The defects caused by doping are important for understanding the increased photocatalytic activities of TiO2:N in organic reactions and in the evaluation of OH radical production after doping. TiO2:N was therefore synthesized using a modified polymeric method and N doping was performed by calcination with urea. The resulting powders were characterized using field emission scanning electron microscopy, X-ray diffraction, diffuse reflectance spectroscopy, Raman spectroscopy, Fourier transformation infrared spectroscopy, and photoluminescence emission spectroscopy (PL). N doping did not alter the morphology of the nanoparticles, and the anatase phase predominated, with the retention of the rutile phase. The band gap values, superficial areas, and crystallite sizes of the powders decreased after doping. The PL results showed an additional energy level in the TiO2:N band gap structure as a result of TiO2 lattice defects caused by doping. At low N contents, the powders showed continuous emissions from the blue region to the yellow region and a high N content shifted the PL emissions to the red region. These results suggest that the use of these powders could increase the efficiencies of solar cells and water-splitting processes. The photocatalytic activity of the powders under UVC illumination was confirmed for different organic dye molecules. The OH radical production did not change extensively after doping, as shown by experiments with terephthalic acid, and higher photocatalytic efficiencies in Rhodamine-B degradation under UVC illumination were achieved using the doped samples.

1. Introduction

Hydroxyl radicals produced by photon excitation with photocatalysts are widely used in the remediation of organic pollutants and similar processes. This heterogeneous catalytic process, also known as the advanced oxidative process, is based on the incident photon at the photocatalyst surface, generally TiO2, ZnO, CdS, or SrTiO3, producing charge separation if the photon energy is above the semiconductor band gap. Reductive and oxidant sites are then created to complete this process [1]. TiO2 is a good photocatalyst for these purposes and has been extensively studied [29].

TiO2 has a wide band gap (3.2 eV), which limits its photoactivity to the ultraviolet (UV) region. Doping extends the wavelength absorption of TiO2, and one of the best options for achieving this goal is replacing lattice O with anionic dopants such as N [2, 3, 6]. Doping induces energy levels creation within the band gap, which increases the electron-hole pair yield under irradiation with visible light, because the delocalized s/p states at the band gap edges improve the charge mobility. The increased charge mobility increases the photocatalytic activity of TiO2.

Defects caused by doping, such as O vacancies (VO), result in color centers and are closely related to the visible light activity of TiO2. Theoretical studies have shown that the visible light performance of doped TiO2 can be partly attributed to defects created during doping [10]. It is important to correlate the defects caused by doping with the increase in the photocatalytic activity. The aim of this study was to investigate the role of such defects using photoluminescence (PL) spectroscopy over a wide visible light wavelength range. It is also important to correlate the creation of defects by doping with the photocatalytic activity and OH radical production and identify the changes caused by N doping.

2. Methods

2.1. Synthesis of TiO2:N

In this study, we attempted to incorporate N atoms easily into TiO2, in higher amounts than those generally used [29]. Ti4+ resins were prepared by a polymeric precursor method, as described in our previous work [7], by dissolving titanium tetraisopropoxide (Aldrich) in an aqueous solution of citric acid (Merck) at 75°C in a molar ratio of 1 : 3. The titanium citrate obtained was polymerized by adding ethylene glycol (Merck) in a 1 : 1 molar ratio. The doped samples were designed with initial N contents: SAM 02 = 1 wt% of N (with respect to TiO2), SAM 03 = 3 wt% of N. SAM 01 is the original TiO2 sample.

