# Synthesis and Characterization of Hierarchical Structured TiO2 Nanotubes and Their Photocatalytic Performance on Methyl Orange

Authors: Kai Liu; Shiwei Lin; Jianjun Liao; Nengqian Pan; Min Zeng
Journal: Journal of Nanomaterials
 (2015)

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## Abstract

Hierarchical structured TiO2 nanotubes were prepared by mechanical ball milling of highly ordered TiO2 nanotube arrays grown by electrochemical anodization of titanium foil. Scanning electron microscopy, transmission electron microscopy, X-ray diffraction, specific surface area analysis, UV-visible absorption spectroscopy, photocurrent measurement, photoluminescence spectra, electrochemical impedance spectra, and photocatalytic degradation test were applied to characterize the nanocomposites. Surface area increased as the milling time extended. After 5 h ball milling, TiO2 hierarchical nanotubes exhibited a corn-like shape and exhibited enhanced photoelectrochemical activity in comparison to commercial P25. The superior photocatalytic activity is suggested to be due to the combined advantages of high surface area of nanoparticles and rapid electron transfer as well as collection of the nanotubes in the hierarchical structure. The hierarchical structured TiO2 nanotubes could be applied into flexible applications on solar cells, sensors, and other photoelectrochemical devices.


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## Body

## 1. Introduction

Compared with photocatalysis (PC), photoelectrocatalysis (PEC) is more efficient and effective. In PEC system, a photoanode is used as the working electrode, instead of directly dispersing catalyst into the wastewater. What is more, during the degradation process of the pollutants in the water, PEC could also generate hydrogen at a low bias voltage under the irradiation of solar light [1, 2].For PEC, the fundamental requirement for high solar energy conversion is that the material should have good photoelectrochemical response ability as well as high stability. Among the plentiful semiconductor catalysts, TiO2 photocatalysts are one type of attractive and promising materials due to their excellent properties such as high photocatalytic activity, stability, nontoxicity, and low price [3]. Recently, highly ordered TiO2 nanotube arrays (TNTAs) have been fabricated using a simple electrochemical anodization process and demonstrated to be with potential applications such as gas sensors [4], solar cells [5], photodegradation [6], and water splitting [7]. TiO2 nanotube arrays possess large internal surface area, direct electron transfer path, and low recombination rate [8–11], enabling us to achieve a higher photocatalytic activity and efficiency. However, due to the rigidity in the planar structure, the electrode connections for sensors or solar cells are difficult and thus pose a challenge in practical use. Therefore, the porous nanostructured TiO2 film in the form of particles is still desirable in practical applications. The present ways to prepare hierarchical structure materials are using hydrothermal method with previously mechanical mixing [12, 13] or subsequently deposition [2], which are not efficient and homogenous.In this work, we reported the fabrication of hierarchical structured anatase TiO2 nanotubes in gram-scale via a facile two-step approach: highly ordered uniform TiO2 nanotube arrays were first grown by conventional electrochemical anodization of titanium foil, followed by mechanical ball milling. The geometrical structure could be easily controlled by milling duration. Further, the photocatalytic efficiency varies with the milling time. The preferable photocatalytic activity can be attributed to the combined advantages of high surface area of nanoparticles and efficient charge carrier collection as well as fast electron transfer of the nanotubes in the hierarchical structure (as shown in Scheme 1). Besides the application in the formaldehyde detector in our previous report [14], hierarchical structured TiO2 nanotubes by this two-step method show superior photoelectrochemical properties.Scheme 1
Illustration of the large surface area and efficient charge carrier collection as well as transfer in the hierarchical structured TiO2 nanotubes.


