is obvious that TNT synthesized at 35°C (Figure 1(a)) exhibits amorphous structure as only diffraction peaks of Ti substrate (JCPDS no. 44-1294) are visible, which is similar to TNT fabricated at room temperature (~27°C) [36]. Although Xiao et al. observed formation of crystalline TNT in dimethyl sulfoxide at electrolyte temperature of 50–60°C [38], however, bath temperature higher than 35°C is not being used in our study as this lead to the formation of different surface morphology other than nanotubes as will be discussed later. Nevertheless, TNT crystallizes to form a mixture of anatase (101) at 25.4° (JCPDS no. 21-1272) and rutile (110) (JCPDS no. 21-1276) phase at 27.6° after calcination at 500°C as shown in Figure 1(b).

Figure 1: XRD patterns of (a) as-anodized TNT synthesized at 35°C and (b) calcined TNT. A, R, and Ti represent anatase, rutile, and titanium, respectively.

TNT was synthesized at 20 V in five different electrolyte bath temperatures: 10, 18, 27, 35, and 40°C. Figure 2 shows the FESEM micrographs of the top morphology of TNT fabricated in different bath temperatures. It can be clearly seen that TNT fabricated at low bath temperature was covered with lots of surface debris whereas clean TNT could be obtained when much higher anodization temperature was used (18°C and above) as shown in Figures 2(a)–2(c). In addition, tube length changes by a factor of two, corresponding to a decrease in length with increasing anodization temperature from 430 ± 16 nm at 10°C to 240 ± 13 nm at 35°C. For tube wall thickness, only slight decrease from 21 ± 3 nm to 15 ± 3 nm could be observed.

(a)

(b)

(c)

(d)

Figure 2: FESEM images of TNT synthesized at (a) 10°C, (b) 18°C, (c) 35°C, and (d) 40°C for 1 h.

For electrochemical oxidation of Ti in fluorinated electrolyte, it is well known that there are three processes, namely, field-assisted oxidation of Ti, field-assisted dissolution of Ti metal ions, and chemical etching of Ti and by fluoride ions that control the formation of TNT. As both chemical etching process and solubility of product ions are greatly affected by temperature change, with etching rates typically being exponential functions of the temperature. Therefore, at lower anodization temperature, thicker wall and longer tube obtained could be ascribed to weaker chemical dissolution at the pore bottom as well as slower oxide etching rate by fluoride ions at the tube top [39]. On the contrary, chemical dissolution by F⁻ and dissolution of oxide layer occurs at a faster rate at higher temperature. Chemical dissolution at the tube bottom will reduce the thickness of the oxide layer, and hence field-assisted dissolution will reoccur at the tube bottom. By this process, pores will penetrate the Ti substrate resulting in longer nanotube. However, shorter tube observed at high temperature in this study might be due to that chemical dissolution rate at the tube top occurs faster than that at the tube bottom. Nevertheless, it is worth mentioning that tube diameter increases with increasing anodization temperature being 58 ± 7 nm at 10°C and 81 ± 11 nm at 35°C. This observation, however, is in contrast with the finding reported by Mor et al. [39] who found no discernible change in tube diameter fabricated at different electrolyte temperatures. As reported elsewhere, change in tube diameter is generally influenced by applied voltage with larger tube diameter associated with the use of higher applied voltage [40, 41].

Larger tube diameter observed at high anodization temperature may be ascribed to increase in horizontal dissolution as the earlier formed parts of the tube wall (tube mouth) at the top are subjected to longer exposure in fluoride etching environment and thus decelerating dissolution in vertical direction [42]. As a result, tube growth at the tube bottom will be relatively slower. In contrast, the tube mouth will experience relatively faster dissolution leading to larger tube diameter.

Nanotubular structure completely disappeared (Figure 2(d)) when anodization of Ti is carried out at 40°C, suggesting a temperature limit above which nanotubular structure will diminish. It is known that soon after oxide layer is formed, dissolution occurs from many directions and, with increasing anodization temperature, velocity of F⁻ drift also increases. This led to faster chemical dissolution of oxide layer at multiple directions before formation of nanotubular structure. Moreover, it is believed that magnetic agitation during anodization enhanced the severity of chemical dissolution which in return results in the formation of nodule-like structure observed at 40°C.

