## Introduction

In the last decade, there is a numerous number of studies about functionality improvement of semiconductor photocatalysts to achieve both of ultraviolet (UV)-light and visible (VIS)-light responsive performance. Several strategies, such as band gap engineering by doping cations and/or anions, modification of surface structures, and design heterojunction with cocatalysts of metals or semiconductors, were employed to achieve UV/VIS responsive photocatalytic performance1,2,3,4. Although typical methods, such as solid state reaction5,6, solvothermal/hydrothermal reaction7,8,9,10, and vacuum deposition11,12, are successful approach to synthesize doped semiconductors and heterojunction materials, it is necessary to employ energy consuming and/or high environmental burden conditions, such as quite high temperature sintering, toxic gas flow, high pressure, and vacuum condition, which will give negative impact on environment. Mechanochemical process is known as a facile and an environmentally benign method13,14. Mechanochemical reaction often produces unique metastable materials which cannot be prepared by conventional thermochemical techniques15. For example, metastable amorphous calcium carbonate phase was successfully stabilized by mechanochemical Na doping16. Synthesis of metastable Li2OHCl is another example, which showed higher ionic conductivity compared with thermodynamically stable phase17. Nowadays, mechanochemical process is widely employed to synthesize not only typical organic and inorganic compounds, but also doped compounds and composites18,19,20,21. Moreover, the mechanisms of the co-crystallization and metastable formation through mechanochemical reactions were reported in the specific systems22,23. There is a strong demand to develop facile and promising process by using mechanochemical reaction for highly functional materials, such as UV- and VIS-light responsive semiconductor photocatalysts.

Titanium dioxide, TiO2, is one of the most investigated semiconductor which shows excellent photocatalytic activity under irradiation of UV-light24. Doping of metals/nonmetals and/or formation of heterojunction of TiO2/semiconductors were reported to effectively enhance photocatalytic performance25,26. For a preparation of doped TiO2 through mechanochemical reaction, metals and metal salts were used as dopant sources of cations in general. However, metals tend to weld each other to form composite rather than doping and metal salts gave unexpected doping from counter anions18,27. To avoid these drawbacks, it is necessary to optimize numerous mechanochemical reaction parameters, such as gas atmosphere, milling media, milling speed, milling time, and ball-to-powder weight ratio. Use of metal oxides instead of metals and metal salts is expected to be easier and successful way to dope metal cations into TiO2 matrixes.

In this study, we focused on the fabrication of Nb doped TiO2 by using mechanochemical process. Commercially available TiO2 nanoparticles (mixture of anatase and rutile phase) was employed as a starting material and synthesized TiNb2O7 microparticles was used as a Nb doping agent. Variety amounts of Nb atom were homogeneously incorporated into both of anatase and rutile nanoparticles by wet mechanochemical process. Nb doped anatase nanoparticles showed improved thermal stability owing to the pinning Nb atoms. It was found that heat treatment led Nb atoms distributed inhomogeneously at surface of nanoparticles to form gradient chemical compositional structures of poorly Nb doped TiO2 and highly Nb doped TiO2. The Nb doped TiO2 with chemical compositional gradient structure showed enhanced photocatalytic activity under both of UV- and VIS-light irradiation. Although Nb doped TiO2 were synthesized through vairous methods, such as pulsed laser deposition28,29, sol–gel technique30,31, thermal plasma processing32, and spray pyrolysis33, chemical compositional gradient structures have not been reported. This indicates that mechanochemically synthesized materials are key to form the gradient structure and enhance photocatalytic property. The method reported here is a simple and facile approach, hence it is expected to widely apply other dopant-semiconductor systems towards highly functionalized photocatalysts.

## Methods

### Chemicals

Titanium(IV) tetraisopropoxide (TTIP, 95%), niobium(V) pentaethoxide (NPE, 99.9%), diethanolamine (99%), polyethyleneimine (Mw = 1800), methyl orange (MO), sodium dihydrogen phosphate (NaH2PO4, 85%), phosphoric acid (H3PO4, 85%), ethanol (99.5%) were used as received. H3PO4 was purchased from Kanto Chemical Holdings. All other reagents were purchased from Wako Pure Chemicals Industries, Ltd. Ultrapure water of 18.2 MΩ∙cm resistivity was used in all experiments.