## 2. Experimental Section

### 2.1. Fabrication of Hierarchical Structured TiO2 Nanotubes

Anodization method was used to prepare TNTAs. A large piece of raw titanium foil with thickness of 0.5 mm was cut into small pieces of 40 × 50 mm2, which were then cleaned with acetone, ethanol, and deionized water for 15 min, successively. Anodization was performed in a two-electrode configuration with Ti foil as the working electrode and stainless steel foil as the counter electrode. The interspace between the working and counter electrodes was about 3 cm. A direct current power supply was used as the voltage source to drive the anodization. The electrolyte consisted of 0.3 wt% NH4F and 2 vol% H2O in ethylene glycol. Ti foil was anodized at 60 V for 24 h at room temperature. After anodization, nanotubes were removed from Ti foil by sonication in water for 5 min. To achieve crystalline structure, nanotubes were annealed at 500°C for 3 h in air with a heating rate of 2°C/min.1.0 g as-prepared TiO2 nanotubes were weighed out and placed in a laboratory plastic ball mill, together with 0.5 mL ethanol and 10.0 g agate balls (5.0 mm in diameter) as milling media. The grinding was conducted in a shaker mill (QM-3B, Nanjing NanDa Instrument Plant) that was operated at the speed of 600 rpm for 0.5, 5, and 10 h, respectively. The dispersant was 0.2 mL glycerol which was added in the last 5 min of the milling process.


### 2.2. Electrophoretic Deposition of Hierarchical Structured TiO2 Film

The hierarchical structured TiO2 nanotubes were suspended in 2-propanol to a concentration of 1 mg/mL under 1 h sonication. Electrophoretic deposition (EPD) method was applied to fabricate TiO2 films onto fluorine-doped tin oxide (FTO) glass at 100 V/cm.


### 2.3. Sample Characterization

Field-emission scanning electron microscope (FESEM) images were obtained at 15 kV accelerating voltage (Hitachi S4800). Close examination of the hierarchical structure was further carried out by transmission electron microscopy (TEM, JEOL 2100). X-ray diffraction (XRD) was performed on a diffractometer (Bruker D8) using CuKα as the radiation source. XRD patterns were collected between 2θ of 20–80° at a scan rate of 2° per min. Specific surface area determined by Brunauer-Emmett-Teller (BET) method was investigated by specific surface area and pore size analyzer (Beckman Coulter SA3100). UV-visible absorption measurement of TiO2 films was carried on UV-visible spectroscopy (Persee TU-1901). Photoluminescence (PL) spectra were recorded via a photoluminescence spectrometer (Hitachi F-7000) with an excitation wavelength of 300 nm at room temperature.


### 2.4. Electrochemical Measurements

Photocurrents of the as-prepared TiO2 films were analyzed by electrochemical workstation (Zanher Zennium) in a three-electrode system with a platinum foil counter electrode (1 cm × 1 cm) and a saturated calomel reference electrode. The working electrode was illuminated with UV light (370 nm, 100 mW/cm2). The electrolyte was 1 M sodium sulfate aqueous solution. Electrochemical impedance spectra (EIS) were carried out by applying bias of the open-circuit voltage under 100 mW·cm−2 illumination and were recorded over a frequency range from 1 kHz to 0.01 Hz with ac amplitude voltage of 10 mV.


### 2.5. Photocatalytic and Photoelectrochemical Degradation of Methyl Orange

Photocatalytic activities and photoelectrochemical catalytic activities of TiO2 films were measured by examining the degradation behavior of methyl orange (MO). Before experiments started, MO solution with photoanode was kept in the dark for 30 min to achieve adsorption/desorption equilibrium. Then the photoelectrodes were irradiated by a 300 W high-pressure mercury lamp with strongest wavelength of 365 nm (Bilon GGZ300). The interval between the lamp and the electrode surface was 5 cm. Photoelectrochemical catalytic measurements were performed with an additional DC power supply to provide 1.0 bias voltage. The initial concentration of MO solution was 5 mg/L. The pH value of MO solution was adjusted to 2 using 1 M H2SO4. For photoelectrochemical catalysis, sodium sulfate was added to the acidic MO solution reaching the concentration of 0.2 M. The MO degradation during catalytic reaction was monitored by UV-visible spectrophotometer.


