# Study on Synthesis and Photocatalytic Activity of Porous Titania Nanotubes

Authors: Huang Liu; Yanhua Zhang; Hongtao Yang; Wei Xiao; Lanlan Sun
Journal: Advances in Materials Science and Engineering
 (2016)

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## Abstract

Using the common natural cellulose substance (filter paper) and triblock copolymer (Pluronic P123) micelles as dual templates, porous titania nanotubes with enhanced photocatalytic activity have been successfully synthesized through sol-gel methods. Firstly, P123 micelles were adsorbed onto the surfaces of cellulose nanofibers of filter paper, followed by hydrolysis and condensation of tetrabutyl titanate around these micelles to form titania layer. After calcination to remove the organic templates, hierarchical titania nanotubes with pores in the walls were obtained. The sample was characterized by X-ray diffraction pattern (XRD), scanning electron microscopy (SEM), transmission electron microscopy (TEM), nitrogen adsorption/desorption, Fourier Transform Infrared Spectroscopy (FT-IR), Ultraviolet-Visible Diffuse Reflectance Spectroscopy (UV-Vis DRS), and X-ray photoelectron spectroscopy (XPS). As compared with commercial P25 catalyst, the porous titania nanotubes prepared by this method displayed significantly enhanced photocatalytic activity for degrading methyl orange under UV irradiation. Within 10 minutes, the porous titania nanotubes are able to degrade over 70% of the original MO, while the value for the commercial Degussa P25 is only about 33%.


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## Body

## 1. Introduction

As the most promising photocatalyst, titania materials (TiO2) have been expected to play an important role in a wide range of fields including environmental pollution control, photocatalyst, and high effect solar cell due to their excellent physicochemical properties such as relatively high photocatalytic activity, thermal and chemical stability, nonphoto corrosive, being nontoxic, being capable of photooxidative destruction of most organic pollutants, and low cost [1–5]. Numerous recent research has shown that the photocatalytic activity of titania materials is mainly influenced by the surface area, grain size, crystallinity, crystal structure, band gap, and so forth [6–9]. Normally, the anatase-type titania materials (band gap energy 3.2 eV) generally exhibit much higher photocatalytic activity than that of rutile (band gap energy 3.0 eV) [10–13]. Therefore, preparation of anatase phase of titania nanomaterials has attracted increasing attention and many methods have been developed, such as anodization of titanium foil [14, 15], the hydrothermal treatment of TiO2 nanoparticles with alkali solution [16, 17], surfactant-assisted templating methods [18, 19], hydrolysis of TiF4 under acidic conditions [20, 21], and deposition of sol-gels within templates [22].In this paper, we synthesized titania nanotubes through sol-gel method with employed natural cellulose substance (filter paper) as template. The resulting titania nanotubes truly inherit the complex network structures and hierarchical morphologies of the initial cellulose substance and exhibit obviously enhanced photocatalytic activity compared with commercial P25.


## 2. Experimental

### 2.1. Reagents

Commercial ashless quantitative filter paper (GB/T1914-93) was used throughout the work. Triblock copolymer Pluronic P123 (PEG-PPG-PEG) and titaniumn-butoxide [Ti(OnBu)4, TBT, 99%] were purchased from Aldrich. All aqueous solutions were prepared using Milli-Q water (Resistivity, 18.2 MΩ cm). All the other chemicals were guaranteed ones and used as received.


### 2.2. Preparation of Porous Titania Nanotubes

The synthetic procedure of hierarchical titania nanotubes is schematically illustrated in Scheme1. During the synthesis process, commercial ashless quantitative filter paper was used as the template of the hierarchical nanotubular structure. In a typical procedure, 0.29 g surfactant P123 was added into the mixture of 40 mL ethanol and 40 mL deionized water followed by stirring for about 30 min. Then, 150 mg precut squared filter paper fractions ofca. 5 mm × 5 mm were immersed in and the mixture was treated with ultrasonication for 3 h to promote formation of the surfactant micelles. After that, 20 mL 1 M HCl aqueous solution was injected in the mixture under stirring. 40 mL ethanol and 3.4 g TBT solutions were subsequently added dropwise to the mixture under vigorous stirring at room temperature. After stirring for 30 min, the mixture was treated with ultrasonication for 30 min and then the filter paper fractions were filtered off, washed with deionized water, and finally vacuum-dried at room temperature overnight. The as-prepare filter paper was firstly calcined in a tubular furnace at 120°C for 1 h, then heated up to 300°C, and kept for 1 h followed by 450°C for 4 h. The whole process was in air atmosphere with a ramping rate of 3°C/min.Scheme 1
Schematic illustration of the preparation process for hierarchical titania nanotubes templated by filter paper.