### Synthesis of TiNb2O7 microparticles

TTIP (1 mmol), NPE (2 mmol), and diethanolamine (2 mmol) were dissolved in 5 mL of ethanol. After stirring for 20 min, homogenous sol was obtained. Water (35 mmol) was added to the sol under vigorous stirring and keep stirring at least for 5 min to obtain gel. Gelatinous precipitates were dried at 100 °C for 12 h. Dried powders were heat treated at 1150 °C for 3 h (ramp rate: 5 °C/min). Heat treated powder of TiNb2O7 was employed as a Nb source in subsequent mechanochemical process because TiNb2O7 was reportedly segregated from Nb doped TiO2 only after high temperature heat treatment that means TiNb2O7 will be highly compatible with TiO232.

### Mechanochemical synthesis of Nb-doped TiO2 nanoparticles

Obtained TiNb2O7 powders were mixed with commercial anatase–rutile TiO2 nanoparticles (EVONIK AEROXIDE® P25, Nippon Aerosil, Tokyo, Japan) with a molar ratio of Nb/(Ti + Nb) = 0 (without TiNb2O7), 0.02, 0.05, and 0.10. After grounded for 30 min in a mortar, mixed powders (2.5 g) were dispersed in 20 mL of ethanol solution including polyethyleneimine (7.2 × 10−2 mmol). Obtained suspensions were sealed in zirconia pod (inner volume of 80 mL) and milled in a tilted rotation planetary ball mill (Planet M2-3F, Nagao System Inc.) at revolution speed of 700 rpm and rotation speed of 1750 rpm (152 G) for 2 h with zirconia balls (5 mm in diameter, #243, 83.5 g). Milled suspensions were dried at room temperature for 5 days and heat treated at 500 − 900 °C for 3 h (ramp rate: 5 °C/min, cooling rate: 2 °C/min). The powders prepared through this process were denoted as NTO-x-y, where x and y are nominal Nb/(Ti + Nb) in percentage (0 ≤ x ≤ 10) and heat treatment temperature (500 ≤ y ≤ 900) (As dried samples before heat treatment are denoted as NTO-x-dry).

### Photocatalytic test

The solution pH was kept at 2.1 using buffer solution to avoid agglomeration of nanoparticles during photocatalytic test, which changes background light scattering by particles. Phosphate buffer solution (0.10 mol/L, pH = 2.1) were prepared using NaH2PO4 and H3PO4. Sample powders (10 mg) were dispersed in 6 mL of buffered aqueous solution and ultrasonicated for 30 min. MO buffered aqueous solution (20 μmol/L, 20 μL) was added to the suspensions. Colored suspensions (3 mL) in close capped quartz cell (1 × 1 cm2 base rectangular cell) were exposed to UV/VIS-light after stirring in dark condition. UV light and VIS light were generated by UVF-203S Type-A light source (San-Ei Electric Co., Ltd., Japan) (365 nm) and UVF–203S Type-C light source (San-Ei Electric Co., Ltd., Japan) (405 and 436 nm) with intensities of 60 and 255 mW/cm2, respectively. The light probes were contacted to the quartz cell, which means the light-to-solution distance was same for all the experiments, ~ 1 mm. After appropriate irradiation time, the suspensions were left for 30 s without stirring and set in a UV–vis spectroscopy to determine MO concentration from the F(R) at 514 nm of diffuse reflectance spectra using calibration curve.

### Characterization

A field emission scanning microscope (SEM; S-8020, Hitachi High-Technologies Corp., Japan) equipped with energy dispersed X-ray spectroscopy (EDS) was used for evaluation of particle size and elemental composition. A transmission electron microscope (TEM; JEM-2100F, JEOL Ltd., Japan) equipped with EDS and scanning TEM mode (STEM) was employed at an operating voltage of 200 kV to clarify the crystal phase and elemental composition of individual particles. Powder X-ray diffraction (XRD) (SmartLab, Rigaku Corp., Japan) using Cu Kα radiation (λ = 0.1544 nm) equipped with one dimensional detector was used to characterize crystal phases of samples. X-ray photoelectron spectrometer (XPS) analyses were carried out with ESCA-5600 (Ulvac-Phi, Japan) using a monochromatic Al Kα source (1486.6 eV, 200 W) to evaluate an elemental composition of adjacent surface of particles and an oxidation state of Ti and Nb atoms. The instrument work function was calibrated to give an Au 4f7/2 of metallic gold binding energy of 83.95 eV ± 0.1 eV. Survey spectra and high-resolution spectra were collected with a step of 0.4 and 0.05 eV, respectively. The obtained spectra were calibrated using C 1 s binding energy (284.8 eV) of the samples as an internal standard. Ultraviolet–visible (UV–Vis) spectroscopy (V-650 spectrophotometer, JASCO Corp., Japan) equipped with an integrating sphere was used to characterize optical band gap of samples and evaluation of decolorization of MO solution. The reflectance values of obtained diffuse reflectance spectra were transformed to Kubelka–Munk units, F(R) by using Eq. (1)

