SN Applied Sciences

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Photodegradation of methylene blue under direct sunbeams by synthesized anatase titania nanoparticles

  • Amar KunduEmail author
  • Aparna Mondal
Research Article
Part of the following topical collections:
  1. 1. Chemistry (general)


Surfactant-assisted titania nanoparticles have been successfully synthesized using an inorganic salt of titanium by controlled hydrolysis method. Anionic (Sodium dodecyl sulfate), nonionic (Brij C10) and cationic (Dodecyl amine) surfactants have been used to synthesize the titania nanoparticles. The XRD patterns of the 500 °C annealed nanoparticles exhibit technologically important anatase phase. Anatase to rutile transformation is observed for Ti-D-650 nanoparticles at lower temperature. It has been observed that the Ti-S-900 nanoparticles retained to the anatase phase at higher temperature up to 900 °C. The Brij C10 assisted nanoparticles (Ti-B-500) exhibited high surface area and lower crystallite size compared to other nanoparticles. In addition, Ti-B-500 samples exhibited wormlike mesopores structure. XPS study confirmed the presence of sulphur in Ti-B-500 nanoparticles, which creates an O–S mixed environment into the lattice. The nanoparticles also showed a red shift in the UV-DRS study with a lower band gap (indirect) energy about 3.02 eV. Impedance spectrum of the Ti-B-500 nanoparticles confirmed the enhanced electron–hole separation rate involved in the photodegradation process. Photodegradation rate of methylene blue [2 × \(10^{ - 5}\)(M)] with Ti-B-500 nanoparticles under direct sunbeams has been observed to be higher compared to other surfactant-assisted nanoparticles. The rate of photodegradation is found to be best at pH = 6.7 with a rate of 0.0864 \({ \hbox{min} }^{ - 1}\) and the catalyst showed best reusability even after five cycles of experiment.


Titania Mesoporous Surfactants Photocatalysis 

1 Introduction

Now a days, considerable attention has been devoted on developing clean and ecological energy sources owing to the cumulative energy and environmental challenges [1, 2, 3, 4, 5, 6, 7]. Solar energy has the potential to produce a green and environmentally friendly society and by using it, numerous research devoted to empowering the transformation of solar energy into operational energy. Solar energy is being used in solar cells, photocatalysis, photo-electrochemical cells, and in other various applications [8, 9, 10, 11, 12]. Among various semiconductors, titania (TiO2) has always been the one widely studied due to its chemical stability, water insolubility, low cost, promising photo-chemical property and non-toxic nature [13, 14, 15, 16]. It has also been used intensively as a photocatalyst for wide range of applications along with H2-generation, CO2 reduction and in environmental remediation [17, 18, 19]. Over the past few decades, researchers have given remarkable efforts to improve the photocatalytic activity of TiO2-based materials [20, 21, 22, 23, 24]. According to the literature, to improve the photocatalytic activity, generation, migration, and separation of photogenerated electrons and holes are essential which can be achieved by preparing high crystalline small TiO2 crystals [25, 26]. Anatase phase of TiO2 is mostly used as photocatalyst over rutile TiO2 because of higher redox potential and lower electron–hole pair recombination rate [27]. However, anatase to rutile phase transformation occurs just above 600 °C due to thermodynamically metastable nature of the anatase phase. Therefore, preparing stable anatase TiO2 nanoparticles with higher crystallinity by thermal treatment is bit difficult [28]. Earlier, numerous procedures are developed to produce TiO2 nanoparticles with controlled shape, size and porosity for use in ceramics, composites, thin films, and catalysts [29, 30, 31, 32, 33, 34, 35]. Today various methods such as sol–gel, micelle and inverse micelle, hydrothermal, solvothermal, direct oxidation, chemical and physical vapor deposition, electrodeposition, sonochemical, microwave, ultrasonic spray pyrolysis and so on have been developed to synthesize TiO2 nanoparticles [36, 37, 38, 39, 40, 41, 42, 43, 44, 45]. Among the above mentioned methods, the micelle and inverse micelle (also known as microemulsion method) approaches are cost-effective and energy efficient to produce nanometer-sized particles and porous materials [46, 47, 48, 49]. The important feature of these methods is to constrain the reactions in the nano-reactors core of reverse micelles, which control the particle size and porosity generated when the micelles are intact in solution and removed during calcination.

In this work, the TiO2 nanoparticles are synthesized with and without different surfactant templates (anionic, non-ionic and cationic) to utilize the nanoparticles for photodegradation of organic dye molecules. Moreover, the experiment is carried out under direct sunlight to use the catalyst in real time applications.