2.2. Powder Characterization

The TiO2:N nanoparticles were characterized by X-ray diffraction (XRD) (Shimadzu XDR 6000), using Cu Kα radiation ( = 0.154 nm), in the range 10–80°, at a scanning rate of 2° min−1 in order to do the structural characterization of TiO2:N nanoparticles. The crystallite sizes of the N-doped TiO2 nanoparticles were determined using the Scherrer formula, from the broadening of at least three different peaks in the XRD pattern [11]; the surface areas (S.A.) were determined by N2 physisorption (ASAP 2000 adsorption analyzer), using the Brunauer-Emmett-Teller (BET) method, in a ASAP 2000 adsorption analyzer. The Raman spectra were collected (Horiba Jobin Yvon model HR550 with a CCD detector (−70°C)) using the 514 nm line of a 17 mW laser; 200 scans were used for each measurement. Fourier transform infrared (FTIR) spectra were also performed (Perkin Elmer FTIR spectrometer 1000 model) for all samples. The size and morphology of the samples were characterized by field emission scanning electron microscopy (FESEM) (FEI/Inspect model F50).

Diffuse reflectance UV-visible (UV-vis) spectra were obtained using a UV-vis-near infrared Cary 5G spectrophotometer. The substrate spectrum was taken as the baseline and was recorded prior to each measurement. UV-vis spectroscopy was performed in diffuse reflectance mode () and the spectra were corrected using the Kubelka-Munk model [7]. The band gap values () of the samples were determined using the Tauc equation [12]:where is the absorption coefficient (cm−1), is the photon energy (eV), and is a constant. The value depends on the nature of the electronic transition and is 1 for a direct and 0.5 for an indirect semiconductor with a crystalline structure. The equation is only used for monochromatic irradiation, an infinitely thick sample layer, low sample concentration, a uniform solute distribution, and absence of fluorescence. The Tauc equation can therefore be written as

PL studies of solid samples were performed using a fluorescence spectrometer (Perkin Elmer LS 55) with a krypton multiline laser with an excitation wavelength of 350 nm.

Rhodamine-B (Rhod-B) (C28H31ClN2O3) photodegradation experiments were performed under UVC and visible light irradiation; each sample (2 mg) was added to a beaker containing Rhod-B aqueous solution (20 mL) of concentration 2.5 mg L−1. The solution was stirred constantly with a magnetic stirrer and irradiated with six UVC lamps (TUV Philips, 15 W, maximum intensity at 254 nm). Visible light irradiation was performed separately, using six fluorescent lamps (Quality, 15 W, maximum intensity at 440 nm). The photocatalytic oxidation of Rhod-B was monitored using UV-vis measurements (Shimadzu-UV-1601 PC spectrophotometer) at various light-exposure times. The same Rhod-B photocatalytic experiments under UVC illumination were conducted for two other dyes, methyl orange (C14H14N3NaO3S) (MO) and methylene blue (C16H18N3SCl) (MB). Aqueous solutions (20 mL) at concentrations of 5.0 mg L−1 for MO and 2.5 mg L−1 for MB were used.

The photocatalytic activities of the samples were studied using terephthalic acid (TA) oxidation, as described by Raubach et al. [13]. In this reaction, the organic acid is selectively oxidized to 2-hydroxyterephthalic acid, a fluorescent species, by the action of free radicals in solution; therefore the reaction rate is proportional to the radical concentration in the medium. A TA solution (5 g L−1) was prepared by dissolving TA in water. The TiO2 samples (2 mg) were placed in beakers and immersed in TA solution (20 mL). The fluorescence spectra of 2-hydroxyterephthalic acid were obtained using a Perkin Elmer luminescence spectrometer LS50B [13]. The samples in TA solution were illuminated with UV and visible light. The fluorescence emission spectra (excitation at 315 nm) of the solutions were recorded every 15 min during illumination. A sample without any photocatalyst, that is, only TA solution, was also illuminated with UV and visible light.

3. Results and Discussion

Figure 1 presents the FESEM images of SAM 01 (a), SAM 02 (b), and SAM 03 (c), which indicate that the N doping process did not alter the particle morphology. This would be evident as agglomeration of the spherical nanoparticles, which have an average size of 10–15 nm in the undoped sample. In Figure 1(c), the nanoparticle crystals cannot be clearly identified, as is possible in Figure 1(a), demonstrating that the N doping process could promote a reduction in the nanoparticle size. This decrease in size directly modifies the superficial area, generating a greater interaction between the nanoparticles, thus promoting the smoother appearance of nanoparticles in the FESEM images of SAM 02 and SAM 03 than that of the undoped sample, SAM 01.