### 2.3. Characterizations

The micromorphologies of obtained hierarchical titania nanotubes sample were examined by S-4800 field emission scanning electron microscope (FE-SEM) from Hitachi, transmission electron microscopy (TEM), and high resolution transmission electron microscopy (HR-TEM, FEI Tecnai G20/JEM 2010, operated at 200 kV). To prepare the specimens for electron microscope observation, a small piece of the nanotubular titania sheet specimen was suspended in ethanol by supersonic dispersion. Then some of the suspension was dropped onto silicon wafer and sputtered with gold or platinum for SEM observation. And some are dropped onto copper mesh for TEM observation. The crystal phase of the obtained hierarchical titania nanotubes materials was determined by powder X-ray diffraction (XRD) recorded on a Dandong TD3500 Advanced diffractometer (Cu-Kα, λ
=
0.15418 nm). Nitrogen adsorption and desorption isotherms were acquired at 77 K on a TriStar II 3020 surface area and pore analyzer. The linear part of the Brunauer-Emmett-Teller (BET) equation was used for the specific surface area determination. And the pore-size distributions were obtained from the adsorption branch of the nitrogen physisorption isotherms using the BJH method. The Fourier Transform Infrared Spectroscopy (FT-IR) of the sample was recorded on a Nicolet Magna-IR 750 spectrometer at a resolution of 0.125 cm−1. Ultraviolet-visible diffuse reflectance absorption spectra (UV-Vis DRS) were employed to characterized the hierarchical TiO2 sample on a U-4100 spectrometer (Hitachi Japan) with BaSO4 powder as the reference standard. The surface composition of the product was determined by X-ray photoelectron spectrometer (XPS, ESCALAB 250XI, USA).


### 2.4. Photodegradation Experiment

A widely used dye methyl orange (C14H14N3NaO3S), which can act as a representative dye pollutant, was chosen to evaluate the photocatalytic performance of TiO2 nanotubes under UV light. Firstly, 100 mL aqueous solution of TiO2 catalyst (0.2 g) was treated with ultrasonication for 30 min to promote dispersion uniformity and 400 mL dye aqueous solution of MO (30 mg/L) was prepared for subsequent photocatalytic activity test. Then, the two prepared solutions above were mixed in a quartz tube. Before irradiation, the above mixed solution was stirred for 30 min in the dark for establishing the adsorption-desorption equilibrium. Then under ambient conditions and stirring, the mixture was exposed to the UV irradiation produced by a 500 W Hg arc lamp equipped with a band-pass light filter (365 ± 15 nm). At every 2-minute interval, about 3 mL suspension was withdrawn from the mixture for analysis on a Varian Cary-50 UV-Vis spectrophotometer. The initial concentration of dye solution before photodegradation experiment is noted as C
0 and the concentration of dye solution at each irradiated time interval is noted as C. Therefore, the percentage of residual dye can be recorded as C
/
C
0.


## 2.1. Reagents

Commercial ashless quantitative filter paper (GB/T1914-93) was used throughout the work. Triblock copolymer Pluronic P123 (PEG-PPG-PEG) and titaniumn-butoxide [Ti(OnBu)4, TBT, 99%] were purchased from Aldrich. All aqueous solutions were prepared using Milli-Q water (Resistivity, 18.2 MΩ cm). All the other chemicals were guaranteed ones and used as received.


## 2.2. Preparation of Porous Titania Nanotubes

The synthetic procedure of hierarchical titania nanotubes is schematically illustrated in Scheme1. During the synthesis process, commercial ashless quantitative filter paper was used as the template of the hierarchical nanotubular structure. In a typical procedure, 0.29 g surfactant P123 was added into the mixture of 40 mL ethanol and 40 mL deionized water followed by stirring for about 30 min. Then, 150 mg precut squared filter paper fractions ofca. 5 mm × 5 mm were immersed in and the mixture was treated with ultrasonication for 3 h to promote formation of the surfactant micelles. After that, 20 mL 1 M HCl aqueous solution was injected in the mixture under stirring. 40 mL ethanol and 3.4 g TBT solutions were subsequently added dropwise to the mixture under vigorous stirring at room temperature. After stirring for 30 min, the mixture was treated with ultrasonication for 30 min and then the filter paper fractions were filtered off, washed with deionized water, and finally vacuum-dried at room temperature overnight. The as-prepare filter paper was firstly calcined in a tubular furnace at 120°C for 1 h, then heated up to 300°C, and kept for 1 h followed by 450°C for 4 h. The whole process was in air atmosphere with a ramping rate of 3°C/min.Scheme 1
Schematic illustration of the preparation process for hierarchical titania nanotubes templated by filter paper.


## 2.3. Characterizations

The micromorphologies of obtained hierarchical titania nanotubes sample were examined by S-4800 field emission scanning electron microscope (FE-SEM) from Hitachi, transmission electron microscopy (TEM), and high resolution transmission electron microscopy (HR-TEM, FEI Tecnai G20/JEM 2010, operated at 200 kV). To prepare the specimens for electron microscope observation, a small piece of the nanotubular titania sheet specimen was suspended in ethanol by supersonic dispersion. Then some of the suspension was dropped onto silicon wafer and sputtered with gold or platinum for SEM observation. And some are dropped onto copper mesh for TEM observation. The crystal phase of the obtained hierarchical titania nanotubes materials was determined by powder X-ray diffraction (XRD) recorded on a Dandong TD3500 Advanced diffractometer (Cu-Kα, λ
=
0.15418 nm). Nitrogen adsorption and desorption isotherms were acquired at 77 K on a TriStar II 3020 surface area and pore analyzer. The linear part of the Brunauer-Emmett-Teller (BET) equation was used for the specific surface area determination. And the pore-size distributions were obtained from the adsorption branch of the nitrogen physisorption isotherms using the BJH method. The Fourier Transform Infrared Spectroscopy (FT-IR) of the sample was recorded on a Nicolet Magna-IR 750 spectrometer at a resolution of 0.125 cm−1. Ultraviolet-visible diffuse reflectance absorption spectra (UV-Vis DRS) were employed to characterized the hierarchical TiO2 sample on a U-4100 spectrometer (Hitachi Japan) with BaSO4 powder as the reference standard. The surface composition of the product was determined by X-ray photoelectron spectrometer (XPS, ESCALAB 250XI, USA).