$$F(R_{\infty } ) = { (}1 - F(R_{{\infty ,{\text{s}}}} ){)}^{2} /2(F(R_{{\infty ,{\text{s}}}} ))$$
(1)

where $$F(R_{{\infty ,{\text{s}}}} )$$ is measured reflectance value. Raman spectroscopy (RAMANtouch, Nanophoton Corp., Japan) was employed to characterize crystal phases and defects (excitation: 532 nm). The N2 adsorption–desorption measurement using Belsorp-18 (Bel Japan Inc., Japan) was employed to evaluate specific surface area by the Brunauer–Emmett–Teller (BET) method.

## Results and discussion

### Incorporation of Nb into TiO2 nanoparticles through mechanochemical treatment

TTIP and NPE were used as precursors to synthesize TiNb2O7 as a Nb doping agent. Addition of water to ethanolic solution, including TTIP, NPE, and diethanolamine, triggered hydrolysis and condensation of both metal alkoxides. During reaction, diethanolamine worked as a reaction controlling agent, which hinder vigorous reaction of NPE and enabled to form homogenous Ti and Nb mixed precipitates. Dried precipitates were characterized as poorly crystalline TiNb2O7 by XRD measurement (Figure S1). The precipitates were heat treated at 1150 °C for 3 h. Heat treated precipitates were characterized as well-crystalline TiNb2O7 with a crystallite size of 63.7 nm calculated using 110 diffraction peak. Obtained TiNb2O7 showed angulate shape with a particle size of 840 ± 359 nm (Fig. 1a,d). TiNb2O7 microparticles and commercially available TiO2 nanoparticles (particle diameter of 44.1 ± 16.7 nm) (Fig. 1b,e) were mixed and mechanochemically treated. After mechanochemical treatment, as dried powder (NTO-5-dry, see experimental section for sample IDs) showed the particle size of 43.8 ± 20.0 nm which is comparable size to the pristine TiO2 (Fig. 1c,f). Figure 2a,b are TEM image of NTO-5-dry. The lattice fringe close to particle surface became disorder after mechanochemical treatment, which is a feature of amorphous phase. Raman spectra of pristine TiO2, NTO-5-dry, and NTO-5-600 were shown in Figure S2. The peak around 145 cm−1, assigned as Eg mode of symmetric stretching vibrations of O–Ti–O bonds of anatase phase34, was shifted to 148 cm−1 after mechanochemical treatment (NTO-5-dry), which indicates formation of oxygen vacancies13. Grayish color of NTO-5-dry powder agrees formation of oxygen vacancies in TiO2 matrix35. The peak shifted back to 145 cm−1 after heat treatment at 600 °C indicating elimination of vacancies. The atomic ratios of Nb/(Ti + Nb) evaluated by SEM–EDS and XPS were well matched with nominal molar ratio (Table S1). Figure 2c shows the local Nb/(Ti + Nb) ratio measured by STEM-EDS line scanning. The scanned line was shown in Fig. 2a as green dots, which crosses both of rutile and anatase nanoparticles. Nb atoms were detected at entire points, which implies that Nb atoms were homogeneously incorporated in both of anatase and rutile nanoparticles.

XRD patterns of powders before and after mechanochemical treatment were shown in Fig. 2d with the pattern of TiNb2O7 microparticles. Detected crystalline species were anatase and rutile phase with trace amount of TiNb2O7 after mechanochemical reaction. Crystallite size of TiNb2O7, anatase, and rutile before/after mechanochemical treatment were calculated as 63.7/31.7 nm, 21.4/20.7 nm, and 29.2/25.8 nm, respectively. Drastic crystallite size reduction of TiNb2O7 indicates that TiO2 crystals were more stable than TiNb2O7 crystals against mechanical energy. Reported Young’s modulus of each crystals (255.5–311.6 GPa for TiO236 and 173 ± 5 GPa for TiNb2O737) supports that preferential amorphization of TiNb2O7 crystals took place during mechanochemical treatment. Lattice volume of anatase (135.98(8) Å3) and rutile (62.48(3) Å3) phases of NTO-5-dry was comparable to those of pristine TiO2 (136.01(7) Å3 and 62.51(3) Å3). This may be result of competitive effects between lattice expansion due to Nb substitution31,32 and lattice contraction due to interstitial oxygen in TiO238 incorporated to compensate charge balance39,40.