Figure 2(a) shows XRD data for nanoparticles with different N contents. The data show that anatase and rutile phases are present in all samples, even at the higher N content (SAM 03). However, as the N percentage increases, the anatase phase becomes predominant; that is, the presence of N causes the anatase retention effect associated with doping [7]. This result also confirms that the dopant has not altered the anatase and rutile structures; TiN was not identified in either of the samples.

Figure 2(b) shows that the anatase (101) diffraction peaks shift to higher angles for SAM 03. This change could be related to N substitution of O sites during doping, although the N atomic radius is different from the O atomic radius. When substitution occurs, the doped nanoparticle (TiO2:N) surfaces become more positive because of the electronic distribution of N ([He]2s22p3), and this can cause structural changes in the lattices of doped nanoparticles.

Figure 2(c) shows the Raman shifts of the synthesized samples, which are in agreement with the spectra reported for titanium oxide predominantly in the anatase phase [7]. The anatase phase is confirmed by the major Raman bands at 160, 415, 537, and 659 cm−1. The presence of the rutile phase, especially in SAM 01, is confirmed by Raman bands at 215 and 466 cm−1. As the N content in doped samples increases, the nanoparticles present a yellow color that could interfere with the Raman band intensity, and the intensity of the anatase phase decreases, as presented in the insert of Figure 2(c). Additionally, the retention of the rutile phase with increasing N content is confirmed by the Raman band at 466 cm−1.

The TiO2:N nanoparticle crystallite sizes were determined, using the Scherrer formula, from the broadening of at least three different peaks in the XRD patterns [11]; the results are listed in Table 1. The crystallite size decreases with increasing N content, because anatase retention reduces the boundary mobility [7]. The trend for the S.A. behavior changes is similar to that for crystallite size; that is, as the N percentage increases, the S.A. decreases. Sample SAM 03 presents a more pronounced decrease in the S.A. compared to the pristine sample (SAM 01), while sample SAM 2 presents an increase in the S.A. These results are in accordance with those in the literature [29], which report that doped samples with low N contents have higher surface areas. The changes in the surface areas indicate that doping changed not only the nanoparticle surfaces but also their sizes.

Figure 3 presents the FTIR spectra of samples synthesized and defines functional group modifications on the nanoparticles surfaces. The synthetized samples show similar spectra with analogous absorption peaks. The absorption peak at 1620–1630 cm−1 is associated with the vibration of adsorbed water molecules bonds and/or surface hydroxyl groups. The absorption peak intensity increases slightly with increasing N content. It is possible to observe another absorption peak at 3410 cm−1, which is also linked to hydroxyl group vibrations. Its intensity is also elevated for the sample with a higher N dopant content (SAM 03) compared to that of the pristine TiO2 (SAM 01). The absorption peak at 485 cm−1 is typically attributed to Ti-O and Ti-O-Ti bond vibrations (Figure 3). The absorption peak at 900 cm−1 is linked to peroxide (O-O) bond vibrations and clearly increases in intensity as the N content in samples increases. The presence of N-H bond vibrations at 1400 cm−1 could be avoided due to N atoms located near a Ti atom in interstitially doped samples or replacing O atoms in substitutionally doped samples [14].