3.2. Effect of Voltage Ramp prior to Constant Potential

It was also noticed that the length of TNT could be controlled by voltage ramp prior to constant voltage at 20 V during anodization. By employing a voltage ramp, a desired pH gradient could be established between the tube bottom and the tube mouth. Thus this will create a preference environment conducive for the growth of longer tube [43].

Figures 3(a) and 3(b) show the polarization curves for voltage ramp rate between 10 mV/s and 350 mV/s and current transients at 20 V once the voltage ramp has ended, respectively. It is apparent from Figure 3(a) that the current density increases at the beginning of anodization, followed by a sudden drop indicating the formation of thin barrier oxide layer.

(a)

(b)

Figure 3: (a) Polarization curves at different voltage ramps prior to constant voltage at 20 V and (b) current transients at 20 V after the voltage ramp has completed.

However, it is observed that the exact position for the current density rise strongly depends on the voltage ramp rate (see corresponding solid arrow in Figure 3(a)), consistent with different electric fields driving ion transport during voltage ramping [35]. Current fluctuations during voltage ramping could be observed after the initial sudden drop is ascribed to the field-assisted oxidation which increased the resistance of the oxide layer and field-assisted dissolution promoted by F⁻ (pore formation).

Once the voltage ramp was terminated, the current becomes relatively constant as shown in Figure 3(b), indicating an equilibrium between pore growth rate at the bottom of the pores and chemical etching rate of the oxide film at the oxide/electrolyte interface is achieved leading to tube formation [44]. TNT produced without applying voltage ramp prior to constant voltage has a length of about 390 nm which is similar to that synthesized using voltage ramp of 350 mV/s as shown in Table 1. No significant structural different was observed for TNT formed with a difference voltage ramp.

Table 1: Dimensional data of TNT produced at different voltage ramps prior to constant voltage of 20 V.

Voltage ramp (mV/s)
Tube diameter (nm)
Wall thickness (nm)
Tube length (nm)

10
67 ± 9
15 ± 3
444 ± 11

50
70 ± 8
17 ± 3
607 ± 18

350
70 ± 6
16 ± 3
388 ± 9

No ramp
75 ± 9
17 ± 4
393 ± 17

Nevertheless, it is noted that lowering the ramp to 50 mV/s did increase the tube length to about 600 nm, suggesting that pore formation occurs while the oxide layer is relatively thin. Further decreasing the ramp to 10 mV/s does not increase in the layer thickness. Therefore, employing 50 mV/s prior constant voltage could be regarded as the optimized voltage ramp as thickest oxide layers are obtained. It is also observed that the tube diameter is independent of voltage ramp, which is mainly affected by anodization voltage [34].

3.3. Effect of Addition of Complexing Agent

Figure 4 shows the XRD pattern of TNT and TNT/EDTA anodized at 20 V for 1 h in pH 4.5 electrolyte. Even though no significant difference in crystal phase was observed for both samples, however, relative intensity of anatase peak at 25.4° (101) increases for TNT/EDTA sample. In addition, TNT/EDTA sample also possessed additional anatase peaks at 38.1° (004), 48.1° (200), 54.0° (105), and 55.1° (211), respectively. Therefore, it is reasonable to infer that the tube length (thickness of oxide layer) of the TNT/EDTA sample had increased compared to TNT sample.

Figure 4: XRD patterns of (a) TNT and (b) TNT/EDTA calcined at 500°C. A and Ti represent anatase and titanium, respectively.

Figures 5(a) and 5(b) show the representative FESEM images of TNT and TNT/EDTA samples and it is obvious that no morphology changes for both samples. From the inset in Figure 5, highly ordered nanotubes with open mouth were formed, and the average inner diameter was measured to be 63 ± 8 nm and the outer diameter was of 92 ± 11 nm, with a wall thickness of 15 ± 4 nm. However, the cross-sectional view of TNT/EDTA (Figure 5(b)) clearly reveals that addition of EDTA has played a very vital role in increasing the tube length by 2.6 times fromto 770 ± 58 nm within 1 h of anodization with a growth rate of approximately 13 nm/min.

(a)

(b)

Figure 5: FESEM cross-sectional view images of (a) TNT and (b) TNT/EDTA; the insets show the top view images of the corresponding samples.