2 Experimental section

2.1 Chemicals used

Titanium (IV) oxysulphate (TiOSO4) (as a TiO2 precursor) and Brij C10 have been procured from Aldrich Chemicals. Sodium dodecyl sulphate (SDS), dodecylamine (DDA), Ammonia solution (about 25%) (as precipitating agent), isopropanol and ethanol have been procured from Merck Chemicals. All chemicals were of analytical reagent grade and used without any additional purification. Deionized water from ELGA PURELAB Option-Q water purification system has been used during the synthesis.

2.2 Preparation of titania nanoparticles

Titania nanoparticles have been prepared by controlled precipitation of the precursor by ammonia solution in presence of surfactant templates. In a typical procedure, the surfactant solutions are prepared separately as follows; Sodium dodecyl sulfate (SDS), dodecyl amine (DDA) are dissolved in water and Brij C10 (average Mn ~ 683) in isopropanol at 15 wt% ratio and stirred constantly for 30 min. Different surfactant solutions are added dropwise separately to each set of 0.5(M) precursor solution followed by constant stirring for 1 h. Then to each set of mixed solution (precursor and surfactant solutions), NH4OH solution (30 vol%) is added slowly to obtain the precipitate until the pH of the solutions becomes 7. The resulting precipitates are kept under aging about 2 days at room temperature. The precipitates are filtered and washed with distilled water for numerous times and through ethanol 4–5 times to remove excess surfactants and other impurities. The subsequent precipitates are dried in oven at 60 °C and then calcined at 500 °C, 650 °C and 900 °C in air atmosphere at a heating rate of 4°/min for 2 h. For evaluation purpose, TiO2 samples are prepared using the same procedure without surfactant template. The synthesized powders are assigned as “Ti—(S, B, and D)—T”. S—represent sodium dodecyl sulphate, B—represent Brij C10, D—represent dodecylamine, and T—represent the annealed temperatures. The titania nanopowder synthesized without surfactant template is named as Ti-T.

2.3 Chemical characterization of nanoparticles

In order to analyze the phase formation or crystallization X-ray diffraction has been carried out at room temperature in Rigaku Ultima IV X-ray diffractometer using 0.154056 nm Cu-Kα radiation. Rietveld refinement is carried out with the help of Full Prof Suite using standard lattice parameters, cell volume, Wyckoff positions and Pseudo-Voight profile function is used to refine the XRD patterns. First, using linear interpolation method, background data has been created and the scale factor, zero correction, displacement, lattice parameters, full-width half-maximum (FWHM) parameter, and Wyckoff positions are refined one by one to acquire the best fit. The occupancy of all the atomic sites are kept fixed during the process. We have carried out the refinement and other characteristic measurement for the 500 °C annealed nanoparticles because these samples only hold the pure anatase phase. The Scherrer’s equation is applied to estimate the crystallite size using FWHM of the (101) peak of anatase. Raman spectra are recorded in Witec Alpha-300 Confocal Raman microscope using solid-state laser source with an excitation line of 532 nm. N2 adsorption/desorption isotherms are obtained on a Quantachrome Autosorb-1 apparatus after degassing the samples at 200 °C for 2 h at relative pressure range 0.03–1.00. High-Resolution micrographs of the annealed samples are recorded using FEI Tecnai F30 S-TWIN equipped with QANTEX EDS detector. The band gap energy of the nanoparticles is calculated from Kubelka–Munk equation using UV–vis diffuse reflectance spectra (UV–vis DRS), taken with BaSO4 as reflectance standard in UV-2450 Shimadzu spectrometer equipped with an integrating sphere assembly. X-ray photoelectron spectra (XPS) are studied by Photoemission Electron Spectroscopy (PES) beamline BL-14 of the Indus-2 synchrotron source in an ultrahigh vacuum with the source of monochromatic X-ray beam energy of 4357 eV. A double-crystal Si (111) monochromator and SPECS in the PHOIBOS 225 HV hemispherical electron energy analyzer has been used to record the spectra. The binding energy (BE) is calibrated using the C 1s peak. Electrical measurements are carried out with sample pellets. To prepare the pellets first, the nanoparticles are mixed with a binder (PVA = polyvinyl alcohol) and shaped in the pellet form. Then the pellets are heated at 400 °C for 2 h to remove the binder. The pellets are then polished with emery paper and cleaned using acetone. To make an electrode, the pellets are coated with silver paint on both surfaces and then dried at 150 °C for 2 h to remove the moisture present in the samples. In this investigation HIOKI IM -3570 Impedance analyzer with a computer set up is used in the frequency range 100 Hz–1 MHz to collect the data. The impedance data are fitted using Zview2 software.