Figure 4 shows the diffuse reflectance UV-vis spectra of the samples. The absorption behavior clearly changes after doping and with increasing N content, indicating that N doping increases interference in the absorption profiles. The absorption behaviors between 400 and 600 nm in the spectra indicate interenergetic bands between the conduction and valence bands of TiO2 after N doping. Band gap values are easily obtained from diffuse reflectance spectroscopy measurements using the Tauc function [12] (Figure 4(b)); the values are presented in Table 1. The band gap value is obtained by plotting the Tauc function as a function of the energy of the exciting light and extrapolating the linear part of the resulting curve to the desired value. Doping changes the band gap value linearly (Table 1). Pristine TiO2 has the highest value (2.93 eV) and SAM 03 has the lowest value (2.85 eV). This energy difference (0.08 V) is in accordance with that reported in the literature [2, 3, 6, 9]. It is important to remember that any decrease in the band gap can improve the nanoparticle properties such as visible light photocatalytic activity [3, 7], because the band gap is related to the excitation energy of electron transfer between the conduction and valence bands of the semiconductor. Electronic transitions begin at 408 cm−1 for the pristine sample, 409 cm−1 for SAM 02, and 417 cm−1 for SAM 03. The higher-wavelength absorbance of the doped samples is a good indication of effective doping.

The electronic structure and defects induced by impurities on the oxide surface were investigated using PL spectroscopy; the spectra of SAM 01, SAM 02, and SAM 03 are shown in Figure 5. The emission spectra provide useful information, because electron-hole pairs emit different energies when they decay, including decay related to interlevels, not only band gap decay. When the TiO2 samples were excited at wavelengths lower than 320 nm, the interband recombination peak appeared at around 360 nm in emission spectrum; another peak appeared at 550 nm, which is ascribed to indirect recombination via VO. The appearance of other peaks related to the electronic structure and indirect recombination of bulk defects is also possible [15]. Praveen et al. [16] reported similar results for anatase TiO2 nanoparticles excited at 345 nm, with an emission peak at 587 nm, which were attributed to Ti4+ ions near VO (intragap surface state). A peak at 431 nm (400–450 nm) was observed from a band edge-free excitation, and this surface emission was attributed to an indirect transition, to , and was correlated with recombination in shallow trapped surface states.

Figure 5 shows the PL emission spectra between 350 and 850 nm of the samples excited at 350 nm. A major peak is observed at around 500 nm for SAM 01 and SAM 02, and another principal peak is observed at around 620 nm for the other sample. The first peak, at 500 nm, is associated with indirect transitions in the pristine TiO2 sample. As N is added to the TiO2 crystal, other energy levels are created between the conduction and valence bands, similar to the PL emissions of calcium sulfide behavior synthesized using a microwave-assisted solvothermal method, which shows a blue-shifted emission [16]. The second emission fluorescence peak with a blue emission at around 620 nm is only observed for the doped samples (SAM 02 and SAM 03) and is associated indirectly with an additional energy level in the band gap; this enables other indirect electronic transitions via radiative recombination between donors charges, associated with VO, and acceptors, associated with defects [15, 17]. Nonstoichiometric concentrations of VO and impurity-related defects in TiO2:N help in explaining the results. As impurity atoms are introduced into the TiO2 lattice, the potential energy changes; therefore, the energy level of VO changes, resulting in shifts of the emission peaks of the TiO2:N samples [17].

The behavior of SAM 02 is clearly different from those of the other samples, and a major peak at around 500 nm and another peak at around 620 nm (fluorescence quenching) are observed, indicating transitional behavior between those of the pristine and higher-doped samples. The SAM 02 behavior is attributed to a mixture of VO and N impurities. However, N impurities occupy the interstitial sites, forming a coulombic shield that transfers the radiation to nearby atoms [17]. This results in a continuous emission from the blue region to the yellow region (450–650 nm) as a result of radiative recombination between the donors associated with VO and acceptors related to the original defects.

After doping, except in the case of SAM 02, the emission spectra of the samples were displaced to the red region; for the pristine sample, emission was observed in the green region of the UV-vis spectrum. For SAM 02 and SAM 03, it is possible to obtain emission across practically the entire visible spectrum, from the blue to green regions, but higher emission was only observed for SAM 02.

