Open Access

Enhancement of Photo-Oxidation Activities Depending on Structural Distortion of Fe-Doped TiO2 Nanoparticles

Nanoscale Research Letters201611:41

Received: 4 November 2015

Accepted: 20 January 2016

Published: 29 January 2016


To design a high-performance photocatalytic system with TiO2, it is necessary to reduce the bandgap and enhance the absorption efficiency. The reduction of the bandgap to the visible range was investigated with reference to the surface distortion of anatase TiO2 nanoparticles induced by varying Fe doping concentrations. Fe-doped TiO2 nanoparticles (Fe@TiO2) were synthesized by a hydrothermal method and analyzed by various surface analysis techniques such as transmission electron microscopy, Raman spectroscopy, X-ray diffraction, scanning transmission X-ray microscopy, and high-resolution photoemission spectroscopy. We observed that Fe doping over 5 wt.% gave rise to a distorted structure, i.e., Fe2Ti3O9, indicating numerous Ti3+ and oxygen-vacancy sites. The Ti3+ sites act as electron trap sites to deliver the electron to O2 as well as introduce the dopant level inside the bandgap, resulting in a significant increase in the photocatalytic oxidation reaction of thiol (–SH) of 2-aminothiophenol to sulfonic acid (–SO3H) under ultraviolet and visible light illumination.


Distorted TiO2 2-Aminothiophenol Photo-oxidation Bandgap narrowing


Titanium oxide (TiO2) is one of the most promising materials for various applications such as solar cells, gas sensors, photocatalysis, and corrosion protection due to its chemical stability, nontoxicity, and low cost [1, 2]. Furthermore, its high oxidation properties have been applied to the degradation of organic pollutants [35]. However, the problems caused by the large bandgap (3.0–3.2 eV) result in poor efficiency and limited light absorption in the visible region, which makes a practical application difficult [6, 7]. To solve these chronic problems and enhance catalytic properties, narrowing the bandgap is necessary.

One strategy is co-deposition of a noble metal such as Pt, Ag, Au, or Pd onto the TiO2 surface. This strategy has little effect on narrowing the bandgap, although it does improve the separation of holes and electrons significantly [813]. However, it is not cost effective and makes almost no contribution to light absorption in the visible range. Another strategy is the introduction of foreign atoms as dopants inside the TiO2 substrate [1416]. This can narrow the TiO2 bandgap and change the electronic band structure, which can increase the photocatalytic performance significantly. If the effect is similar or the same as that of noble metals, transition metals such as Fe, Co, and Ni are the most feasible and cost-effective dopant candidates. Such transition metals possess various oxidation states and thus contribute to bandgap control.

We introduced Fe ions into the TiO2 substrate using a hydrothermal method and systematically investigated the photocatalytic activities of Fe-doped TiO2 nanoparticle (Fe@TiO2) at various Fe doping concentrations. Structural and electronic changes were characterized by surface analysis techniques. The photocatalytic activities were characterized by the oxidation of 2-aminothiophenol (2-ATP) with different light sources in the ultraviolet (365 nm) and visible (540 nm) regions. We found that 5 wt.% of Fe dopants in TiO2 nanoparticles form a new distorted phase in which catalytic performance is significantly enhanced by bandgap narrowing.



Titanium isopropoxide (TTIP, 99.9 %), tetramethyl ammonium hydroxide solution (TMAOH, 25 wt.% in H2O), and Fe(NO3)3 9H2O (99.9 %) were purchased from Sigma-Aldrich and used as received.

Preparation of Fe-Doped TiO2 Nanoparticles

Preparation of Dispersed Fe@TiO2 Nanoparticle Solution

TMAOH (1.2 g) was introduced into a round-bottomed flask (100 ml) containing double-distilled water (22.25 g). The diluted TMAOH solution was stirred for 10 min. TTIP (3.52 g, 12.4 mmol) was separately diluted with isopropanol (3.5 g) and stirred for 10 min. The diluted TTIP was added dropwise into the TMAOH solution with vigorous stirring at room temperature. Initially, white TiO2 precipitants appeared. Then, a desired amount of Fe(NO3)3 9H2O (99.9 %) as a dopant was introduced into the synthetic gel solution. The round-bottomed flask containing the synthetic gel solution was placed in an oil bath. The temperature of the oil bath was maintained at 80 °C under continuous stirring. After approximately 10 min, the synthetic gel solution became a transparent solution. The synthetic gel was transferred to a Teflon-lined autoclave. The autoclave was placed in a convection oven preheated to 220 °C for 7 h. The produced Fe@TiO2 nanoparticles were collected by centrifugation at 10,000 rpm and washed with copious amounts of DDW to remove unreacted chemicals. Fe@TiO2 nanoparticles are dispersed into aqueous solution with concentration 0.05 g/mL. The dispersed Fe@TiO2 nanoparticle solution turned deep yellow with increasing Fe dopant concentration (see Additional file 1: Figure S1).