2.4 The photocatalytic activity and recyclability tests

The photocatalytic effectiveness of all the nanoparticles are evaluated by the extent of degradation of methylene blue (MB) in an aqueous solution under direct solar light irradiation without maintaining the intensity of sunlight during subsequent reactions. In a typical experiment, a 200 mL of 2 × 10−5(M) MB solution was taken in a 500 ml beaker to which photocatalysts of 200 mg (1 g/L) were added separately with vigorous stirring. An aliquot of the solution is taken to measure the concentration of the adsorbed dye after 30 min. of adsorption–desorption equilibrium in the dark. Then the dye solutions are set aside under sunlight at room temperature for the photodegradation process to take place. Sample aliquots are withdrawn from the reaction mixture at 10 min. time interval and then centrifuged. The dye concentration of the residual solution is analyzed using UV–Vis spectrophotometer. Changes in the MB concentration are measured from its characteristic absorption band maximum (λmax = 663 nm). To find out the effect of pH on photodegradation, we have adjusted acidity and basicity of the dye solution using hydrochloric acid (HCl) and sodium hydroxide (NaOH), respectively. Effect of catalyst loading on the photodegradation process is also investigated. Moreover, we have examined the catalytic activity on photodegradation by repeating it for five cycles of experiment.

3 Results and discussion

3.1 X-ray diffraction

Figure 1a shows the X-ray diffraction (XRD) pattern of 500 °C calcined TiO2 nanoparticles, which manifest the formation of anatase phase (tetragonal) with absence of any secondary phase. The XRD pattern of anatase phase is well matched with the JCPDS card no. 21-1272 and the basic parameters from the JCPDS are used for the refinement. The presented refinement patterns shows a good reasonable fit between the experimental and simulated data. The obtained refined parameters are shown in Table 1. XRD patterns of 650 °C calcined titania nanoparticles are presented in Fig. 1b. The results indicate more sharp peaks, which specifies the formation of higher crystalline particles. Except Ti-D-650, all other 650 °C annealed nanoparticles retained to the anatase phase. Moreover, the results show that DDA templating actually helps in increasing the anatase to rutile transformation at lower temperature. The Ti-D-650 nanoparticles contain anatase and rutile phases with 81% and 19%, respectively. The content of anatase phase is calculated using Eq. 1, where FA, IA, and IR represent percentage of anatase phase, intensity of the anatase peak and intensity of rutile peak respectively. Figure 1c represents the XRD profile of 900 °C annealed nanoparticles. The data indicates that except Ti-S-900, the other nanoparticles have transformed from anatase to rutile phase fully or partially. The Ti-S-900 nanoparticles retained to anatase phase at higher temperature up to 900 °C. Best to the author’s knowledge, anatase phase stability at that higher temperature in pure titania till now not has been reported. Steven J. Hinder et al. reported pure anatase phase stability up to 850 °C [50]. Crystallite sizes (Dhkl) of the nanoparticles have been calculated using the Scherrer’s Equation (Eq. 2), where “λ” is the wavelength and “\(\upbeta_{hkl}\)” is the full width at half maximum. Among the 500 °C calcined particles, Ti-B-500 formed the lower crystallite size about 8.0 nm. The crystallite size (anatase lattice) of all nanoparticles are presented in Table 1.
Fig. 1

Powder X-ray diffraction (PXRD) pattern of a 500 °C (Rietveld refined) b 650 °C and c 900 °C calcined titania nanoparticles

Table 1

Rietveld refined parameters (only 500 °C heated samples) and crystallite size of prepared titania nanoparticles

Sample name

Lattice parameters

Crystallite size (nm)

a = b (Å)

c (Å)

Cell volume (Å3)




500 °C

650 °C

900 °C








































$${\text{F}}_{\text{A}} = 100 - \left( {\frac{1}{{1 + 0.8({\text{I}}_{\text{A}} \left( {101} \right)/{\text{I}}_{\text{R}} \left( {110} \right)}}} \right)100$$
$${\text{D}}_{\text{hkl}} = \left[ {\frac{{0.9\uplambda }}{{\upbeta_{hkl} {\text{Cos}}\uptheta }}} \right]$$