Figure 3a shows XRD patterns of powders heat treated at 500–900 °C (NTO-5-y, y = 500–900). The intensity of peaks assigned as rutile phase increased with increasing the heat treatment temperature. The weight fraction of rutile phase against anatase phase, fR, was calculated using following Eq. (2)41;

$$f_{{\text{R}}} = \, 1/\left( {1 + 0.79 \cdot I_{{\text{A}}} /I_{{\text{R}}} } \right)$$
(2)

where IA and IR are integrated intensities of rutile 110 diffraction peak and anatase 101 diffraction peak, respectively. Temperature dependent changes of fR were shown in Fig. 3b. NTO-0-dry and NTO-5-dry showed fR comparable to pristine TiO2. Although a phase transition from anatase to rutile by mechanochemical treatment was reported42, amorphous layer formation on the surface of nanoparticles and preferential amorphization of TiNb2O7 may consume mechanical energy and retard phase transition of anatase. In the case of ground mixed powders of pristine TiO2 and TiNb2O7 in a mortar, fR drastically increased with temperature and reached fR ~ 1.0 after heat treatment at 700 °C. NTO-0-y showed smaller fR than powder mixtures at each heat treatment temperature, which indicates formed surface amorphous layer worked as effective grain boundary and retarded phase transition. In the case of NTO-5-y, ~ 60% of anatase crystals were remained even after heat treated at 800 °C. In addition to amorphous layer formation, incorporated Nb atoms worked as pinning sites and improved thermal stability31,32. Thermal stability of anatase phase was also improved in the case of NTO-2-y and NTO-10-y (Figure S3a), which indicates that incorporated Nb atoms effectively worked as pining sites even if small quantity.

Chemical compositions of heat-treated powders were investigated by using SEM–EDS and XPS techniques (Fig. 4a). Nb/(Ti + Nb) ratio calculated from SEM–EDS spectra of NTO-2-y, NTO-5-y, and NTO-10-y were well matched with nominal value. On the other hand, Nb/(Ti + Nb) ratio calculated using XPS spectra were increased with increasing the heat treatment temperature, which means that heat treated Nb doped TiO2 have inhomogeneous chemical composition between surface and core of the particles. The Nb/(Ti + Nb) increased with increasing heat treatment temperature independently of the integrated area of diffraction peak of TiNb2O7, except NTO-10-900 (Figure S3b). This implies that Nb atoms were still incorporated in the TiO2 lattice and/or in amorphous like Nb-rich oxide phases at the surface of nanoparticles. Figure 4b,c were XPS Ti 2p and Nb 3d core level spectrum of NTO-5-600. Both spectra were fitted with two of peak functions. The fitted peak positions of Ti 2p1/2 and Ti 2p3/2 were 464.6 eV and 458.9 eV, respectively, which is a good agreement with reported value of Ti4+43. The fitted peak positions of Nb 3d3/2 and Nb 3d5/2 were 210.0 eV and 207.2 eV, respectively. The Nb 3d5/2 peak position is intermediate of Nb4+ (205.9 eV) and Nb5+ (207.5 eV)44. In the case of titanium niobium oxides family (TiNbmO2+2.5 m), relatively Ti rich compounds, such as TiNb2O7 (m = 2)45 and Ti2Nb10O29 (m = 5)46 showed Nb 3d5/2 peak position same as mixture of Nb4+ and Nb5+ in Nb-doped TiO231 and relatively Nb rich compounds, such as TiNb6O17 (m = 6)47 and TiNb24O62 (m = 24)48 showed the peak position same as Nb5+ in Nb2O5. Considering Nb/(Ti + Nb) of NTO-5–600 was 0.11, it is reliable that Nb was exist as a mixture of Nb4+ and Nb5+. All the samples showed Ti 2p3/2 = 458.8 ± 0.2 eV and Nb 3d5/2 = 207.1 ± 0.2 eV which indicate that the oxidation states of Ti and Nb were stable during heat treatment.