The photocatalytic activities of the TiO2 nanoparticles under UVC (maximum at 257 nm) and visible (maximum at 550 nm) light (Figures 6(a) and 8(a), resp.) were investigated using Rhod-B degradation. Photocatalytic efficiency plots of the TiO2 nanoparticles with different light sources were used to determine the order of the photodegradation reaction. The reaction should be first order with respect to Rhod-B, and the kinetic law can be described asand [AS] is the photocatalytic concentration (number of actives sites), which is constant for a given sample; therefore where ; integration gives

In accordance with (5), if is plotted as a function of , a straight line of slope is obtained. A comparative study of the kinetic parameters of Rhod-B photodegradation reactions with the different nanoparticle samples was performed.

The rate constant, (s−1), obtained from the curves of Rhod-B photodegradation under UVC and visible light are shown in Figures 6(b) and 8(b), where a column represents the values. It is important to note that the values for Rhod-B degradation under visible light are lower than those under UVC light, by an order of 10−1. Under UVC light, the SAM 02 rate constant is lower than those of SAM 01 and SAM 03; this suggests that the higher N content significantly increases the UV photocatalytic activity and that N doping promotes Rhod-B degradation under these conditions. The surface areas are also correlated with the rate constants under UVC illumination. The band gap values are similar to the photocatalytic profiles, but because of the higher energy illuminating the semiconductor surface in the case of UVC illumination, the band gap value is more important for visible light photocatalytic activity.

To confirm the photocatalytic activity of synthesized samples with different dyes, photocatalytic degradation experiments were conducted for MO and MB, as presented in Figures 7(a) and 7(b), respectively. Under UVC illumination, both dyes underwent photolysis for 2 h, showing increased degradation with the use of these photocatalysts. SAM 01 shows higher photocatalytic activity for dye degradation under UVC illumination, decreasing the initial concentrations () of MO and MB by 52% and 87%, respectively, over 2 h. The doped samples show lower photocatalytic activity for dye degradation under UVC illumination compared to the pristine sample but nevertheless demonstrate good photocatalytic activity with both dyes. SAM 02 presents concentration decreases of 23% for MO and 62% for MB, while SAM 03 presents decreases of 30% for MO and 55% for MB. These results show that it is possible to confirm that the photocatalytic activity efficiencies are influenced, principally by the photocatalyst material/composition through doping, and also by the functional groups of molecules. Some molecules could decompose and generate subproducts that interfere with the photocatalytic activity, generally decreasing the photocatalytic efficiency.

From Figures 6 and 7, it is possible to verify that the photocatalysis mechanism varies for different dyes. However, it is generally agreed that the primary reactions responsible for the photocatalytic effect are the interfacial redox reactions of electrons and holes that are generated when the semiconductor catalyst is exposed to light of sufficient energy. Holes and electrons produced in this illumination process are consequently responsible for the generation of redox species that will be involved in all degradation mechanisms. Aside from the influence of the dye molecules on the photocatalyst mechanism, other factors such as catalyst concentration, light intensity, reaction time, and the pH of aqueous solution could also influence this process.

The pH of the aqueous solution is an important factor in TiO2 synthesis, as it significantly affects the size and form of aggregates and could affect the charge on the particles and positions of the conductance and valence bands. In the photocatalytic process, the pH changes the manner of interaction between organic pollutants and catalysts and, in particular, the extent of adsorption on the photocatalyst surface. An oxide surface is uncharged at the pH defined as the zero point charge (), which for TiO2 is governed by the production method.

In this context, the isoelectric point (iep) is defined as the condition when positive and negative charges are present on the particle surface in equal amounts; consequently, there is only H+/OH ion adsorption at the particle surface. In this case, the iep has the same value as . If the pH of the aqueous solution is higher than the iep, there is a resultant negative charge at the oxide surface, and the adsorption of cations is preferred as cationic electron oxidation donors and acceptors. Conversely, if the pH is lower than the iep, the oxide surface charge is positive; the adsorption of anions is favored; consequently, more protons than hydroxide groups are generated by an acidic solution. In summary, the charge on the titanium dioxide surface is negative or positive, according to the equilibrium equations given below [18]:

The iep of the synthesized samples are similar to those of TiO2:N obtained in previous work [7], and it is possible that SAM 01, SAM 02, and SAM 03 present an oxide surface that is negatively charged in a solution with neutral pH, as the pH of the three dye solutions is near to the neutral condition (MO: 8.0, MB: 7.0, and Rhod-B: 7.5).