Preparation of the Fe@TiO2 Dispersed Nanoparticle Layers

Silicon wafers (1 cm × 1 cm) were washed with absolute ethanol, sonicated, and dried with an N2 stream followed by oxygen plasma treatment for 3 min. The dispersed Fe@TiO2 nanoparticle solution was then spin coated onto the silicon wafers at 2000 rpm. Subsequently, the spin-coated layers were annealed at 600 °C for 12 h at a heating rate of 5 °C/min in ambient atmosphere.


The X-ray diffractions (XRDs) of the Fe@TiO2 nanoparticles were obtained using a Rigaku D/Max-A diffraction meter by Ni-filtered Cu-Kα radiation (40 kV, 300 mA). The scans were obtained by 4°/min with 0.01° step size. Raman spectra were obtained using a spectrometer (Horiba, LabRAM ARAMIS) with a 514.5-nm Ar ion CW laser. The morphologies of the samples were characterized by performing field-emission scanning electron microscopy (FE-SEM, FEI Inspect F50) at an acceleration voltage of 10 kV and field-emission transmission electron microscopy (FE-TEM, FEI Tecnai G2 F30 S-Twin) with energy dispersive X-ray spectroscopy (EDX) at an acceleration voltage of 300 kV. Scanning transmission X-ray microscopy (STXM) was performed at the 10A beamline at the Pohang Accelerator Laboratory (PAL). A Fresnel zone plate with an outermost zone width of 25 nm was used to focus the X-rays onto the Fe@TiO2 nanoparticles on the TEM grids. The transmitted intensity was measured with a scintillation-photomultiplier tube. Image stacks were acquired at 695–745, 450–480, and 520–570 eV using X-ray absorption spectroscopy (XAS) to extract the Fe L-edge, Ti L-edge, and O K-edge spectra, respectively. High-resolution photoemission spectroscopy (HRPES) experiments were performed at the PAL 8A1 beamline equipped with an electron analyzer (Physical Electronics, PHI-3057). The Fe 2p, Ti 2p, O 1s, and S 2p core level spectra were obtained using photon energies of 770, 510, 590, and 230 eV, respectively, to enhance the surface sensitivity. The binding energies of the core level spectra were determined with respect to the binding energy (E B = 84.0 eV) of the clean Au 4f core level for the same photon energy.

Photocatalytic Oxidation Reactions

2-Aminothiophenol (C6H4SHNH2, Sigma-Aldrich, 99 % purity) was purified by turbo pumping prior to dosing onto the Fe@TiO2 samples. A direct dozer controlled by a variable leak valve was used to dose the molecules with the same amount of oxygen molecules onto the Fe@TiO2 nanoparticles. UV-visible light (λ = 365 nm, 550 nm) exposure was maintained at 8 W through the vacuum chamber quartz window. Chamber pressure was maintained at 1 × 10−6 Torr during dosing, and the number of exposed molecules was defined by the dosing time in seconds: 1 L (Langmuir) corresponds to 1 s dosing at 1 × 10−6 Torr.

Results and Discussion

We first acquired TEM (Fig. 1) and SEM (Additional file 1: Figure S2) images varying the weight percent of the Fe dopants. SEM images were obtained from the Fe@TiO2 on Si substrate, and TEM images were obtained from the powder Fe@TiO2 by using a similar method. According to the morphology of both images, they show the same structural feature. When 1 wt.% was doped inside TiO2, very fine (70 nm) and homogeneous circular Fe@TiO2 particles are evident. These particles are much smaller than bare TiO2 particles (~200 nm). It is expected that the Fe ions act as nucleation sites and crystallize to particles as a fine structure. When the Fe dopant concentration was increased, particles with fine needle-like structure and big arrow structure are evident.
Fig. 1

TEM images. a 1, b 3, and c 5 wt.%, and corresponding high-resolution images (a′), (b′), and (c′). White arrows indicate the location of inset diffraction patterns