3.2 Raman analysis

Structural phase of TiO2 nanoparticles is further investigated using Raman spectroscopy. Figure 2 displays the Raman shifts profile in TiO2 nanoparticles. The scattering bands are located at 148.4–151.3 (Eg), 397.1–401.6 (B1g), 520.8–525.2 (B1g + A1g), and 642.4–645.6 cm−1 (Eg), corresponding to the characteristic peaks of anatase phase of TiO2. The Eg mode is due to the symmetric stretching vibration of O–Ti–O, the B1g mode is associated with symmetric bending vibrations of O–Ti–O in TiO2, and A1g mode is the result of asymmetric bending vibration of O–Ti–O. From the Raman spectra, broadening and shifting of Raman active modes (to higher wavenumber) are observed for Ti-B-500 nanoparticles, which is due to the lower crystallite size of the nanoparticles. Change in crystallites size (to lower value) changes the vibrational properties of the Ti-B-500 nanoparticles. Owing to the size-induced radial pressure, a volume contraction occurs within the nanoparticles. The interatomic distances in the nanoparticles are decreased which leads to an increase in the force constant, resulting in shifting of Raman peaks towards higher wavenumber [51]. The broadening of the Raman peak is due to the lattice defects which might be created due to the oxygen vacancies displacing the oxide ions from their normal lattice positions [52].
Fig. 2

Raman shifts pattern in Ti-(S, B and D)-500 nanoparticles

3.3 Microstructural analysis

The morphology of the nanoparticles has been characterized by FESEM as shown in Fig. 3a–d. As we can see, the images show less particle agglomeration in surfactant-modified nanoparticles compared to Ti-500. The surfactant templating supports the synthetic process to generate less nucleated homogenous polymorphs. The particle size distribution of titania nanoparticles are presented in their corresponding FESEM images (insets). Ti-S-500, Ti-B-500, and Ti-D-500 have average particle size of 24.4, 17.5, and 22.2 nm respectively. It was very difficult to calculate the particle size for Ti-500 due to its agglomerated nature.
Fig. 3

FESEM Micrographs of a Ti-S-500, b Ti-B-500 c Ti-D-500 and d Ti-500 nanoparticles

The nanoparticles are also observed by the high resolution transmission electron microscope (HRTEM) to identify the nucleation nature of nanoparticles. Ti-S-500 nanoparticles shown in Fig. 4a are found to be weakly agglomerated, and of uniform in size. Figure 4a.1 displays the lattice fringes corresponding to the anatase phase with inter-planar (101) distance of 0.364 nm. The stable regular and worm-like pores formed in Ti-B-500 nanoparticles are shown in Fig. 4b.3. Development of anatase nanocrystals confirmed from the formation of lattice fringes with an inter-planar (101) distance of 0.357 nm is shown in Fig. 4b.1. Figure 4c shows the non-porous microstructure of Ti-D-500 nanoparticles with a geometrical shape and the particles have an anatase phase with inter-planar (101) distance of 0.364 nm. Figure 4d shows the agglomerated nanoparticles of Ti-500, formed via the growth of bigger particles after nucleation as there is an absence of surfactant throughout the synthetic process. The particles have anatase phase with inter-planar (101) distance of 0.359 nm. The ring pattern observed in selected area electron diffraction (SAED) pattern in Fig. 4a.2, b.2, c.2 and d.2 indicates the development of well crystalline nature in all nanoparticles.
Fig. 4

TEM Micrographs, HRTEM micrographs (inset), and SEAD pattern (inset) of a Ti-S-500, b Ti-B-500 c Ti-D-500 and d Ti-500 nanoparticles

In order to understand the nucleation process of titania nanoparticles, we have proposed a mechanistic pathway about how the particles are designed according to their microstructure. Due to the ionic nature of SDS and DDA, they are dissolved in water and also they started to form micelle in solution at CMC. The surfactant head groups (polar groups) of the micelles attracted first the precursor ions (Ti4+) and then the precipitating agent that was introduced. As the surfactants are polar in nature, they are organized in solution to form a unilameller vesicle in which, both the precursor and precipitating agent are present. After that, they formed the corresponding precipitate (TiO(OH)2) into the core of the vesicle. During the ageing process, the precipitate gets aggregated into core and while washing the precipitate, the excess surfactant from the solution gets removed. When the precipitate is annealed at 500 °C, the corresponding oxide (TiO2) is formed with a geometrical shape due to the complete removal of the surfactant. The nucleation of the nanoparticles is illustrated in Fig. 5a. When the non-ionic (Brij C10) nature of the surfactant prevails, strong interaction between the solvent and surfactant does not operate. As a result, the surfactant molecules get self-aggregated in different shapes in the solution as shown in Fig. 5biii and the precipitate forms without any core, whereas the ionic surfactants does it. After ageing and washing, the precipitate is annealed at 500 °C, which removes the surfactant from the samples generating a pore within the resultant oxide.
Fig. 5