## 2.1. Fabrication of Hierarchical Structured TiO2 Nanotubes

Anodization method was used to prepare TNTAs. A large piece of raw titanium foil with thickness of 0.5 mm was cut into small pieces of 40 × 50 mm2, which were then cleaned with acetone, ethanol, and deionized water for 15 min, successively. Anodization was performed in a two-electrode configuration with Ti foil as the working electrode and stainless steel foil as the counter electrode. The interspace between the working and counter electrodes was about 3 cm. A direct current power supply was used as the voltage source to drive the anodization. The electrolyte consisted of 0.3 wt% NH4F and 2 vol% H2O in ethylene glycol. Ti foil was anodized at 60 V for 24 h at room temperature. After anodization, nanotubes were removed from Ti foil by sonication in water for 5 min. To achieve crystalline structure, nanotubes were annealed at 500°C for 3 h in air with a heating rate of 2°C/min.1.0 g as-prepared TiO2 nanotubes were weighed out and placed in a laboratory plastic ball mill, together with 0.5 mL ethanol and 10.0 g agate balls (5.0 mm in diameter) as milling media. The grinding was conducted in a shaker mill (QM-3B, Nanjing NanDa Instrument Plant) that was operated at the speed of 600 rpm for 0.5, 5, and 10 h, respectively. The dispersant was 0.2 mL glycerol which was added in the last 5 min of the milling process.


## 2.2. Electrophoretic Deposition of Hierarchical Structured TiO2 Film

The hierarchical structured TiO2 nanotubes were suspended in 2-propanol to a concentration of 1 mg/mL under 1 h sonication. Electrophoretic deposition (EPD) method was applied to fabricate TiO2 films onto fluorine-doped tin oxide (FTO) glass at 100 V/cm.


## 2.3. Sample Characterization

Field-emission scanning electron microscope (FESEM) images were obtained at 15 kV accelerating voltage (Hitachi S4800). Close examination of the hierarchical structure was further carried out by transmission electron microscopy (TEM, JEOL 2100). X-ray diffraction (XRD) was performed on a diffractometer (Bruker D8) using CuKα as the radiation source. XRD patterns were collected between 2θ of 20–80° at a scan rate of 2° per min. Specific surface area determined by Brunauer-Emmett-Teller (BET) method was investigated by specific surface area and pore size analyzer (Beckman Coulter SA3100). UV-visible absorption measurement of TiO2 films was carried on UV-visible spectroscopy (Persee TU-1901). Photoluminescence (PL) spectra were recorded via a photoluminescence spectrometer (Hitachi F-7000) with an excitation wavelength of 300 nm at room temperature.


## 2.4. Electrochemical Measurements

Photocurrents of the as-prepared TiO2 films were analyzed by electrochemical workstation (Zanher Zennium) in a three-electrode system with a platinum foil counter electrode (1 cm × 1 cm) and a saturated calomel reference electrode. The working electrode was illuminated with UV light (370 nm, 100 mW/cm2). The electrolyte was 1 M sodium sulfate aqueous solution. Electrochemical impedance spectra (EIS) were carried out by applying bias of the open-circuit voltage under 100 mW·cm−2 illumination and were recorded over a frequency range from 1 kHz to 0.01 Hz with ac amplitude voltage of 10 mV.


## 2.5. Photocatalytic and Photoelectrochemical Degradation of Methyl Orange

Photocatalytic activities and photoelectrochemical catalytic activities of TiO2 films were measured by examining the degradation behavior of methyl orange (MO). Before experiments started, MO solution with photoanode was kept in the dark for 30 min to achieve adsorption/desorption equilibrium. Then the photoelectrodes were irradiated by a 300 W high-pressure mercury lamp with strongest wavelength of 365 nm (Bilon GGZ300). The interval between the lamp and the electrode surface was 5 cm. Photoelectrochemical catalytic measurements were performed with an additional DC power supply to provide 1.0 bias voltage. The initial concentration of MO solution was 5 mg/L. The pH value of MO solution was adjusted to 2 using 1 M H2SO4. For photoelectrochemical catalysis, sodium sulfate was added to the acidic MO solution reaching the concentration of 0.2 M. The MO degradation during catalytic reaction was monitored by UV-visible spectrophotometer.