## 2.4. Photodegradation Experiment

A widely used dye methyl orange (C14H14N3NaO3S), which can act as a representative dye pollutant, was chosen to evaluate the photocatalytic performance of TiO2 nanotubes under UV light. Firstly, 100 mL aqueous solution of TiO2 catalyst (0.2 g) was treated with ultrasonication for 30 min to promote dispersion uniformity and 400 mL dye aqueous solution of MO (30 mg/L) was prepared for subsequent photocatalytic activity test. Then, the two prepared solutions above were mixed in a quartz tube. Before irradiation, the above mixed solution was stirred for 30 min in the dark for establishing the adsorption-desorption equilibrium. Then under ambient conditions and stirring, the mixture was exposed to the UV irradiation produced by a 500 W Hg arc lamp equipped with a band-pass light filter (365 ± 15 nm). At every 2-minute interval, about 3 mL suspension was withdrawn from the mixture for analysis on a Varian Cary-50 UV-Vis spectrophotometer. The initial concentration of dye solution before photodegradation experiment is noted as C
0 and the concentration of dye solution at each irradiated time interval is noted as C. Therefore, the percentage of residual dye can be recorded as C
/
C
0.


## 3. Results and Discussion

### 3.1. Characterization of Porous Titania Nanotubes

The XRD pattern in Figure1(a) shows that the commercial P25 is a mixture of anatase phase and rutile phase, while the XRD pattern of our obtained porous titania nanotubes demonstrates that anatase is actually the only crystal phase (Figure 1(b)). The distinctive X-ray diffraction peaks around 25.6°, 38.1°, 48.2°, 54.1°, 55.3°, 62.9°, 68.9°, 70.7°, and 75.3° in Figure 1(b) correspond to the (101), (004), (200), (105), (211), (204), (116), (220), and (215) crystalline planes of anatase (Figure 1(c), I41/amd, JCPDF card number 73-1764), respectively, which indicates the high crystallinity of our product. The crystallite size can be estimated from the widening XRD peak via the Scherrer equation described as follows: (1)
d
=
k
λ
β
cos
⁡
θ
,where d is the crystallite size; k is a constant (0.89); λ is the X-ray wavelength (1.5418 Å for Cu K
α); β (radian) is the full-width at half-maximum for the (101) peak at 2θ = 25.6°; and θ is the angle of the diffraction peak (degree). The estimated average crystallite size based on the (101) peak isca. 22.6 nm.Figure 1
Characteristic XRD pattern of (a) P25; (b) the prepared hierarchical TiO2 nanotubes sample; and (c) JCPDF card number 73-1764 of anatase TiO2.The morphology of obtained TiO2 sample was observed by SEM and TEM. Figure 2(a) is the overview FE-SEM image of the sample, which shows that the titania sample really inherits the complex network structure and the hierarchical morphology of the original filter paper template, and the resulting titania is composed of many randomly intersecting titania microfibers with high aspect ratios. From the further magnified SEM image in Figure 2(b), we can observe that the tube wall of the individual titania microtube is composed of lots of fine nanotubes, which measured the tubular structure with inner diameters of 80–90 nm and tube wall thickness of 30–40 nm. Figure 2(c) is a typical TEM image of an individual titania nanotube, whose hollow interior can be clearly identified. The inset in Figure 2(c) indicates that abundant intergranular pores with size ofca. 12 nm located in the tube-wall, which came from the aggregation of small TiO2 nanoparticles. From the HR-TEM image shown in Figure 2(d), it can be observed that the average grain size of porous TiO2 nanotubes is ~20 nm, which consists with the result of XRD analysis. Besides, the HR-TEM image in Figure 2(d) also shows that the measured lattice spacing of sample is 0.35 nm, corresponding to the lattice distance of anatase (101) planes, which further confirms the anatase crystalline phase of the nanotubular titania product. Several multicrystal diffraction rings ascribed to the anatase phase can be observed clearly in the SAED pattern of sample (Figure 2(d) insert), which are particularly indexed (from small to large rings) as 101 (d
=
0.35 nm), 004 (d
=
0.237 nm), 200 (d
=
0.189 nm), and 211 (d
=
0.166 nm). These results agree well with the XRD analysis described above.Figure 2
Micromorphology observations of prepared porous TiO2 nanotubes. (a) FE-SEM image. (b) Further magnified SEM image. (c) TEM image of individual titania nanotube and magnified TEM image of tube wall (insert). (d) HR-TEM image and SAED pattern (insert).
(a)
(b)
(c)
(d)According to the IUPAC classification of porous materials, the nitrogen adsorption and desorption curve of the obtained hierarchical porous TiO2 nanotubes material in Figure 3(a) show a type II isotherm pattern with a hysteresis loop of type H3 in the IUPAC classification [23], revealing the presence of abundant intergranular pores in the tube wall. The capillary condensation step at relative pressure about 0.3 (P
/
P
0) might be attributed to the uniform mesopores in the tube walls. And the sharp step of capillary condensation at the relative pressure range of 0.5–0.95 (P
/
P