A plausible mechanistic pathway to the formation of a Ti-S-500, Ti-D-500 and b Ti-B-500 nanoparticles

3.4 BET surface area and pore size distribution

Figure 6a shows the nitrogen adsorption–desorption isotherms of nanoparticles. All the nanoparticles show type IV isotherm with a hysteresis loop, but the isotherm of Ti-B-500 is the vibrant one which confirms the presence of mesopores [53]. Specific surface area, pore diameter and total pore volume of the nanoparticles are listed in Table 2. Ti-B-500 nanoparticles have a higher surface area of 117 m2/g compared to others due to the formation of pores [also confirmed in TEM micrographs (Fig. 4b.3)]. The structural properties, surface area, and pore volume indicate that the Brij C10 surfactant assisted TiO2 has a technologically advanced anatase nanostructure. Figure 6b illustrates the pore-size distribution plot of the corresponding nanoparticles. A sharp peak appeared approximately at 8 nm for Ti-B-500 and it is gradually decreased to 55 nm indicating the availability of large amount of mesopores along with some macropores (55–150 nm). Ti-500 nanoparticles also have a sharp peak like Ti-B-500 indicating the formation of pores, but it has not been found in TEM, which suggest that it may appear due to the formation of grain boundaries.
Fig. 6

a N2 adsorption–desorption isotherms and b pore size distribution plot of Ti-(S, B and D)-500 nanoparticles

Table 2

Surface area, pore diameter and pore volume of Ti-(S, B and D)-500 nanoparticles

Sample name





Surface area (m²/g)





Pore diameter (nm)





Total pore volume (cm 3 g −1 )





3.5 XPS analysis

X-ray photoelectron spectroscopy (XPS) has been carried out to understand the elemental identification and chemical states of element present in the titania nanoparticles. Figure 7 displays the XPS survey spectra, high-resolution spectra of Ti 2p and O 1s and the binding energy (BE) values along with atomic percentage of the elements. Survey spectrum confirmed the presence of Ti, O, and C atoms in all the nanoparticles. The carbon peak is attributed to adventitious hydrocarbon from XPS instrument itself. Additionally, the Ti-B-500 nanoparticles contain N-atom (1.32 at.%) and S-atom (1.57 at.%) as evident from the survey spectrum. The high-resolution spectra of Ti 2p of Ti-B-500 represent the binding energies of Ti 2p3/2 and Ti 2p1/2, which are centered at 457.3 eV and 462.3 eV respectively, corresponding to a spin–orbit coupling. The high-resolution O 1s peak could be deconvoluted into two peaks at 528.1 eV and 530.1 eV, corresponding to Ti–O–Ti and Ti–O–H bonds, respectively. According to the previous literature, pure TiO2 has binding energies of Ti 2p3/2 and Ti 2p1/2 at 459.0 eV and 464.7 eV respectively [54]. Here, the pure Ti-500 nanoparticles have binding energies of Ti 2p3/2 and Ti 2p1/2 at 458.9 eV and 464.9 eV respectively. Therefore, the lower shifts in binding energy of Ti-B-500 nanoparticle are due to the presence of mixed O–S atom into the lattice environment which is confirmed by National Institute of Standards and Technology (NIST) XPS database [55]. Binding energies of Ti 2p (Ti 2p3/2 and Ti 2p1/2 states) and O 1s (deconvoluted peaks corresponding to Ti–O–Ti and Ti–O–H bonds) in other nanoparticles are indicated to their corresponding high-resolution spectra. The source of sulphur in Ti-B-500 nanoparticles is from the precursor (TiOSO4). To make the precipitates sulphate free, each time the filtered solutions are cross checked with BaCl2 test. However, during synthesis of Ti-B-500, some sulphate ions remained with the surfactant Brij C10. Due to non-ionic nature of the surfactant, complete removal does not take place and after calcination, sulphur atoms are introduced to Ti-B-500 nanoparticles.
Fig. 7

XPS full survey spectrum and high-resolution spectra of Ti 2p and O 1s in Ti-(S, B and D)-500 nanoparticles