## 3. Results and Discussion

### 3.1. Morphology of Hierarchical Structured TiO2 Nanotubes

Figures1(a)–1(d) show FESEM images of TiO2 nanotube arrays and samples under different milling time. All images were taken under the same magnification and microscope settings. Figure 1(a) indicates that nanotubes were uniformly formed and loosely connected to each other. The contact between nanotubes is weak and breakable, which allows the formation of dispersed nanotubes. Of the nanotubes, the diameter is about 110 nm and the wall-thickness is in a range from 10 to 20 nm. Figures 1(b) and 1(c) indicate that nanotube arrays were broken into discrete nanotubes and crushed into fragments during the mechanical milling process. After being milled for 0.5 h, some of the nanotubes turned into small pieces and adhered to the outer walls of other nanotubes. When the milling time was extended to 5 h, the surface morphology appeared to be uniform, and nanotubes were completely dispersed into individual ones and coated with nanoparticles homogeneously. The hierarchical structured nanotubes exhibit corn-like shape. Nanotubes were ground into nanoparticles totally after 10 h of milling, and nanoparticles heavily aggregated as shown in Figure 1(d).Figure 1
FESEM images of as-prepared TiO2 nanotube arrays (a) and hierarchical structured TiO2 fabricated after different ball milling time: (b) 0.5 h, (c) 5 h, and (d) 10 h. TEM investigation of 0.5 h (e) and 5 h (f) milled samples.
(a)
(b)
(c)
(d)
(e)
(f)TEM investigation was shown in Figures1(e) and 1(f). TEM images show the close examination of hierarchical structured TiO2 nanotubes. After 20 min of ultrasonic treatment to prepare the TEM sample, nanoparticles still adhere to nanotubes uniformly, indicating that the bonding force between nanoparticles and nanotubes is strong. The close contact provides a direct way for nanotubes to collect charge carriers from nanoparticles.


### 3.2. Crystalline Phases of Hierarchical Structured TiO2 Nanotubes and P25

Figure2 shows XRD patterns of the hierarchical TiO2 nanotubes and P25. It was found that the nanotubes prepared by anodization without annealing were amorphous (black line). The annealing process performed at 500°C in atmosphere could generate a uniform structure of anatase phase (red line). Furthermore, XRD patterns gave no obvious indication of rutile phase. That is to say, no phase change occurred in the annealed samples during the ball milling process [15, 16]. Commercial P25 has both anatase and rutile phase. And the mass fraction of rutile (X
R) and anatase (X
A) of P25 was determined using the following equation [17]:(1)
X
R
=
1
1
+
1.26
I
A
/
I
R
×
100
%
,where I
A and I
R are the intensities of anatase (101) and rutile (110) peaks, respectively. The content of anatase and rutile in P25 is 86.25% and 13.75%, respectively.Figure 2
X-ray diffraction patterns of different TiO2 samples.


### 3.3. Specific Surface Areas of Hierarchical TiO2 Nanotubes

Specific surface areas data are shown in Figure3. As milling time prolonged, specific surface area increased. Specific surface areas of detached nanotube arrays are 27.87 m2/g and become 32.47 m2/g, 42.14 m2/g, and 42.70 m2/g after 0.5 h, 5 h, and 10 h of milling, respectively. After 0.5 h, 5 h, and 10 h of milling, the values of specific surface area increased by 16.5%, 51.2%, and 53.2% compared to pristine nanotubes, which is due to the rising proportion of nanoparticles.Figure 3
Specific surface areas of TiO2 nanotubes after different milling time (with error bars).


### 3.4. UV-Visible Absorption Spectra of TiO2 Films

Light absorption of TiO2 films was measured by UV-visible spectroscopy as shown in Figure 4. P25 (black line) and manually ground TiO2 nanotubes (red line) had higher absorption than ball milled TNTAs. The manually ground sample mostly consisted of nanotubes because of the relatively mild comminution. Nanotubes could increase light scattering; thus an enhanced light absorption was observed [12]. Commercial P25 contains rutile phase, which could absorb more light than anatase for its narrower band gap of 3.0 eV [18]. The shapes of curves for mechanical milled TiO2 showed no difference, because the phase composition was totally anatase after being annealed at 500°C.Figure 4
UV-visible absorption spectra of different TiO2 films.