According to the fast Fourier transform (FFT) pattern in the upper inset of the high-resolution TEM images, the big arrow structures in each image correspond to the highly ordered TiO2 structure in which particle grains are overlaid with other crystalline directions and indicate different FFT patterns. The expected pattern overlaps are indicated in the lower inset of Fig. 1. These big arrow structures were regarded as pure or low concentration Fe@TiO2 particles. When the Fe concentration increases to 3 and 5 wt.%, small needle structures are evident on both SEM and TEM images. Such structures are obtained as Fe2O3 complex by exclusion of Fe ions from the arrows structures. According to Additional file 1: Figure S3, EDX spectra show the portion of Fe atom in TiO2 substrates. At 5 wt.%, large arrow structures contain almost no Fe atom which also support the exclusion of Fe atom from the big arrow structures. Thus, these small needles (120 nm × 40 nm) are composed by bundling of smaller units, such as Fe2O3 and TiO2 structures. Those structures are dominant in 5 wt.% Fe@TiO2. XRD and Raman analyses (Fig. 2) elucidate the structural features with variation of concentration.
Fig. 2

XRD and corresponding Raman spectra show that the crystal structures and chemical states vary with the amount of Fe dopant. a, d 1 wt.% Fe@TiO2. b, e 3 wt.% Fe@TiO2. c, f 5 wt.% Fe@TiO2

According to the XRD and Raman spectra shown in Fig. 2, anatase TiO2 structure is observed not only from 2θ = 25.27° and 48.05° with XRD (JCPDS#84-1286), which are associated with (101) and (200), but also from 144 (E g ), 196 (E g ), 392 (B 1g ), 520(A 1g ), and 638 (E g ) on the Raman spectra [17]. Those clearly identify the structure of anatase TiO2 with no polymorph features. According to the XAS spectra from STXM (Fig. 3), the ratio between two e g peaks of the Ti L-edge shows higher absorption of d z 2 (459.1 eV) compared to d x 2− y 2 (460.0 eV), which is a typical XAS spectrum of the anatase TiO2 phase.
Fig. 3

XAS spectra of a Fe L-edge, b Ti L-edge, and c O K-edge of 1 wt.% Fe@TiO2 (black line), 3 wt.% Fe@TiO2 (red line), and 5 wt.% Fe@TiO2 (blue line). Insets are STXM images of each spectrum

At 3 wt.% of Fe ions, the hematite-Fe2O3 structure appeared in the Raman spectra. When only a few layers of Fe2O3 were coated on the TiO2 surface, no XRD peak features were evident; however, coating with a small number of layers of Fe2O3 can cause lattice distortion. Additional file 1: Figure S4 shows the variation of the XRD peak position with the associated lattice constant of the (101) facet and the relative Raman intensity of E g (410)/E g (144) to elucidate the doping effects on structures. At 1 and 2 wt.% of Fe dopants, there are no Raman features with respect to Fe2O3, changing the lattice constant on XRD. This change occurs with the successful doping of Fe on the Ti substitutional sites. Such doping triggers the formation of oxygen vacancies to compensate the regional oxidation balance, which causes lattice contraction. At 3 wt.% of Fe dopants, the Raman spectrum of the hematite phase initially appears at 225, 245, 298, 409, and 611, which is associated with A 1g  + 4E g [18]. Furthermore, the lattice constant of the (101) facet expands too close to the original phase. This means that the precipitation can be attributed to the phase separation between Fe2O3 and TiO2. At a higher doping concentration (5 wt.%), very small features of the anatase phase are shown by XRD. On the other hand, new structural features are indicated at 21.08° and 26.35°. These new structural features are contributions from the formation of a TiO2 composite with Fe2O3. According to previous investigations, the composite of (Cr, Fe)2Ti n − 2O2n − 1 indicates a monoclinic system, and their intergrowth can be attributed to the d-spacing changes from 18.9° to 22° as 2θ. In particular, in the case of n = 5, d-spacing near 25° and 27° is also evident. Thus, the spectrum is characterized as Fe2Ti3O9 (Fe2O3 3TiO2) [1921].

The differences among the electronic structures of the samples were characterized by XAS measurements using STXM (Fig. 3). O K-edge XAS spectra has four peaks at 529.9, 532.3, 537.9, and 543.7 eV. Two peaks at 529.9 and 532.3 eV are attributed to the transition from O 1s orbital to the O 2p orbital hybridized with Ti 3d t 2g and e g states, respectively. Two additional peaks at 537.9 and 543.7 eV are attributed to the delocalized state of the Ti 4sp and O 2p bands. At 3 to 5 wt.% dopant concentrations, the peak at 532.3 eV is reduced. This may be because of the presence of surface-oxygen-vacancy sites that cause reduction in Ti 3d–O 2p hybridization in e g states and finally shows the reduction of intensity of 532.3 eV [22, 23]. This is also evident from the Ti L-edge spectra as well as the HRPES data.