3.6 Band gap measurement

The optical responses of the nanoparticles are investigated using UV-DRS as shown in Fig. 8a. The Ti-B-500 nanoparticles show an absorption edge around 416 nm and the other nanoparticles are closer to 395 nm, i.e. a red shift. The red shift may be attributed to the presence of sulphur atom in the lattice. Both Ti 3d and O 2p orbitals in pure TiO2 are the participant of the valence band (VB) and conduction band (CB). Splitting of the Ti 3d orbital (VB) generates two parts: the t2g and eg states and CB divided into the lower and upper parts. Presence of sulphur (the S 3p states) in the lattice may be contributing to the formation of VB with the O 2p and Ti 3d states because some extents of the S 3p state is delocalized. Thus, the mixing of S 3p states with VB increases the width of the VB itself [56]. This result arises in the red shift and consequently decreases the band gap energy in Ti-B-500 nanoparticles. The direct and indirect band gap energies are calculated using Tauc’s plot and marked in the inset of Fig. 8b and c, respectively.
Fig. 8

a UV–vis absorption spectra, b direct band gap, c indirect band gap and d the schematic diagram of S 3p modified VB of Ti-(S, B and D)-500 nanoparticles

3.7 CIS analysis

The complex impedance spectroscopy (CIS) is a powerful and sensitive characterization technique to investigative the electron-transfer kinetics occurring in different materials, like single crystal, polycrystalline, polymer composite and amorphous ceramics over a wide range of temperatures. Moreover, a relationship between electrical and microstructural properties can be established i.e., the electrical properties of a polycrystalline ceramic depend on its grains, grain boundary and space charge polarization. The electric relaxation process occurring at the microscopic dimensions can be visualized using equivalent circuits to elucidate the experimentally perceived impedance spectra. Resistance (R), capacitance (C), inductance (L) and constant phase elements (Q) are the essentials of an equivalent circuit. These elements are linked in series and/or parallel to describe the relaxation phenomena occurring due to the grains, grain boundary and space charge polarization. The fundamental complex electrical parameters (like admittance (Y*), permittivity (ε*), impedance (Z*), and electric modulus (M*)) obtained from CIS technique are interlinked to each other [57, 58]. The relations between the parameters are expressed as;
  • Complex impedance (Z*) = Zʹ − iZʺ

  • Complex admittance (Y*) = Yʹ + iYʺ = 1∕Z*

  • Complex permittivity (ε*) = εʹ − iεʺ = 1∕iωCoZ*

  • Complex modulus (M*) = Mʹ + iMʺ = iωCoZ*

where single prime (ʹ), double prime (ʺ), i, Co and ω represent the real part, imaginary part, imaginary factor (√ − 1), vacuum capacitance and angular frequency (2πf) of the complex electrical parameters, respectively.
Figure 9a shows the room temperature impedance spectra of the titania nanoparticles. The Nyquist plots are modeled using RQ–RQ circuit and are represented in Fig. 9b. All the samples show formation of two semicircular arcs. The arc at high frequency (1st) is due to the grain property while the low frequency arc (2nd) signifies the grain boundary of the samples. The radius of the arcs gives the resistance of individual grain (Rg) and grain boundary (Rgb). It is observed that Ti-S-500 catalyst (Fig. 9b) has the largest arc radius among the rest. Therefore, it has higher resistance value in both grain and grain boundary. On the other hand, Ti-B-500 displays the low resistance value at grain and grain boundary (i.e., smaller arc radius) due to the porous nature of Ti-B-500 catalyst (Fig. 4b). It is alleged that mesoporous TiO2 is a consequence of the unique character of well-sintered nanograins (at interfaces). Thus, it formed a facile electronic transport path with a long diffusion length as in 1D single crystalline nanorods [59]. Therefore, it is assumed that the enhanced diffusion length for electrons in Ti-B-500 catalyst is because of the formation of accumulation of electrons at the grain–grain interface [60]. Such assembly of electrons at the interface assists electronic conduction across the grains. The resistance values of Ti-D-500 and Ti-500 catalyst are similar and fall between the Ti-B-500 and Ti-S-500. The resistance values of the samples are tabulated in Table 3.
Fig. 9

a Nyquist plots of the complex impedance spectra and b individual fitted Nyquist plots (green line) of the respective titania catalysts. Additionally, the red and blue arc of the semicircles indicates resistance at high and low frequency, respectively

Table 3

Grain and grain boundary resistance values of titania catalysts

Sample name





Grain resistance (kΩ)





Grain boundary resistance (kΩ)





As per CIS analysis, it is observed that Ti-B-500 catalyst has low resistance at both grain and grain boundary, which indicates high charge transfer rate (i.e. larger electron–hole separation). The increased electron–hole separation rate leads to the formation of effective active site to participate in reaction at surface of the catalyst, which shows the enhanced photocatalytic activity in Ti-B-500 catalyst.