### 3.5. Photocatalytic Activities of TiO2 Films

Photocatalytic degradation activities of methyl orange by hierarchical TiO2 and P25 films are shown in Figure 5. The results of degradation are reported as ratio of (C
/
C
0) versus illumination time (t). The initial concentration of MO solution was indicated by the initial absorbance and denoted by C
0, and the concentration of MO during reaction was denoted by C. For the selected milling time, a gradual increase in photocatalytic activity is observed with increasing ball milling time. The photocatalytic activity reached a maximum after 10 h of milling. Because of the larger surface area and high surface energy introduced by ball milling, 10 h milled TiO2 could absorb more methyl orange. Besides, residual stress and lattice distortion may result in a good separation of electrons and holes to reduce the recombination rate [15, 16, 19, 20]. As a result, a larger amount of electrons and holes were available for the photocatalytic reaction. Therefore, a faster methyl orange degradation rate of 10 h milled film was observed. P25 shows a relatively faster degradation rate than the other samples, which may be due to the higher light absorbency.Figure 5
Photocatalytic degradation of methyl orange by different TiO2 films.


### 3.6. Photocurrent of TiO2 Films

Photoelectrochemical properties of the photoanodes were characterized by linear sweep voltammetry. There were no obvious photocurrent responses for each photoanode in the dark, when the applied potential was linearly raised from −0.8 to 1 V (Figure6). However, under UV illumination, photocurrents were distinctly detected for all the thin-film electrodes, showing a positive correlation to the applied potential which could reduce the recombination of photogenerated charge carriers. The relatively small surface area of disordered TiO2 nanotubes limited the contact with electrolyte leading to the fact that the film obtained by manual grinding exhibited extremely poor performance in this measurement. However, the linear-like curve showed good charge transferring and collecting abilities of nanotubes. The 5 h milled film outperformed the other films in the photocurrent spectroscopy under UV irradiation in the whole applied potential range. The larger photocurrent densities of the hierarchical structured TiO2 films are due to the coexistence of nanoparticles and nanotubes. Nanoparticles could increase surface area and nanotubes could act as light harvester and good charge carrier transporter and collector [12]. However, when milling time extended to 10 h, without nanotubes establishing an efficient charge carrier transfer pathway among the particles, the long zigzag transfer path introduces more recombination which leads to a relatively low photocurrent density. The varied open circuit potential may be due to the different morphology of the samples [21]. Interestingly, although P25 and the manually ground sample could absorb more light (even P25 has a large specific surface area of 57.4 m2/g [22]), the photo currents (black and green lines) are much smaller than those of the hierarchical structured nanotubes (blue and red lines), which indicates that the nanotubes embedded in nanoparticles could collect more charge carriers and provide a direct pathway to FTO substrate.Figure 6
Photocurrent density versus applied potential curves of the films under UV illumination or in dark.


### 3.7. Photoelectrochemical Catalytic Activities of the Films

As shown in Figure7, photoelectrochemical catalytic activity of 5 h milled TiO2 film is superior to those of the other films. The enhanced activity derived from the special hierarchical structure includes three aspects. Firstly, the fragments adhering to nanotubes could enlarge the surface area. Consequently, the films with hierarchical structure could provide more active sites for photocatalytic reaction [23]. Secondly, nanotubes could enhance light-harvesting and charge-separating abilities of films. Due to the existence of nanotubes, more light is scattered and multiply absorbed, which leads to the improvement of light-harvesting ability of the films and good absorption of UV light [24]. Thus, hierarchical structured TiO2 nanotubes could harvest more light and generate more free charge carriers to induce photocatalysis under UV irradiation. Lastly, nanotubes could act as charge collectors, which could gather electrons from nanoparticles and provide the carriers with efficient paths [12]. The additional DC power supply drives the electrons transferring more easily, which means that more electrons are available for the photocatalytic reaction. Due to the high surface energy introduced by ball milling process, hierarchical TiO2 nanotubes could absorb more reaction substrate, which results in a faster degradation in the initial tens of minutes. The degradation rate of P25 went faster in the last several minutes because of the influence of the anatase-rutile mixed phase. Due to the higher light scattering ability, manually ground sample showed a slightly faster degradation rate, but it was still much lower than that of 5 h milled sample.Figure 7
Photoelectrochemical catalytic activities of different TiO2 films.