Ti L 3,2-edge XAS spectra show the traditional anatase TiO2 structure, which arises from the transitions of Ti 2p electrons to unoccupied 3d electronic states in a distorted octahedral crystal field. Two t 2g , such as 457.4 and 462.7 eV, result from the transition of 2p 3/2 and 2p 1/2, respectively. Two e g bands, i.e., 459–460 and 464.8 eV, can be attributed to the transition from the 2p 1/2. When Fe ions are doped inside the TiO2, the intensity ratio of peaks t 2g (457.4 eV) to e g (459~460 eV) is gradually lowered compared with that of 1 wt.% Fe@TiO2 nanoparticles, which indicates a weak crystal field or an increment of the number of under-coordinated Ti atoms [24, 25]. Furthermore, the ratio of peaks d z 2 to d x 2− y 2 indicates the distortion of the octahedral crystal field, which is noticeable in the discrepancy between the rutile and anatase structures. These ratios also decrease as the percentage of Fe dopants increases. Therefore, the anatase structure transforms to less crystalline anatase by the formation of Fe2O3 3TiO2. This transformation also gives rise to the surface defect structure, indicating that the small doublet at 456.0 and 456.6 eV is in the Ti3+ state [26].

L 3 and L 2-edges located at approximately 710 and 721 eV have been assigned as transitions from Fe 2p to an unoccupied 3d orbital. The distinct features at the L 3-edge indicate typical t 2g (706.0 eV) and e g (707.4 eV) splitting because of the presence of only the Fe3+ valence form. However, there is no noticeable oxygen state with respect to Fe2O3 [2729].

The core level spectra (Fe 2p, Ti 2p, and O 1s) of the Fe@TiO2 nanoparticles were obtained with HRPES (Fig. 4) to determine the changes in electronic properties. According to the core level spectra of O 1s, the nanoparticles are composed of two different chemical environments assigned as TiO2 (530.9 eV) and Fe2O3 (533.0 eV), which correspond to the previous XRD, Raman, and XAS spectra. In Ti 2p core level spectra, there is a Ti3+ peak at 458.1 eV as well as the typical Ti4+ spectra of TiO2 at 459.4 eV. The ratio of Ti3+ peak to Ti4+ increases with the doping concentration, which is attributed to the oxygen-vacancy sites. When vacancies are generated, the oxidation state of the site is compensated by the nearest neighbor Ti through formation of Ti3+. This is also clearly evident from the pre-edge of the Ti L-edge and e g intensity of the O K-edge in the XAS spectra. Fe shows Fe3+ characteristics at 710.7 eV, which is also comparable with the previous results.
Fig. 4

HRPES results for Fe 2p, Ti 2p, and O 1s core level spectra of Fe@TiO2 nanoparticles with various doping levels. a, d, g Core level spectra from 1 wt.% Fe@TiO2. b, e, h Those from 3 wt.% Fe@TiO2. c, f, i Those from 5 wt.% Fe@TiO2. HRPES results corresponding to the S 2p core level spectrum obtained after photocatalytic oxidation of 2-aminothiophenol on j 1, k 3, and l 5 wt.% Fe@TiO2 nanoparticles

Next, we determined the photocatalytic activities of each Fe@TiO2 nanoparticle by the oxidation of 2-ATP molecules. The surface-sensitive S 2p core level spectra were recorded using HRPES after 360 L of 2-ATP exposure in the presence of the same amount of oxygen under 365-nm UV light illumination. There are three distinct 2p 3/2 peaks at 161.5, 162.9, and 168.6 eV, which correspond to the C-SH unbounded state (denoted S1), bounded state (denoted S2), and sulfonic acid (SO3H) (denoted S3), respectively [30, 31]. Sulfonic acid was formed from the oxidation of thiol in 2-ATP. According to the S3 peaks of S 2p, sulfonic acid is increased as the concentration of Fe dopants in TiO2 increases. To confirm the effect of the energy of light and its photocatalytic performance, relative intensities were plotted as the ratio of S3 to S1 (Fig. 5).
Fig. 5

Plots of the ratios of S3 to S1, indicating photocatalytic activity by oxidation of 2-ATP as a function of molecular exposure under a 365-nm UV light and b 540-nm visible light

Figure 5 shows the changes of relative intensity as a function of 2-ATP exposure under two different light sources. When UV (365 nm) is irradiated on the catalysts, photocatalytic activity increases by increase of Fe doping concentrates: 1 (0.15), 3 (0.29), and 5 wt.% (0.58). One significant observation is that photocatalytic oxidation is enhanced by increasing doping concentration under illumination in the visible range (540 nm). Otherwise, the ratio increased from 0.16 at 1 wt.% Fe to 0.73 at 5 wt.% of Fe, which shows significant increments compared to the intensity ratios under UV illumination. The phenomena arise from narrowing the TiO2 bandgap by doping and the heterojunction of Fe2O3 and TiO2 with high concentration.