4 Photocatalytic application

4.1 Effect of contact time

The photocatalytic activity of the nanoparticles is evaluated in terms of degradation efficiency. Before the photocatalytic experiment, dye adsorption on the respective nanoparticles is examined. The maximum adsorption about 11% is observed for Ti-D-500 nanoparticles during the adsorption–desorption equilibrium. Ti-B-500 nanoparticles showed a maximum of 93% degradation within 30 min under sunlight. The complete degradation of MB using Ti-B-500 is observed after 60 min of sunlight irradiation. Figure 10a displays the percentage of degradation of MB dye at different time interval of the respective nanoparticles. Percentages of photodegradation by Ti-S-500, Ti-D-500, and Ti-500 nanoparticles are observed about 44%, 37%, and 27% respectively. The photocatalytic reactions follow the first order rate kinetics (Fig. 10b). According to the first order rate kinetics, the rate constant (k) can be calculated using the equation \({ \ln }(C_{t} /C_{0} ) = kt\), where,\(C_{t}\) and \(C_{0}\) are the concentrations at “t” time and initial concentration, respectively. The kinetic rate has been calculated and summarized in Table 4, which indicates the photodegradation rate for Ti-B-500 is 4.5, 2.3, and 1.4 times higher than the Ti-500, Ti-S-500, and Ti-D-500 respectively. The rate of MB photocatalytic degradation is found to be comparable to the literature data. Zhang et al. reported MB (1 × 10−5(M)) photocatalytic degradation under visible light (Xe lamp (500 W)) by Au/TiO2–HAP-300 nanocatalyst with rate constant of 0.0955 min−1 [61]. The rate constant of Ti-B-500 and Au/TiO2–HAP-300 are comparable but the concentration of MB is doubled in our case. Pandey et al. reported ZrC nanoparticles which shows 80% photodegradation of methylene blue in 5 h under solar light irradiation with kinetic rate of 0.005 min−1 [62]. Mallakpour et al. synthesized LDH-VB9-TiO2 and LDH-VB9-TiO2/cross-linked PVA nanocomposite via facile and green technique and the prepared samples are studied for MB dye degradation under UV-light irradiation. The rate constants are found to be 0.0085 min−1 and 0.0038 min−1 for LDH-VB9-TiO2 and LDH-VB9-TiO2/cross-linked PVA nanocomposite, respectively [63]. Poureteda et al. synthesized CeO2 nanoparticles and studied photodegradation of MB dye. The kinetics rates are found to be 0.0162 min−1 and 0.0157 min−1 under UV and sunlight irradiation, respectively [64]. Therefore, from the literature data it is clear that the Ti-B-500 catalyst has higher photocatalytic activity. The mechanism of photocatalysis by Ti-B-500 nanoparticles is represented in Fig. 10c.
Fig. 10

a Degradation profile at different time interval, b pseudo-first order rate kinetic plot of the MB degradation using titania nanoparticles and c photodegradation mechanism using Ti-B-500 nanoparticles

Table 4

Pseudo-first order rate kinetic parameters of MB degradation from aqueous solution using Ti-(S, B and D)-500 catalysts

Sample name





Rate (min −1 )





R 2 value





4.2 Effect of pH on photocatalysis

To evaluate the effect of pH, experiments have been carried out with the best photocatalyst Ti-B-500. The concentration of dye and catalyst employed is fixed at 2 × 10−5(M) and 1 g/L respectively. The photocatalytic degradation is performed at pH of ~ 3, ~ 5, ~ 9, and ~ 11 at room temperature. Without addition of any acid or base, the pH of the dye solution has been observed to be 6.7. To adjust the acidic and basic pH value, HCl and NaOH are employed to the dye solutions. The Ti-B-500 nanoparticles noticeably accepted that the photodegradation efficiency on MB and catalysis with pH = 6.7 is higher (Fig. 11) compared to the other pH values which can be ascribed to the surface charge of Ti-B-500 nanoparticles. In the dark environment (during adsorption–desorption equilibrium) there is a slight increase in MB adsorption at the acidic pH range but enormous changes in adsorption have been observed at basic pH range. It is observed that the MB dye adsorption of 9% at pH ~ 3 and 12% at pH ~ 5, whereas 25% at pH ~ 9 and 79% at pH ~ 11. The rate of degradation at various pH is listed in Table 5. The increase of MB adsorption is due to the negative charge developed on catalyst surface at higher pH. So, a strong electrostatic attraction operates between negatively charge catalyst surface and the MB cation [65]. On the other hand, acidic pH helps to produced more number of holes, which involves in oxidation reaction to enhance the degradation process. However, the study shows that the rate of dye degradation is decreased at acidic pH because Ti-B-500 nanoparticles may tend to agglomerate and reduce the surface area which is required for maximum dye adsorption as well as photon absorption. In addition, at the high acidic end there operates a repulsive force between the positively charged catalyst surface and the methylene blue cation. On the other hand, hydroxyl radicals (\({\text{HO}}^{ \cdot }\)) are largely responsible for oxidation process which can be generated in an alkaline solution. So, the catalyst surface becomes negatively charged at pH ~ 9 and strong adsorption occurs with the MB followed by photocatalysis. However, at higher pH (~ 11) the dye adsorbed more on the catalyst surface, which subsequently makes the surface less exposed to the sunlight. Therefore, the creation of \({\text{HO}}^{ \cdot }\) is reduced, i.e., it makes the oxidation reaction slower and decreases the MB degradation rate.
Fig. 11