### 3.8. Photoluminescence Spectra and Electrochemical Impedance Spectra of the Films

To further discuss the separation of electrons and holes in hierarchical structured TiO2 samples, photoluminescence (PL) spectra of the prepared films were investigated. As shown in Figure 8(a), a good separation of electrons and holes is observed in the pristine nanotubes. PL intensities increased with the extended milling time. This is due to the introduction of recombination centers through milling process [25]. There is a strong peak at 398 nm, which is considered to be the emission of band gap transition as the energy of light is approximately equal to the band gap energy of anatase (387.5 nm). Four small peaks at the wavelengths of 451 nm, 468 nm, 483 nm, and 493 nm mainly resulted from surface oxygen vacancies and defects of the samples [26]. However, the intensities of all the prepared samples are lower than that of P25. As P25 contains 13.75% rutile phase, a strong peak is observed at 413 nm, which is equal to the band gap energy of rutile.Figure 8
Photoluminescence spectra (a) and electrochemical impedance spectra (b) of TiO2 films.
(a)
(b)Then we also investigated electrochemical impedance spectra (EIS) of the prepared films. As shown in Figure8(b), the semicircle at low frequency becomes much smaller after 5 h of ball milling, indicating a lower resistance of the electron transfer at TiO2/electrolyte interface. As mentioned above, nanotubes in the hierarchical structure could reduce charge recombination and facilitate electron transfer due to their one-dimensional structure [27]. Because of the straight path provided by nanotubes, charge recombination rate could decrease and charge transfer rate increases. It is considered that the relatively larger size of the present nanotubes could enlarge the pore size to improve the diffusion of electrolyte, which is beneficial for electron transfer in electrolyte. Therefore, an enhanced photocatalytic activity was absorbed, as indicated in Figure 7.


## 3.1. Morphology of Hierarchical Structured TiO2 Nanotubes

Figures1(a)–1(d) show FESEM images of TiO2 nanotube arrays and samples under different milling time. All images were taken under the same magnification and microscope settings. Figure 1(a) indicates that nanotubes were uniformly formed and loosely connected to each other. The contact between nanotubes is weak and breakable, which allows the formation of dispersed nanotubes. Of the nanotubes, the diameter is about 110 nm and the wall-thickness is in a range from 10 to 20 nm. Figures 1(b) and 1(c) indicate that nanotube arrays were broken into discrete nanotubes and crushed into fragments during the mechanical milling process. After being milled for 0.5 h, some of the nanotubes turned into small pieces and adhered to the outer walls of other nanotubes. When the milling time was extended to 5 h, the surface morphology appeared to be uniform, and nanotubes were completely dispersed into individual ones and coated with nanoparticles homogeneously. The hierarchical structured nanotubes exhibit corn-like shape. Nanotubes were ground into nanoparticles totally after 10 h of milling, and nanoparticles heavily aggregated as shown in Figure 1(d).Figure 1
FESEM images of as-prepared TiO2 nanotube arrays (a) and hierarchical structured TiO2 fabricated after different ball milling time: (b) 0.5 h, (c) 5 h, and (d) 10 h. TEM investigation of 0.5 h (e) and 5 h (f) milled samples.
(a)
(b)
(c)
(d)
(e)
(f)TEM investigation was shown in Figures1(e) and 1(f). TEM images show the close examination of hierarchical structured TiO2 nanotubes. After 20 min of ultrasonic treatment to prepare the TEM sample, nanoparticles still adhere to nanotubes uniformly, indicating that the bonding force between nanoparticles and nanotubes is strong. The close contact provides a direct way for nanotubes to collect charge carriers from nanoparticles.


## 3.2. Crystalline Phases of Hierarchical Structured TiO2 Nanotubes and P25

Figure2 shows XRD patterns of the hierarchical TiO2 nanotubes and P25. It was found that the nanotubes prepared by anodization without annealing were amorphous (black line). The annealing process performed at 500°C in atmosphere could generate a uniform structure of anatase phase (red line). Furthermore, XRD patterns gave no obvious indication of rutile phase. That is to say, no phase change occurred in the annealed samples during the ball milling process [15, 16]. Commercial P25 has both anatase and rutile phase. And the mass fraction of rutile (X
R) and anatase (X
A) of P25 was determined using the following equation [17]:(1)
X
R
=
1
1
+
1.26
I
A
/
I
R
×
100
%
,where I
A and I
R are the intensities of anatase (101) and rutile (110) peaks, respectively. The content of anatase and rutile in P25 is 86.25% and 13.75%, respectively.Figure 2
X-ray diffraction patterns of different TiO2 samples.