Figure 6 and Additional file 1: Figure S5 (subtracted spectra by valence band of bare-TiO2) show the valence band spectra and changes with variations of the Fermi-edge. As shown in the valence band spectra (Fig. 6b), density of states arises at the valence band maximum and is expanded from 2.3 to 2.0 eV, and then to 1.4 eV, which indicates that the density of states lowers the bandgap significantly. There are two significant reasons for the bandgap reduction when the doping concentration is increased to 5 wt.%. One is the Fe3+ doping inside the TiO2, which generates the surface states as well as the oxygen-vacancy sites observed by XAS spectra with Ti3+ states on the HRPES spectra [32]. Those Ti3+, oxygen-vacancy couples introduce the dopant level inside the bandgap below the conduction band minimum and above the valence band maximum, respectively. Calculated density of states of anatase TiO2 with one oxygen vacancy per 16 oxygen atoms shows the similar Fermi-edge at below 2 eV [33]. And controllable Ti3+ shows the significant reduction the bandgap [34, 35]. The second reason is the precipitation as hematite Fe2O3, where the particles have a lower bandgap (2.1 eV) compared to TiO2 (3.2 eV) and promote bandgap narrowing by heterojunction between Fe2O3 and TiO2, enhancing the absorption of visible light [8, 26, 36]. From the mechanistic point of view, generated electrons after light absorption are trapped to the Ti3+ state below the conduction band minimum which facilitates the charge separation by using heterojunction. Those trapped electrons are transferred to O2 species with formation of Ti-O2 binding as peroxide. Peroxide has been indicated as electron scavenger O2 species in the traditional photocatalytic oxidation on TiO2 [37, 38]. S 2p spectra of HRPES (Fig. 4) show the relatively large amount of bound state (S2) when the doping level is increased. This is caused by the dissociative adsorption of –SH group at the oxygen atom of TiO2 which triggers the decomposition of peroxide [39, 40]. Consequently, the amount of trapped electrons at the Ti3+ state captures and stabilizes the O2 then 2-ATP decomposes –SH to –S-O-Ti (bound state, S2), –OH on the peroxide. (Scheme 1) –SH group of 2-ATP can be activated by the transfer of hole from the valence band. The energy relaxation of –SH group is around 2 eV compared to bare TiO2 which makes electron deficient –SH group to facilitate the oxidation reaction with electron rich peroxide [41]. Surface Fe3+ sites play a role of stabilization of –OH by hydrogen bonding during reaction process [42, 43]. From those reasons, doping concentration at 3 and 5 wt.% shows the narrowed bandgap that absorbs the photons more efficiently under 540 nm visible light, thus resulting in the significant enhancement of photo-oxidation activity [44, 45].
Fig. 6

a Valence band spectra and b the Fermi-edge obtained at 0, 1, 3, and 5 wt.% of Fe-doped TiO2 nanoparticles (marked) from the photon energy of 80 eV

Scheme 1

Schematic diagram for charge transfer with reaction mechanism


In summary, Fe@TiO2 nanoparticles were synthesized by sol-gel using a hydrothermal method. Their photocatalytic activity was characterized using surface spectroscopic measurements. According to the XRD, Raman, XAS, and HRPES spectra, Fe ions are successfully doped inside the anatase TiO2 substrate, and the crystal structure is changed to a distorted anatase-like structure that also has a hematite-Fe2O3 character as a Fe2O3 3TiO2 complex. These structural features form the lamellar structure in TEM images, which is attributed to the heterojunction between hematite Fe2O3 and anatase TiO2. Furthermore, the introduction of Fe3+ ions generates discrepancies in the oxidation state, which is compensated by the formation of oxygen vacancies and transforms to the surface [46]. These structural changes induce additional states at the edge of the conduction band and valence band, finally narrowing the bandgap. Moreover, the Ti3+ plays a role of electron trap to deliver the electrons to O2 species for oxidation reaction. As a result, photocatalytic oxidation activities of 2-ATP are significantly increased for both UV and visible photon energies.



This research was supported by the National Research Foundation of Korea (NRF) funded by the Korea government (MSIP) (no. 20090083525 and no. 2015021156).

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (, which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors’ Affiliations

Molecular-Level Interfaces Research Center, Department of Chemistry, KAIST
Beamline Research Division, Pohang Accelerator Laboratory (PAL)
Department of Chemistry, Pukyoung National University
Department of Chemistry, Sookmyung Women’s University


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