Further analysis was demonstrated using TEM and STEM-EDS. Figure 5a–d were STEM and STEM-EDS mapping images. Although Ti atoms were homogenously distributed in the individual particles, Nb atoms inhomogeneously distributed around the edges of the particles. Figure 5e is the result of line scanned STEM-EDS analysis. Nb/(Ti + Nb) clearly increased at the scan point of the particle edges. Figure 5f–h are TEM image of the location where STEM-EDS mapping and line scan were taken. The start and end points of STEM-EDS line scan were located at the nanoparticles of anatase and rutile, respectively. Therefore, Nb rich TiO2 (Nb/(Ti + Nb) ~ 0.25) were formed at the surface of both anatase and rutile nanoparticles. The changes of lattice fringes were analysed by fast Fourier transform method (Figure S4). Clear spots corresponding to anatase 101 and rutile 101 lattice fringes were obtained at the analysis area enough distant from the particle surface. On the other hand, the fast Fourier transform images prepared using the analysis area around surface showed blurred spots with broad ring patterns, which indicates segregation of Nb atoms at the surface made the lattice disordered. XPS, STEM-EDS, and TEM analyses indicate that gradient chemical composition was spontaneously developed; poorly Nb doped TiO2 at the core of the nanoparticles and highly Nb doped TiO2 at the surface of nanoparticles.

Optical properties were investigated using UV–Vis diffuse reflectance spectroscopy (Figure S5 and S6). Obtained diffuse reflectance spectra were converted to (F(R)hν)2 versus hν and (F(R)hν)1/2 versus hν plots for an evaluation of direct and indirect transitions, respectively. Direct band gap energies were decreased with increasing heat treatment temperature (Figure S6a). On the other hands, indirect band gap energies were slightly increased with increasing heat treatment temperature (Figure S6b). There is a rough linear relationship between fR and the direct band gap energy (Figure S6c) and between Nb/(Ti + Nb) and indirect band gap energy (Figure S6d). These results indicate that rutile phase and niobium titanium oxide phases are dominant factor of direct and indirect band gaps, respectively. In fact, direct and indirect band gaps were approaching to corresponding band gaps; direct band gap of rutile phase is 3.0 eV49 and indirect band gap of TiNb2O7 phase is 3.1 eV45, respectively.

In summary, mechanochemical treatment using TiO2 nanoparticles and TiNb2O7 microparticles produced Nb doped TiO2 nanoparticles as a result of preferential amorphization of TiNb2O7 phase. Homogenously incorporated Nb atoms diffused to the surface of nanoparticles after heat treatment. Resultant nanoparticles of both anatase and rutile-based phase had gradient chemical composition of highly Nb doped TiO2 and poorly Nb doped TiO2.

### Photocatalytic performance

The photocatalytic performances of mechanochemically prepared powders were evaluated by decoloration of methyl orange (MO) aqueous solution, which is widely employed to investigate the properties of photocatalysts. In addition to NTO-xy, pristine TiO2 and homogeneously Nb incorporated TiO2 synthesized by thermal plasma treatment32 (Nb/(Ti + Nb) ~ 0.21, TP-20)) were tested as a control. Diffuse reflectance measurements were employed to trace decoloration of MO. Figure 6 shows typical results of MO decoloration. The peaks correspond to MO were clearly decreased with light irradiation time (Fig. 6a,b). The calculated −ln(Ct/C0), where C0 and Ct were MO concentrations of initial and t min light irradiated solutions, were plotted against irradiation time (Fig. 6c). According to the following Eq. (3) for first-order reaction, the rate constants were determined;

$$- \ln \left( {C_{{\text{t}}} /C_{0} } \right) \, = k \cdot t$$
(3)

where k and t were rate constants (kUV and kVIS under UV- and VIS-light irradiation, respectively) and irradiation time. Figure 7a,c are summary of kUV and kVIS for all the tested samples. Both of kUV and kVIS of NTO-0-y were decreased with increasing heat treatment temperature same as TiO2. In the case of TiO2 and NTO-0-y, there was a relation between fR and kUV/kVIS; the photocatalytic activity decreased with increasing fR (Fig. 7b,d). Decrease of kUV is due to decrease of UV-light active anatase phase. The trend of kVIS is different from reported studies, in which heat treated TiO2 photocatalysts showed volcanic plot of VIS-light activity against fR50,51,52. The mechanism of photocatalytic activity in the case of anatase/rutile mixed phase was reported as follows; formation of heterojunction between anatase and rutile allows electrons transfer from rutile to anatase through interface that stabilizes charge separation and hinders charge recombination53. It is supposed that formed amorphous layers after mechanochemical treatment inhibit formation of anatase/rutile heterojunction, which disturbs electron transfer and results decrease of photocatalytic performance.