0) is caused by the existence of macropores in the samples. From the desorption branch of isotherm as shown in the inset of Figure 3(a), the pore distribution plot of the synthesized materials was determined by the BJH (Barrett-Joyner-Halenda) method. The result indicates that the synthesized titania has mesopores with an average pore diameter of ~12 nm, which is higher than the commercial P25 (Degussa) materials (ca. 6.9 nm). The BET specific surface area of the obtained titania sample was estimated about 27 m2/g and the total pore volume was about 0.11 cm3/g. Figure 3(b) is characteristic FT-IR absorbance data of our porous TiO2 nanotubes sample. In this figure, two broad absorption bands centered around 3375 and 2995 cm−1 are observed obviously. The former is associated with the hydroxyl groups of Ti-OH at weak surface active sites and the latter is attributed to water complexes that are strongly bound to the TiO2 surface. Besides, a weak sharp absorption band, which resulted from the deformation vibration for H-O-H bonds of the physisorbed water, and a mixed weak peak caused by the formation of the linear chain of Ti-O-Ti are located at about 1640 cm−1 and 400–480 cm−1, respectively. However, the absorption bands corresponding to the isolated OH group vibrations around 3665 and 3715 cm−1 are both relatively weak that they are overlapped by the broad band, which indicates a high degree of hydration on the anatase TiO2 surfaces.Figure 3
(a) N2 adsorption/desorption isotherms of the prepared TiO2 nanotubes and BJH pore-size distribution plot (insert). (b) FT-IR spectrum of the obtained porous TiO2 nanotubes.
(a)
(b)Band gaps (E
g) of the hierarchical porous TiO2 nanotubes and P25 were estimated according to the equation as follows [24]: (2)
α
=
B
h
ν
-
E
g
n
h
ν
,where α is the absorption coefficient, B is an absorption constant, h is Planck’s constant, E
g is band gap, and n equals 1/2 for direct transition and 2 for indirect transition.Figure4(a) presents the UV-Vis spectra of the TiO2 nanotubes and P25. There is a similar striking feature for the TiO2 nanotubes and P25 that the broad absorption region extends to about 400 nm. As the absorbance (A) is proportional to the absorption coefficient (α), A can substitute for α
. Plots of A
h
ν
2 versus h
ν from the spectral data in Figure 4(a) are presented in Figure 4(b). The intercept of the tangent to the linear part of the curve gives a good approximation of the band gap energies of the samples. Extrapolating the linear part of the curves for the porous TiO2 nanotubes and P25 gives their direct band gaps of 3.43 eV and 3.36 eV, respectively. These values are very close to 3.3 eV for the experimental bulk crystal [25] and the calculated value of 3.45 eV corresponds to X
1
a
→
C
1
b direct interband transition [26]. However, when the curves are plotted as A
h
ν
1
/
2 versus h
ν, good linear relationships are obtained. Consequently, the absorption features in Figure 4(c) are those of the allowed indirect band transitions. Extrapolating the linear part of the curves for our porous TiO2 nanotubes and P25 in Figure 4(c) gives their indirect transition of 2.81 eV and 2.73 eV, respectively. These values are very similar to the calculated value of 2.91 eV corresponding to X
1
a
→
G
1
b indirect interband transition [27]. The results above indicate that the optical properties of TiO2 nanotubes are better than commercial P25 material.Figure 4
(a) UV-Vis absorption spectra of the TiO2 nanotubes and P25. (b) The plots of A
h
ν
2 versus the photon energy (
h
ν
). (c) The plots of A
h
ν
1
/
2 versus the photon energy (h
ν).
(a)
(b)
(c)Using X-ray photoelectron spectroscopy (XPS), we examined the surface chemical state and element composite of our porous TiO2 nanotubes. The XPS full spectrum shown in Figure 5(a) indicates that our TiO2 sample only contains Ti, O, and C elements with the chemical binding energies of Ti 2p (459.4 eV), O 1s (530.4 eV), and C 1s (285.4 eV), respectively. We also measured the C 1s core levels to detect possible doped carbon in TiO2 lattice. Deconvolution of the C 1s peak in the XPS spectrum (Figure 5(b)) shows the presence of two types of carbon bonds, that is, C-C (284.6 eV) and Ti-O-C (288.6 eV). Doped carbon would exhibit carbon ion characteristics peaked at approximately 281.8 eV, which is different from the background peak at 284.6 eV (carbon tape with C
0). As shown in Figure 5(b), there is no carbon ion peak (281.8 eV) for TiO2 sample. The presence of the Ti-O-C structure may be derived from the carbon in residual organic surfactant and filter paper. As shown in the Ti 2p spectral region (Figure 5(c)), there are three peaks at 458.9 eV, 464.4 eV, and 472.3 eV, respectively. These peaks can be attributed to Ti 2p1/2, Ti 2p3/2, and their satellite peaks with typical characteristic Ti4+ binding energies. All Ti 2p signals are symmetric with no shoulders at the lower energy sides, which are significantly different from the spectra of TiO2 doped with carbon or other impurities. According to the high resolution X-ray photoelectron spectra of O 1s, as shown in Figure 5(d), there is a symmetric peak at 530.3 eV, indicating that the oxygen mainly exists in the form of lattice oxygen (O-Ti) in the sample.Figure 5
(a) XPS full spectrum of TiO2 sample. (b) High resolution XPS of C 1s and subpeak fitting chart. (c) High resolution XPS of Ti 2p and subpeak fitting chart. (d) High resolution XPS of O 1s and subpeak fitting chart.
(a)
(b)
(c)
(d)