## 3.3. Specific Surface Areas of Hierarchical TiO2 Nanotubes

Specific surface areas data are shown in Figure3. As milling time prolonged, specific surface area increased. Specific surface areas of detached nanotube arrays are 27.87 m2/g and become 32.47 m2/g, 42.14 m2/g, and 42.70 m2/g after 0.5 h, 5 h, and 10 h of milling, respectively. After 0.5 h, 5 h, and 10 h of milling, the values of specific surface area increased by 16.5%, 51.2%, and 53.2% compared to pristine nanotubes, which is due to the rising proportion of nanoparticles.Figure 3
Specific surface areas of TiO2 nanotubes after different milling time (with error bars).


## 3.4. UV-Visible Absorption Spectra of TiO2 Films

Light absorption of TiO2 films was measured by UV-visible spectroscopy as shown in Figure 4. P25 (black line) and manually ground TiO2 nanotubes (red line) had higher absorption than ball milled TNTAs. The manually ground sample mostly consisted of nanotubes because of the relatively mild comminution. Nanotubes could increase light scattering; thus an enhanced light absorption was observed [12]. Commercial P25 contains rutile phase, which could absorb more light than anatase for its narrower band gap of 3.0 eV [18]. The shapes of curves for mechanical milled TiO2 showed no difference, because the phase composition was totally anatase after being annealed at 500°C.Figure 4
UV-visible absorption spectra of different TiO2 films.


## 3.5. Photocatalytic Activities of TiO2 Films

Photocatalytic degradation activities of methyl orange by hierarchical TiO2 and P25 films are shown in Figure 5. The results of degradation are reported as ratio of (C
/
C
0) versus illumination time (t). The initial concentration of MO solution was indicated by the initial absorbance and denoted by C
0, and the concentration of MO during reaction was denoted by C. For the selected milling time, a gradual increase in photocatalytic activity is observed with increasing ball milling time. The photocatalytic activity reached a maximum after 10 h of milling. Because of the larger surface area and high surface energy introduced by ball milling, 10 h milled TiO2 could absorb more methyl orange. Besides, residual stress and lattice distortion may result in a good separation of electrons and holes to reduce the recombination rate [15, 16, 19, 20]. As a result, a larger amount of electrons and holes were available for the photocatalytic reaction. Therefore, a faster methyl orange degradation rate of 10 h milled film was observed. P25 shows a relatively faster degradation rate than the other samples, which may be due to the higher light absorbency.Figure 5
Photocatalytic degradation of methyl orange by different TiO2 films.


## 3.6. Photocurrent of TiO2 Films

Photoelectrochemical properties of the photoanodes were characterized by linear sweep voltammetry. There were no obvious photocurrent responses for each photoanode in the dark, when the applied potential was linearly raised from −0.8 to 1 V (Figure6). However, under UV illumination, photocurrents were distinctly detected for all the thin-film electrodes, showing a positive correlation to the applied potential which could reduce the recombination of photogenerated charge carriers. The relatively small surface area of disordered TiO2 nanotubes limited the contact with electrolyte leading to the fact that the film obtained by manual grinding exhibited extremely poor performance in this measurement. However, the linear-like curve showed good charge transferring and collecting abilities of nanotubes. The 5 h milled film outperformed the other films in the photocurrent spectroscopy under UV irradiation in the whole applied potential range. The larger photocurrent densities of the hierarchical structured TiO2 films are due to the coexistence of nanoparticles and nanotubes. Nanoparticles could increase surface area and nanotubes could act as light harvester and good charge carrier transporter and collector [12]. However, when milling time extended to 10 h, without nanotubes establishing an efficient charge carrier transfer pathway among the particles, the long zigzag transfer path introduces more recombination which leads to a relatively low photocurrent density. The varied open circuit potential may be due to the different morphology of the samples [21]. Interestingly, although P25 and the manually ground sample could absorb more light (even P25 has a large specific surface area of 57.4 m2/g [22]), the photo currents (black and green lines) are much smaller than those of the hierarchical structured nanotubes (blue and red lines), which indicates that the nanotubes embedded in nanoparticles could collect more charge carriers and provide a direct pathway to FTO substrate.Figure 6
Photocurrent density versus applied potential curves of the films under UV illumination or in dark.