The ionic species of the dyes are also pH dependent. The pka is the pH at which half of the functional groups are neutralized and half are ionic. At one pH unit above or below the pka, the functional groups are predominantly in the ionic and neutral form, respectively. The pH of MO (8.0), MB (7.0), and Rhod-B (7.5) solutions are above the pka of MO (3.39), MB (3.8), and Rhod-B (3.1); consequently, the three dye molecules are present as ionic species in solution.

The variation in the absorption of MO shown in Figure 7(a) is probably due to the insufficient time allowed for equilibration, so that the maximum adsorption was not reached before beginning the photocatalytic process between MO and the TiO2:N nanoparticle surface. Because of the opposite charges on (MO) and the photocatalyst surface, adsorption of MO over the TiO2:N nanoparticle surface occurred and is fundamental for the photocatalysis process. However, for MO photolysis (Figure 7(a)), it is possible that adsorption time is not the only problem. It is probable that, during the decolorization process, some subproducts form, which have a fast half-life (~30 min) and absorb at the same wavelength as MO. Dai et al. [19] reported various subproducts in MO photocatalytic degradation with TiO2 by identifying them by chromatography (HPLC-MS). One principal subproduct that highly influences the absorption behavior of MO forms from homolytic breaking of a nitrogen-carbon bond in the MO structure, resulting in the substitution of a methyl group by a hydrogen atom.

For methylene blue (MB) shown in Figure 7(b), the absorption behavior is similar to that of Rhod-B under UV illumination; that is, there is no great variation in absorption behavior. This is because, in the photocatalytic process using TiO2, degradation is initiated by the opening of the central aromatic ring, resulting in a chromophore molecule that does not interfere with MB absorption [20]. Houas et al. [20] reported that the fastest photocatalytic degradation of MB with TiO2 occurred at an elevated pH (9.0); under such conditions, degradation was complete in 40 min. In comparison, complete degradation at a neutral pH (6.7) required 60 min under UV illumination.

Under visible light, the Rhod-B degradation rate constant profiles have a sinusoidal component (Figures 8(a) and 8(b)). This is probably because N doping increases the TiO2 nanoparticle photocatalytic activity [2, 3]. The effect on the activity is clearer for lower N contents (lower than 2% molar), and it also depends on the synthetic method. However, the photocatalytic activity of SAM 02, which has a low N content, is lower than that of SAM 01. Furthermore, SAM 03, which has a higher N content, did not improve the Rhod-B degradation efficiency under visible light. The effect of N doping at this N content does not promote photocatalytic degradation under visible light; it does so only under UVC illumination. The N doping diminished the band gap value, probably causing an increase in the recombination rate of photocharge.

The Rhod-B absorption behavior under visible illumination is similar to that previously reported [7, 21]. The variation in absorption may occur due to one or more of the suggestions previously discussed for MO and MB, that is, insufficient equilibration time to allow maximum adsorption, solution pH, or even interference by subproducts produced during the photocatalytic process with TiO2:N [21]. Li et al. [22] identified the principal products of photocatalytic degradation with TiO2 by HPLC-MS, confirming an interesting difference between UVC and visible illumination: deethylation is reduced under visible light compared to UV irradiation, and consequently the destruction of the chromophore structure predominates.

Several authors have reported better visible light photocatalytic activity for TiO2:N particles with lower N contents [27]. However, few authors have investigated the mechanism involved in Rhod-B degradation, that is, the dye-sensitizing mechanism [7]. The degradation mechanism of colored materials involves electron promotion from the dye to the semiconductor bands, inducing an increase in the photocatalytic degradation. However, under visible light, electron and hole photoexcitation in the semiconductor energetic bands can also occur, depending on the band gap value; the main radical responsible for degradation is . To understand the photocatalytic results better, the amount of OH radicals was determined.