### 3.2. Photocatalytic Degradation of MO

TiO2 material is the most promising photocatalyst because of its high photosensitivity and wide band gap. Here, we evaluate the photocatalytic performance of the as-prepared porous TiO2 nanotubes by monitoring the degradation of methyl orange (MO) under UV irradiation. Before UV irradiation, the mixture of MO solution and the catalyst was stirred in the dark for 30 min to ensure that MO was adsorbed to saturation on the surface of catalyst. Figure 6 shows the degradation efficiency of MO over the as-prepared TiO2 photocatalyst. As shown in Figure 6(a), the color of the solutions gradually fades with the time increasing, which implies the gradual decrease of MO concentration in mixture. Figure 6(b) shows the absorption spectra of MO solution in the presence of the porous TiO2 nanotubes under exposure to UV light for different periods of time. The result exhibits that the characteristic absorption peak of MO at 464 nm rapidly decreased with the increase of exposure time and disappeared after 20 min, which shows that MO is almost completely degraded under exposure to UV light for 20 min. This demonstrates that the porous TiO2 nanotubes prepared through the present method possess excellent photocatalytic performance for degradation of MO.Figure 6
(a) Photographs and (b) adsorption spectra of MO solutions in the presence of porous TiO2 nanotubes irradiated by UV lamp at different periods of time.
(a)
(b)Figure7 shows the degradation efficiency of MO without and with the presence of catalysts. Blank experiment in the absence of catalyst but under identical UV irradiation for 20 min shows that only 2.4% of MO was degraded (black line in Figure 7(a)). Under the same condition, the existence of commercial Degussa P25 catalyst resulted in the increase of degradation percentage of MO to 45.4% under exposure to UV light for 20 min (blue line in Figure 7(a)). However, in the case of the porous TiO2 nanotubes, it is interesting to note that 93% of the MO in the solution is degraded after 20 min of UV irradiation (red line in Figure 7(a)).Figure 7
Photodegradation kinetics of methyl orange in the presence of porous TiO2 nanotubes. (a) Plot for the degradation percentage (C
/
C
0) of MO solutions versus time intervals. (b) ln
⁡
(
C
/
C
0
) as a function of reaction time.
(a)
(b)Figure7(b) shows the kinetics of photocatalytic degradation of MO under UV irradiation fitted by the first-order kinetics model:(3)
ln
⁡
C
C
0
=
-
k
t
,where k is the pseudo-first-order rate constant (min−1). As shown in Figure 7(b), the photodegradation of MO obeys pseudo-first-order kinetics. The calculated pseudo-first-order rate of MO with porous TiO2 nanotubes (0.10141 min−1) is much larger than that of MO with P25 (0.02477 min−1), which means that the introduction of porous TiO2 nanotubes leads to much more significant enhancement of MO degradation rate under UV light irradiation than that of P25. It can be concluded that the porous TiO2 nanotubes exhibit more prominent photocatalytic activity than the commercial Degussa P25.It has been reported that the photodegradation activity of TiO2 material is mainly attributed to the factors including surface area, absorptive capacity, grain size, crystalline, and morphology. Generally, high surface area and small grain size are most important for promoting the photocatalytic performance of titania materials [28–30]. However, other factors are able to influence their photocatalytic activities to a large extent as well. Though our porous TiO2 nanotubes possess a lower surface area (27 m2/g) than commercial Degussa P25 (20 nm, 48.9 m2/g) and a weaker adsorptive capacity in the dark adsorption of photocatalytic test (Figure 7(a)), as well as the quite similar grain size (~20 nm) with that of Degussa P25, the porous TiO2 nanotubes exhibit much higher photocatalytic activity than commercial Degussa P25 as depicted in Figure 7. The possible reason for the higher photocatalytic performance of porous TiO2 nanotubes can be ascribed to the following two factors. Firstly, the crystallinity of TiO2 materials is an important factor for influencing their photocatalytic performance as well [31, 32]. As can be observed in Figure 1, the obtained porous TiO2 nanotubes exhibit fully pure anatase crystalline form and rather high crystallinity, which means less defects inside the sample and is in favor of the separation of photogenerated electron-hole pairs and the lower recombination of photogenerated hole-electron. That means that the high crystallinity of the porous TiO2 nanotubes is beneficial to their photocatalytic performance. Besides, the abundant pores in the tube wall of the samples benefit for the penetration of light waves and lead to high mobility of photogenerated charges [31, 32]. Meanwhile, the abundant pores also facilitate the mass transport and reactants can deeply enter the catalyst through these pores, which could improve their photocatalytic activity greatly. Therefore, in spite of the lower surface area and similar grain size compared with P25, the synergistic effect arising from the high crystallinity and abundant pores on the tube wall of porous TiO2 nanotubes results in the final excellent photocatalytic performance.Figure8 is the characterization of porous TiO2 nanotubes after performing the MO degradation reaction. It shows that the morphology and microstructure of the TiO2 prepared through the present method were still well maintained after the reaction (Figures 8(a) and 8(b)). Meanwhile, compared with XRD pattern of the sample before photocatalytic reaction (black line in Figure 8(c)), the crystalline of porous TiO2 nanotubes was not obviously destroyed during the reaction (red line in Figure 8(c)). The result indicates that the prepared porous TiO2 nanotubes exhibit good stability during the photocatalytic degradation for MO.Figure 8
(a) Low magnified and (b) large magnified SEM images of porous TiO2 nanotubes after photocatalytic reaction for MO. (c) XRD patterns of porous TiO2 nanotubes before and after photocatalytic degradation for MO.
(a)
(b)
(c)