As shown in Figure 6, an initial current drop during anodization for both TNT and TNT/EDTA samples was observed due to the formation of an oxide layer. However, two different current behaviors could be observed depending on the presence of complexing agent. In the absence of EDTA, a gradual increase in current density is observed ascribed to the thinning of the oxide layer (promoted by F⁻) until it reaches a steady state. At this stage, nanotube formation takes place and no thickness change exists in the barrier oxide layer. With the presence of EDTA, current density decreases smoothly after the initial current decay without a local minimum.

Figure 6: Current density transient recorded during anodization with and without the presence of complexing agent. Inset is the magnifying view of the initial anodization stage.

EDTA is widely recognized as an efficient chelating agent. In aqueous acidic electrolyte, it is believed that Ti metal oxidizes to form a thin oxide layer on the Ti metal at the solid-liquid interface under applied voltage according to. Even though TiO₂ is thermodynamically stable in both acidic and alkaline medium, however, with the presence of F⁻ and [H₂EDTA]²⁻, substantial chemical dissolution occurs according to the following [37, 44, 45]: Therefore, oxide layer becomes thinner with time at a faster rate.

As mentioned earlier, there are three processes control the formation of TNT, namely, field-assisted oxidation of Ti, field-assisted dissolution of Ti metal ions, and chemical dissolution of TiO₂. As thickness reduces, field-assisted dissolution will reoccur and pore will penetrate inside Ti and tubes become longer [40]. Therefore, substantial dissolution in the presence of EDTA could enhance the growth rate of nanotubes as both the field-assisted and chemical etching occur at a faster rate.

However, it was observed that nanotube length increases with elevating anodization duration from 30 to 60 min after which it drops to about 690 ± 36 nm after 120 min of anodization. It was also found that for TNT/EDTA sample, tube diameter remained constant with increasing anodization time, indicating that anodization duration mainly influences the depth of the nanotubes. The result is in good agreement with the literature data [46].

3.4. Photoelectrochemical Response of TNT

In order to evaluate the effect of different dimensions and crystallization of TNT on its photoelectrochemical response, the as-anodized and calcined TNTs synthesized at different electrolyte temperatures, voltage ramps and presence of EDTA were used as photoanode in the photoelectrochemical cell. The photocurrent was recorded by intermittently irradiating the electrodes from halogen lamp using linear sweep photovoltammetry. Figure 7 illustrates the corresponding experimental results of as-anodized and calcined TNTs prepared at various bath temperatures and voltage ramps.

(a)

(b)

Figure 7: Comparison of photocurrent density at 1.0 V (versus Ag/AgCl) of as-anodized and calcined TNTs prepared in pH 4 electrolytes (a) at different electrolyte temperatures and (b) using different voltage ramps prior to constant voltage of 20 V. All the photocurrent measurements were obtained using 10 ppm methyl orange solution from 300 W halogen lamp at scan rate of 20 mV/s.

Apparently, all the as-anodized TNTs show a negligible photocurrent density (as low as 2 μA/cm²) and substantial enhancement of photoresponse after calcination at 500°C. This result is expected as the as-anodized TNT exhibited amorphous structure as revealed by the XRD study (Figures 1(a) and 4(a)). Usually, amorphous TNT contains more defect sites than the crystallized one, which causes the recombination of photogenerated charge carriers. Therefore, photogenerated electrons have difficulty to conduct charge transfer on amorphous TNT under external bias condition to generate photocurrent [7]. This kind of TNT photoanode will be expected to exhibit very low photocatalytic or photoelectrocatalytic reactivity. On the contrary, significant increases in photocurrent for calcined samples is likely attributed to the higher photogenerated electron-hole pairs caused by the higher amount of anatase and rutile content. This result also indicates the necessity to form crystalline phase for the application of this material as photoanode.