Effect of pH on photocatalytic degradation using Ti-B-500 catalyst

Table 5

Pseudo-first order rate kinetic parameters of photocatalytic degradation at different pH


~ 3

~ 5

= 6.7

~ 9

~ 11

Rate (min −1 )






R 2 value






4.3 Effect of catalyst dosage on photocatalysis

In order to determine the effect of catalyst dosage, the dye degradation process is carried out at best pH (6.7) with different amount of catalyst dosage ranging from 1.0 to 4.0 g/L. The kinetic profile is shown in Fig. 12. The degradation efficiency is found to be increasing fast with the amount of catalyst (Ti-B-500) from 1.0 to 3.0 g/L. However, it has been found to decrease when the catalyst dosage is increased to 4.0 g/L. When the catalysts concentration increases, total active surface area increases and resulting in more available active sites on catalyst surface [66, 67]. This increases the photon adsorption, which promotes the faster rate of photodegradation. Simultaneously, high catalyst dose increases the turbidity of the suspension, which leads to decrease in the penetration of sunlight and hence decreases the volume of photoactivated-suspension [68]. The rates of reaction at different catalyst dosage are calculated and shown in Table 6. The photodegradation rate increases 1.1-fold when the dosage varied from 1.0 to 2.0 g/L and 1.7-fold when its 3.0 g/L. whereas, the rate is only increased 1.9-fold when the catalyst dosage is 4.0 g/L.
Fig. 12

Effect of catalysts dosage on photocatalytic degradation using Ti-B-500 catalyst

Table 6

Pseudo-first order rate kinetic parameters of MB photodegradation with the variation of catalyst (Ti-B-500) dosage

Catalyst dosage (g/L)







Rate (min −1 )







R 2 value







4.4 Reusability of the photocatalyst

In order to find the stability and the reusability of the catalyst, the experiment is carried out for five times, which is believed to provide a significant scope for the real time applications. Each time before the reuse, the photocatalyst has been washed with distilled water and ethanol to remove the dye from its surface and then dried at 60 °C in an oven. Figure 13 illustrates the reusability profile of the catalyst on photodegradation. After recycling, there are no notable changes observed in the degradation, which evidently indicates that the photocatalyst prepared is reusable and impressively stable enough.
Fig. 13

The recycling ability of Ti-B-500 photocatalyst on MB degradation

5 Conclusion

In this investigation, the authors have reported synthesis and characterization of pure anatase titania nanoparticles using different surfactant templating. Precipitates are formed through controlled hydrolysis method. Structural analysis of XRD patterns has confirmed the formation of pure anatase phase. HRTEM micrographs of Ti-B-500 nanoparticles have manifested the presence of wormlike mesopores structure. Presence of O–S mixed environment in the Ti-B-500 lattice is observed to be evident from the XPS study. The presence of sulphur may be reducing the band gap energy and contributing to the photon absorption at visible wavelength. Overall, the Ti-B-500 nanoparticles exhibit an O–S mixed environment, high surface area, porosity, smaller particle size, and lower band gap energy. Complex impedance spectra analysis showed effective charge separation in Ti-B-500 catalyst. Methylene blue photodegradation has been carried out under solar light irradiation and Ti-B-500 exhibited high photocatalytic activity with 93% of degradation. The photocatalysts worked best without any alteration of pH. Optimum dosage of catalysts is in the range 3.0–4.0 g/L. The photocatalyst exhibited the best photocatalytic activity and high stability after five cycles of experiment. This research can encourage further more investigations on various materials for applications in the fields of photocatalysis of organic pollutants from wastewater.



The authors are thankful to RRCAT Indore for providing XPS facility. Amar Kundu acknowledges MHRD through NIT Rourkela for his research fellowship.

Compliance with ethical standards

Conflict of interest

On behalf of all authors, the corresponding author states that there is no conflict of interest.


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© Springer Nature Switzerland AG 2019

Authors and Affiliations

  1. 1.Department of ChemistryNational Institute of TechnologyRourkelaIndia

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