## 3.1. Characterization of Porous Titania Nanotubes

The XRD pattern in Figure1(a) shows that the commercial P25 is a mixture of anatase phase and rutile phase, while the XRD pattern of our obtained porous titania nanotubes demonstrates that anatase is actually the only crystal phase (Figure 1(b)). The distinctive X-ray diffraction peaks around 25.6°, 38.1°, 48.2°, 54.1°, 55.3°, 62.9°, 68.9°, 70.7°, and 75.3° in Figure 1(b) correspond to the (101), (004), (200), (105), (211), (204), (116), (220), and (215) crystalline planes of anatase (Figure 1(c), I41/amd, JCPDF card number 73-1764), respectively, which indicates the high crystallinity of our product. The crystallite size can be estimated from the widening XRD peak via the Scherrer equation described as follows: (1)
d
=
k
λ
β
cos
⁡
θ
,where d is the crystallite size; k is a constant (0.89); λ is the X-ray wavelength (1.5418 Å for Cu K
α); β (radian) is the full-width at half-maximum for the (101) peak at 2θ = 25.6°; and θ is the angle of the diffraction peak (degree). The estimated average crystallite size based on the (101) peak isca. 22.6 nm.Figure 1
Characteristic XRD pattern of (a) P25; (b) the prepared hierarchical TiO2 nanotubes sample; and (c) JCPDF card number 73-1764 of anatase TiO2.The morphology of obtained TiO2 sample was observed by SEM and TEM. Figure 2(a) is the overview FE-SEM image of the sample, which shows that the titania sample really inherits the complex network structure and the hierarchical morphology of the original filter paper template, and the resulting titania is composed of many randomly intersecting titania microfibers with high aspect ratios. From the further magnified SEM image in Figure 2(b), we can observe that the tube wall of the individual titania microtube is composed of lots of fine nanotubes, which measured the tubular structure with inner diameters of 80–90 nm and tube wall thickness of 30–40 nm. Figure 2(c) is a typical TEM image of an individual titania nanotube, whose hollow interior can be clearly identified. The inset in Figure 2(c) indicates that abundant intergranular pores with size ofca. 12 nm located in the tube-wall, which came from the aggregation of small TiO2 nanoparticles. From the HR-TEM image shown in Figure 2(d), it can be observed that the average grain size of porous TiO2 nanotubes is ~20 nm, which consists with the result of XRD analysis. Besides, the HR-TEM image in Figure 2(d) also shows that the measured lattice spacing of sample is 0.35 nm, corresponding to the lattice distance of anatase (101) planes, which further confirms the anatase crystalline phase of the nanotubular titania product. Several multicrystal diffraction rings ascribed to the anatase phase can be observed clearly in the SAED pattern of sample (Figure 2(d) insert), which are particularly indexed (from small to large rings) as 101 (d
=
0.35 nm), 004 (d
=
0.237 nm), 200 (d
=
0.189 nm), and 211 (d
=
0.166 nm). These results agree well with the XRD analysis described above.Figure 2
Micromorphology observations of prepared porous TiO2 nanotubes. (a) FE-SEM image. (b) Further magnified SEM image. (c) TEM image of individual titania nanotube and magnified TEM image of tube wall (insert). (d) HR-TEM image and SAED pattern (insert).
(a)
(b)
(c)
(d)According to the IUPAC classification of porous materials, the nitrogen adsorption and desorption curve of the obtained hierarchical porous TiO2 nanotubes material in Figure 3(a) show a type II isotherm pattern with a hysteresis loop of type H3 in the IUPAC classification [23], revealing the presence of abundant intergranular pores in the tube wall. The capillary condensation step at relative pressure about 0.3 (P
/
P
0) might be attributed to the uniform mesopores in the tube walls. And the sharp step of capillary condensation at the relative pressure range of 0.5–0.95 (P
/
P
0) is caused by the existence of macropores in the samples. From the desorption branch of isotherm as shown in the inset of Figure 3(a), the pore distribution plot of the synthesized materials was determined by the BJH (Barrett-Joyner-Halenda) method. The result indicates that the synthesized titania has mesopores with an average pore diameter of ~12 nm, which is higher than the commercial P25 (Degussa) materials (ca. 6.9 nm). The BET specific surface area of the obtained titania sample was estimated about 27 m2/g and the total pore volume was about 0.11 cm3/g. Figure 3(b) is characteristic FT-IR absorbance data of our porous TiO2 nanotubes sample. In this figure, two broad absorption bands centered around 3375 and 2995 cm−1 are observed obviously. The former is associated with the hydroxyl groups of Ti-OH at weak surface active sites and the latter is attributed to water complexes that are strongly bound to the TiO2 surface. Besides, a weak sharp absorption band, which resulted from the deformation vibration for H-O-H bonds of the physisorbed water, and a mixed weak peak caused by the formation of the linear chain of Ti-O-Ti are located at about 1640 cm−1 and 400–480 cm−1, respectively. However, the absorption bands corresponding to the isolated OH group vibrations around 3665 and 3715 cm−1 are both relatively weak that they are overlapped by the broad band, which indicates a high degree of hydration on the anatase TiO2 surfaces.Figure 3