Photocatalytic studies were performed to analyze radical attack to dye for degradation occurs, mainly by OH radicals, in TA solution under UV and visible light. The fluorescence emission spectra (excitation at 315 nm) of the solutions were measured during UV illumination (Figure 9(a)) and visible illumination (Figure 9(b)). As shown in Figures 5(a) and 5(b), a gradual increase in the fluorescence intensity at 425 nm was observed under both illumination conditions. The behavior was similar for all samples. The fluorescence intensity is related to the fluorescent products formed during photocatalysis, especially to those of the reaction between OH radicals and TA [22]. The OH radical formation efficiency can be estimated by comparing the absolute quantum yields for each sample at each measurement time, as shown in Figure 9(a) for UV illumination and Figure 9(b) for visible illumination. The slopes of the sample reaction plots were obtained as described previously for photocatalytic degradation and were correlated with OH radical formation.

In our model, the ideal catalyst semiconductor (TiO2 or TiO2:N) needs to have some specific features. The most important events occur before the excitation light source reaches the system; the nanoparticle catalysts must be able to generate charges, as shown in (8), because the TiO2 and TiO2:N nanoparticles have structural defects (order-disorder) ascribed to different types of vacancies, that is, [], [], or [] clusters [19].

Theoretical studies have shown that symmetry breaking (effect of order-disorder) in the structures of various semiconductors is a necessary condition for the presence of intermediary energy levels within the forbidden band gap [23, 24]. These structural changes are related to short- and medium-range charge polarization, which can be a manifestation of quantum confinement (independent of the particle size). The key point of quantum confinement is the presence of discrete energy levels within the band gap, which is not possible for periodic crystals at long, medium, and short ranges.

In this work, it was considered that the TiO2 lattice contained clusters ( is , , or ) as extrinsic defects, and these are linked to order-disorder effects in the electronic structure. These defects create additional energy levels above the conduction band and below the valence band (Figures 4 and 5), thus decreasing the band gap. The effects can be considered in terms of the following reactions:

As expected, for UV illumination, OH radical generation is superior to that in visible illumination and a linear behavior for OH production is observed for all samples, indicating that nitrogen doping process changed radicals generation (Figure 9), though the role of N content is not totally clear yet. Even in higher contents (SAM 03), the OH radicals generation did not significantly modify with N amount in TiO2:N. However, the photocatalytic activity did not present a clearly relation with OH radical generation proposed by this method. On the other hand, other radicals may be involved in Rhod-B degradation, as O2H radical and even for directly oxidation. Another cause for the increase in photocatalytic activity under UVC illumination of doped samples and not under visible is due to recombination charges induced for decrease in band gap value. In this case, there is not sufficient time to produce OH radical under visible illumination in doped samples as Figure 8 shows. Further studies are in progress to better describe the entire mechanism degradation of organic compound after doping process.

4. Conclusion

The results presented here conclude that the doping process create defects, especially oxygen vacancies (VO) in TiO2 lattice, which did not influence OH radical production when photocatalyst was illuminated, neither by UV or by visible radiation. In this scenario, probably does not occur OH radicals production alteration; however, the photocatalyst activity under visible illumination could be associated with the defects, confirmed by photoluminescence results. Another important effect presented in photocatalytic activity for doped samples is probably a charge recombination, induced by reduced band gap values. Then, the efficiency of Rhod-B degradation process is reduced under visible illumination. The TiO2:N nanoparticles present photocatalytic activity under UVC illumination for other organic molecules such as MO and MB dyes. The powders synthetized present useful paper in solar cells and water splitting processes as the PL emission continuous could increase the efficiency of both systems as for photocatalytic processes.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


The authors appreciate the financial support from CNPq (151177/2013-9), CAPES, FINEP, and EMBRAPA Instrumentação.