## 3.7. Photoelectrochemical Catalytic Activities of the Films

As shown in Figure7, photoelectrochemical catalytic activity of 5 h milled TiO2 film is superior to those of the other films. The enhanced activity derived from the special hierarchical structure includes three aspects. Firstly, the fragments adhering to nanotubes could enlarge the surface area. Consequently, the films with hierarchical structure could provide more active sites for photocatalytic reaction [23]. Secondly, nanotubes could enhance light-harvesting and charge-separating abilities of films. Due to the existence of nanotubes, more light is scattered and multiply absorbed, which leads to the improvement of light-harvesting ability of the films and good absorption of UV light [24]. Thus, hierarchical structured TiO2 nanotubes could harvest more light and generate more free charge carriers to induce photocatalysis under UV irradiation. Lastly, nanotubes could act as charge collectors, which could gather electrons from nanoparticles and provide the carriers with efficient paths [12]. The additional DC power supply drives the electrons transferring more easily, which means that more electrons are available for the photocatalytic reaction. Due to the high surface energy introduced by ball milling process, hierarchical TiO2 nanotubes could absorb more reaction substrate, which results in a faster degradation in the initial tens of minutes. The degradation rate of P25 went faster in the last several minutes because of the influence of the anatase-rutile mixed phase. Due to the higher light scattering ability, manually ground sample showed a slightly faster degradation rate, but it was still much lower than that of 5 h milled sample.Figure 7
Photoelectrochemical catalytic activities of different TiO2 films.


## 3.8. Photoluminescence Spectra and Electrochemical Impedance Spectra of the Films

To further discuss the separation of electrons and holes in hierarchical structured TiO2 samples, photoluminescence (PL) spectra of the prepared films were investigated. As shown in Figure 8(a), a good separation of electrons and holes is observed in the pristine nanotubes. PL intensities increased with the extended milling time. This is due to the introduction of recombination centers through milling process [25]. There is a strong peak at 398 nm, which is considered to be the emission of band gap transition as the energy of light is approximately equal to the band gap energy of anatase (387.5 nm). Four small peaks at the wavelengths of 451 nm, 468 nm, 483 nm, and 493 nm mainly resulted from surface oxygen vacancies and defects of the samples [26]. However, the intensities of all the prepared samples are lower than that of P25. As P25 contains 13.75% rutile phase, a strong peak is observed at 413 nm, which is equal to the band gap energy of rutile.Figure 8
Photoluminescence spectra (a) and electrochemical impedance spectra (b) of TiO2 films.
(a)
(b)Then we also investigated electrochemical impedance spectra (EIS) of the prepared films. As shown in Figure8(b), the semicircle at low frequency becomes much smaller after 5 h of ball milling, indicating a lower resistance of the electron transfer at TiO2/electrolyte interface. As mentioned above, nanotubes in the hierarchical structure could reduce charge recombination and facilitate electron transfer due to their one-dimensional structure [27]. Because of the straight path provided by nanotubes, charge recombination rate could decrease and charge transfer rate increases. It is considered that the relatively larger size of the present nanotubes could enlarge the pore size to improve the diffusion of electrolyte, which is beneficial for electron transfer in electrolyte. Therefore, an enhanced photocatalytic activity was absorbed, as indicated in Figure 7.


## 4. Conclusions

Nanotube-based hierarchical structured TiO2 was facilely prepared by a two-step method: highly ordered TiO2 nanotube arrays were first fabricated through the anodization process and then followed by mechanical milling. The morphologies of 5 h milled hierarchical TiO2 nanotubes exhibit a uniform corn-like shape. Furthermore, 5 h milled TiO2 nanotubes exhibited preferable photoelectrochemical activity in comparison to P25. The superior catalytic activity is suggested to be due to the combined advantages of high surface area of nanoparticles, as well as rapid electron transfer and collection of the nanotubes in the hierarchical structure. It is believed that, through further optimization of the milling process, more uniform desirable porous nanotube with bonded nanoparticles can be achieved. The hierarchical structured TiO2 nanotubes synthesized by this two-step method indicate not only an easy way to in situ modify/dope TiO2 in the milling process but also flexible applications on solar cells and other photoelectrochemical devices.



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*Source: 201650-2015-03-19.xml*