NTO-2-dry, NTO-5-dry, and NTO-10-dry showed significant increase of kUV compared with NTO-0-dry and TiO2. Although mechanochemically synthesized samples showed increased kUV with increasing Nb doping amount, TP-20 having largest amount of Nb dopant revealed lowest kUV. It is supposed that metastable doping by mechanochemical treatment promoted photocatalytic performance. The kUV further improved after heat treatment at 600 °C only in the case of mechanochemically Nb doped samples, which indicates formed chemical compositional gradient enhanced photocatalytic reaction. The kUV tend to decrease with increasing heat treatment temperature above 600 °C, i. e., increasing fR as is shown in Fig. 7b. These results imply that Nb doped anatase nanoparticles having chemical compositional gradient structure are dominant component for an enhancement of UV-light photocatalytic performance. Although kVIS of NTO-2-dry, NTO-5-dry, and NTO-10-dry were smaller than TiO2 and NTO-0-dry, those were drastically increased after heat treatment. Considering kVIS increased with further increasing fR, it is supposed that Nb doped rutile nanoparticles gave significant enhancement of VIS-light photocatalytic performance. Surprisingly, NTO-2-800 showed significant high kUV and kVIS despite smaller specific surface area (3.21 m2/g) compared with pristine TiO2 (45.7 m2/g), NTO-2-dry (53.6 m2/g) and TP-20 (87.2 m2/g). It is reported that Cu nanocluster-grafted Nb-doped TiO2 showed VIS active photocatalytic performance owing to the energy level matching54. Considering these, formation of chemical compositional gradient structures will result energy level matching and lead excellent photocatalytic performance under both of UV- and VIS-light irradiation.

The effects of Nb doping on physical properties of TiO2 have been reported; with increasing amount of Nb dopant, band gap energy became large and electron conductivity enhanced29,55,56,57. In addition, Nb doping leads generation of Ti3+ improving photocatalytic activity58,59, which is not detected by XPS but detected by electron paramagnetic resonance technique60. Considering these reports, the hypothetic mechanism of mechanochemically prepared photocatalysts is summarized in Fig. 8. Electron–hole pair will generate at the poorly Nb doped TiO2 (core part of nanoparticles) due to their smaller band gap energy compared with highly Nb doped TiO2 (surface part of nanoparticles). Electrons will move to highly Nb doped TiO2 because of larger conductivity. In addition, electron will transfer from rutile to trapping site of anatase around heterointerface, which is reported to be 0.8 eV lower than the conduction band edge of anatase61. These processes will stabilize charge separation and retard charge recombination. Considering Nernstian shift of conduction bands of TiO262,63, O2 radical formation through single-electron reduction reaction may be minor reaction. HO2 radical and H2O2 formed and attacked to MO molecules leading decoloration. The reported energy levels of valence band maximum and conduction band minimum of anatase, rutile, and TiNb2O7 (as a typical example of Nb-rich titanium oxides) consistent with our hypothesis45,64.

## Conclusion

Nb doped TiO2 were synthesized through mechanochemical reaction between TiO2 (rutile/anatase) nanoparticles and TiNb2O7 microparticles owing to the relatively lower elastic modulus of TiNb2O7. Homogeneously distributed Nb atoms tended to move to particle surface after high temperature heat treatment, which indicates initially formed Nb doped TiO2 was metastable phase. Resultant materials had gradient chemical compositional structure of poorly Nb doped TiO2 core part and highly Nb doped TiO2 surface part. It was found that the materials with gradient chemical compositional heterojunction structure showed enhanced photocatalytic activity under both of UV- and VIS-light irradiation. Obtained results in this study indicate metastable materials prepared by mechanochemical treatment will show unique functions which are different from materials prepared by conventional thermal processes. It is expected to enhance not only photocatalytic property but also other functionalities, such as catalytic and electrochemical activity, by design materials through mechanochemical treatment.