For calcined TNT prepared at various bath temperatures, photoresponse increases with decreasing bath temperature except for TNT fabricated at 10°C. Higher photocurrent means that photogenerated electrons have been transferred from TNT photoanode to counter electrode more effectively via external circuit under illumination. Interestingly, it is found that even though TNT length produced at room temperature, about 27°C (tube length ~290 nm), is relatively shorter, the photocurrent response is yet comparable to that synthesized at 10°C (tube length ~430 nm). Two reasons may account for such observation. Firstly, as shown in Figure 2(a), debris covering the surface of nanotubes could be observed for TNT synthesized at 10°C. This unwanted debris will reduce the surface area and thus limit the light absorption ability of the sample. Therefore, for TNT synthesized at 27°C, its photoresponse is still comparable even though it has a relatively shorter tube length. Secondly, wall thickness and tube diameters are critical in influencing the photoresponse. In this respect, TNT with thinner wall (15 nm) in our study demonstrated relatively higher photocurrent response than that of thicker wall (21 nm). It is known that when TiO₂ is irradiated, electrons and holes are generated. Unless they could be separated by either being trapped or migrateing to the semiconductor surface, otherwise they always recombine immediately once photogenerated [30, 47]. With thinner wall, photogenerated hole could reach the oxidizable species in the electrolyte easily and reducing the recombination. Moreover, surface states increase rapidly as the wall thickness reduced, and thus resulting in low surface recombination [48]. On the other hand, TNT synthesized at 18°C demonstrated the highest photocurrent density, and its value is about twice the value of that fabricated at 35°C. Apart from short tube length obtained at 35°C which in return resulted in low incident photon absorption, low photoelectrochemical current density observed may reflect the quick recombination of photogenerated charge carriers and low transfer efficiency of photogenerated electron to counter electrode via external circuit.

Generally, TNT obtained with voltage ramp prior to 2 h constant voltage has comparable or longer nanotube length than without ramp. Longest tube was obtained by applying a voltage ramp of 50 mV/s prior to constant voltage. Considering similar tube diameter and wall thickness obtained at different voltage ramps, availability of large active surface area increases linearly with increasing tube length. Thus, higher photocurrent density for TNT synthesized at 50 mV/s voltage ramping was mostly ascribed to the higher active surface area which improves the light-harvesting capability and better photon absorption of this photoanode.

Figures 8(a) and 8(b) show the variation of photocurrent density with potential for calcined TNT/EDTA and TNT prepared at pH 4.5, respectively. Both curves exhibited the typical of n-type semiconductor. Both samples exhibited almost negligible dark current, indicating inactive photoreaction of TNT under dark condition (without illumination). However, the responsive photoresponse for both samples increased drastically under light illumination implying good transfer and recombination of photo-induced charge carriers [49]. In comparison, TNT/EDTA sample exhibited higher photocurrent than TNT sample due to longer tubes obtained than the latter. Moreover, enhancement of photocurrent density could be observed over entire potential range of +1.5 to −0.2 V, implying higher photoelectrochemical reactivity of TNT/EDTA photoanode. The curve slope is also steeper for TNT/EDTA in comparison to that of TNT. Therefore, one could expect that TNT fabricated with the addition of EDTA may demonstrate high photoresponse and act as promising material as photoanode in photoelectrochemical cells.

(a)

(b)

Figure 8: Photoresponse of (a) TNT/EDTA and (b) TNT prepared at 20 V for 1 h at pH 4.5. All the photocurrent measurement were obtained using 10 ppm methyl orange with 0.1 M KCl as supporting electrolyte from 300 W halogen lamp at scan rate of 20 mV/s.

4. Conclusions

In summary, we have successfully synthesized self-organized TNT using electrochemical method in NH₄F containing electrolyte. The influence of electrolyte temperature, voltage ramp prior to constant voltage, and the addition of EDTA on the dimensions of TNT has been investigated. It was found that TNT can still be fabricated at 35°C; however, the tube length decreases whereas tube diameter increases with elevated temperature from 10 to 35°C. On the other hand, applying voltage ramp prior to constant voltage at 20 V during anodization has no influence on the tube diameter and wall thickness. Nevertheless, optimized voltage ramp at 50 mV/s resulted in thickest oxide layers. In addition, nanotube growth rate can be enhanced dramatically with the addition of EDTA. Based on the photoelectrochemical measurement, it can be concluded that structure of TNT including tube length and wall thickness is important factor influencing the photoresponse. Therefore, electrochemical parameters can be manipulated to obtain desired dimensions for various applications such as solar cells and photoelectrocatalysis.

Acknowledgment

This work was supported by an FRGS grant (no. 01-04-10-859FR) from the Ministry of Higher Education, Malaysia.

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