(a) N2 adsorption/desorption isotherms of the prepared TiO2 nanotubes and BJH pore-size distribution plot (insert). (b) FT-IR spectrum of the obtained porous TiO2 nanotubes.
(a)
(b)Band gaps (E
g) of the hierarchical porous TiO2 nanotubes and P25 were estimated according to the equation as follows [24]: (2)
α
=
B
h
ν
-
E
g
n
h
ν
,where α is the absorption coefficient, B is an absorption constant, h is Planck’s constant, E
g is band gap, and n equals 1/2 for direct transition and 2 for indirect transition.Figure4(a) presents the UV-Vis spectra of the TiO2 nanotubes and P25. There is a similar striking feature for the TiO2 nanotubes and P25 that the broad absorption region extends to about 400 nm. As the absorbance (A) is proportional to the absorption coefficient (α), A can substitute for α
. Plots of A
h
ν
2 versus h
ν from the spectral data in Figure 4(a) are presented in Figure 4(b). The intercept of the tangent to the linear part of the curve gives a good approximation of the band gap energies of the samples. Extrapolating the linear part of the curves for the porous TiO2 nanotubes and P25 gives their direct band gaps of 3.43 eV and 3.36 eV, respectively. These values are very close to 3.3 eV for the experimental bulk crystal [25] and the calculated value of 3.45 eV corresponds to X
1
a
→
C
1
b direct interband transition [26]. However, when the curves are plotted as A
h
ν
1
/
2 versus h
ν, good linear relationships are obtained. Consequently, the absorption features in Figure 4(c) are those of the allowed indirect band transitions. Extrapolating the linear part of the curves for our porous TiO2 nanotubes and P25 in Figure 4(c) gives their indirect transition of 2.81 eV and 2.73 eV, respectively. These values are very similar to the calculated value of 2.91 eV corresponding to X
1
a
→
G
1
b indirect interband transition [27]. The results above indicate that the optical properties of TiO2 nanotubes are better than commercial P25 material.Figure 4
(a) UV-Vis absorption spectra of the TiO2 nanotubes and P25. (b) The plots of A
h
ν
2 versus the photon energy (
h
ν
). (c) The plots of A
h
ν
1
/
2 versus the photon energy (h
ν).
(a)
(b)
(c)Using X-ray photoelectron spectroscopy (XPS), we examined the surface chemical state and element composite of our porous TiO2 nanotubes. The XPS full spectrum shown in Figure 5(a) indicates that our TiO2 sample only contains Ti, O, and C elements with the chemical binding energies of Ti 2p (459.4 eV), O 1s (530.4 eV), and C 1s (285.4 eV), respectively. We also measured the C 1s core levels to detect possible doped carbon in TiO2 lattice. Deconvolution of the C 1s peak in the XPS spectrum (Figure 5(b)) shows the presence of two types of carbon bonds, that is, C-C (284.6 eV) and Ti-O-C (288.6 eV). Doped carbon would exhibit carbon ion characteristics peaked at approximately 281.8 eV, which is different from the background peak at 284.6 eV (carbon tape with C
0). As shown in Figure 5(b), there is no carbon ion peak (281.8 eV) for TiO2 sample. The presence of the Ti-O-C structure may be derived from the carbon in residual organic surfactant and filter paper. As shown in the Ti 2p spectral region (Figure 5(c)), there are three peaks at 458.9 eV, 464.4 eV, and 472.3 eV, respectively. These peaks can be attributed to Ti 2p1/2, Ti 2p3/2, and their satellite peaks with typical characteristic Ti4+ binding energies. All Ti 2p signals are symmetric with no shoulders at the lower energy sides, which are significantly different from the spectra of TiO2 doped with carbon or other impurities. According to the high resolution X-ray photoelectron spectra of O 1s, as shown in Figure 5(d), there is a symmetric peak at 530.3 eV, indicating that the oxygen mainly exists in the form of lattice oxygen (O-Ti) in the sample.Figure 5
(a) XPS full spectrum of TiO2 sample. (b) High resolution XPS of C 1s and subpeak fitting chart. (c) High resolution XPS of Ti 2p and subpeak fitting chart. (d) High resolution XPS of O 1s and subpeak fitting chart.
(a)
(b)
(c)
(d)


## 3.2. Photocatalytic Degradation of MO

TiO2 material is the most promising photocatalyst because of its high photosensitivity and wide band gap. Here, we evaluate the photocatalytic performance of the as-prepared porous TiO2 nanotubes by monitoring the degradation of methyl orange (MO) under UV irradiation. Before UV irradiation, the mixture of MO solution and the catalyst was stirred in the dark for 30 min to ensure that MO was adsorbed to saturation on the surface of catalyst. Figure 6 shows the degradation efficiency of MO over the as-prepared TiO2 photocatalyst. As shown in Figure 6(a), the color of the solutions gradually fades with the time increasing, which implies the gradual decrease of MO concentration in mixture. Figure 6(b) shows the absorption spectra of MO solution in the presence of the porous TiO2 nanotubes under exposure to UV light for different periods of time. The result exhibits that the characteristic absorption peak of MO at 464 nm rapidly decreased with the increase of exposure time and disappeared after 20 min, which shows that MO is almost completely degraded under exposure to UV light for 20 min. This demonstrates that the porous TiO2 nanotubes prepared through the present method possess excellent photocatalytic performance for degradation of MO.Figure 6
(a) Photographs and (b) adsorption spectra of MO solutions in the presence of porous TiO2 nanotubes irradiated by UV lamp at different periods of time.
(a)
(b)Figure7 shows the degradation efficiency of MO without and with the presence of catalysts. Blank experiment in the absence of catalyst but under identical UV irradiation for 20 min shows that only 2.4% of MO was degraded (black line in Figure 7(a)). Under the same condition, the existence of commercial Degussa P25 catalyst resulted in the increase of degradation percentage of MO to 45.4% under exposure to UV light for 20 min (blue line in Figure 7(a)). However, in the case of the porous TiO2 nanotubes, it is interesting to note that 93% of the MO in the solution is degraded after 20 min of UV irradiation (red line in Figure 7(a)).Figure 7
Photodegradation kinetics of methyl orange in the presence of porous TiO2 nanotubes. (a) Plot for the degradation percentage (C
/
C
0) of MO solutions versus time intervals. (b) ln
⁡
(
C
/
C
0
) as a function of reaction time.
(a)
(b)Figure7(b) shows the kinetics of photocatalytic degradation of MO under UV irradiation fitted by the first-order kinetics model:(3)
ln
⁡
C
C
0
=
-
k
t
,where k is the pseudo-first-order rate constant (min−1). As shown in Figure 7(b), the photodegradation of MO obeys pseudo-first-order kinetics. The calculated pseudo-first-order rate of MO with porous TiO2 nanotubes (0.10141 min−1) is much larger than that of MO with P25 (0.02477 min−1), which means that the introduction of porous TiO2 nanotubes leads to much more significant enhancement of MO degradation rate under UV light irradiation than that of P25. It can be concluded that the porous TiO2 nanotubes exhibit more prominent photocatalytic activity than the commercial Degussa P25.It has been reported that the photodegradation activity of TiO2 material is mainly attributed to the factors including surface area, absorptive capacity, grain size, crystalline, and morphology. Generally, high surface area and small grain size are most important for promoting the photocatalytic performance of titania materials [28–30]. However, other factors are able to influence their photocatalytic activities to a large extent as well. Though our porous TiO2 nanotubes possess a lower surface area (27 m2/g) than commercial Degussa P25 (20 nm, 48.9 m2/g) and a weaker adsorptive capacity in the dark adsorption of photocatalytic test (Figure 7(a)), as well as the quite similar grain size (~20 nm) with that of Degussa P25, the porous TiO2 nanotubes exhibit much higher photocatalytic activity than commercial Degussa P25 as depicted in Figure 7. The possible reason for the higher photocatalytic performance of porous TiO2 nanotubes can be ascribed to the following two factors. Firstly, the crystallinity of TiO2 materials is an important factor for influencing their photocatalytic performance as well [31, 32]. As can be observed in Figure 1, the obtained porous TiO2 nanotubes exhibit fully pure anatase crystalline form and rather high crystallinity, which means less defects inside the sample and is in favor of the separation of photogenerated electron-hole pairs and the lower recombination of photogenerated hole-electron. That means that the high crystallinity of the porous TiO2 nanotubes is beneficial to their photocatalytic performance. Besides, the abundant pores in the tube wall of the samples benefit for the penetration of light waves and lead to high mobility of photogenerated charges [31, 32]. Meanwhile, the abundant pores also facilitate the mass transport and reactants can deeply enter the catalyst through these pores, which could improve their photocatalytic activity greatly. Therefore, in spite of the lower surface area and similar grain size compared with P25, the synergistic effect arising from the high crystallinity and abundant pores on the tube wall of porous TiO2 nanotubes results in the final excellent photocatalytic performance.Figure8 is the characterization of porous TiO2 nanotubes after performing the MO degradation reaction. It shows that the morphology and microstructure of the TiO2 prepared through the present method were still well maintained after the reaction (Figures 8(a) and 8(b)). Meanwhile, compared with XRD pattern of the sample before photocatalytic reaction (black line in Figure 8(c)), the crystalline of porous TiO2 nanotubes was not obviously destroyed during the reaction (red line in Figure 8(c)). The result indicates that the prepared porous TiO2 nanotubes exhibit good stability during the photocatalytic degradation for MO.Figure 8
(a) Low magnified and (b) large magnified SEM images of porous TiO2 nanotubes after photocatalytic reaction for MO. (c) XRD patterns of porous TiO2 nanotubes before and after photocatalytic degradation for MO.
(a)
(b)
(c)


## 4. Conclusions

In summary, hierarchical porous TiO2 nanotubes were successfully synthesized through a facile and efficient template synthesis strategy with the natural cellulose substance (filter paper) and triblock copolymer (Pluronic P123) micelles as dual templates. The resultant porous TiO2 nanotubes really inherited the hierarchical morphologies of the initial cellulose substances and consisted of many randomly intersecting titania microfibers with high aspect ratios. The further microstructure observation shows that the product was endowed with not only the tubular structure with tube wall thickness of 30–40 nm but also abundant intergranular pores with a diameter ofca. 12 nm on the tube wall. The result of photocatalytic degradation for MO shows that the photocatalytic activity of the porous TiO2 nanotubes is much higher than that of commercial Degussa P25. Under the UV irradiation in a short period of 20 minutes, 93% of the MO in the solution with porous TiO2 nanotubes was degraded while the value for the commercial Degussa P25 is only about 45.4%. It can be concluded that the introduction of porous TiO2 nanotubes leads to much more significant enhancement of MO degradation rate than that of P25. It indicates that the porous TiO2 nanotubes prepared through the present method exhibit more prominent photocatalytic activity than the commercial Degussa P25. The simple and stable method for preparing enhanced photocatalytic activity porous TiO2 nanotubes could be extended to the fabrication of various catalysts for the degradation of organic dye pollutants.



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*Source: 3532817-2016-06-16.xml*