Construction of Rutile-TiO2 Nanoarray Homojuction for Non-Contact Sensing of TATP under Natural Light

Triacetone triperoxide (TATP) is a new terrorist explosive, and most nitrogen-based sensors fail to detect TATP. Herein, a sea urchin-like TiO2-covered TiO2 nanoarray is constructed as a TATP-sensitive homojunction (HJ) by one step hydrothermal method. By taking fluorine-doped tin oxide (FTO) and indium tin oxide (ITO) conducting glass as the substrate, the conducting glass is horizontally and vertically put in the reactor to epitaxially grow TiO2–FTO, TiO2–ITO, TiO2–FTO–HJ and TiO2–ITO–HJ. TiO2–FTO–HJ shows a broad absorption band edge in the visible region and high sensitivity to TATP under the simulating natural light compared with TiO2–FTO, TiO2–ITO, and TiO2–ITO–HJ. E-field intensity distribution simulation reveals that constructing homojunctions between the urchin-shaped TiO2 nanosphere and TiO2 nanoarrays can enhance the localized electromagnetic field intensity at the interface of junctions, which may provide photocatalysis active sites to reduce TATP molecules by promoting charge separation. Moreover, the TiO2–FTO–HJ shows high selectivity to TATP among ammonium nitrate, urea and sulfur, which are common homemade explosive raw materials.


Introduction
In recent years, the bombing terrorist attack has become the main manifestation of terrorism activities. Public places with dense populations, such as railway stations, airports, subway stations, and so on, are becoming the first target of terrorists, and so carrying out explosive detection in public places is an important anti-terrorist measure. How to rapidly and accurately detect explosives in luggage parcels in real time has become an important topic of today's anti-terrorist activities in the international community [1][2][3][4][5].
Common explosives can be simply divided into standard explosives and non-standard explosives. Standard explosives mainly include 2,4,6-trinitrotoluene (TNT), 2,4-dinitrotoluene (DNT), p-nitrotoluene (PNT), picric acid (PA), etc. Non-standard explosives mainly include triacetone peroxide (TATP), Ammonium nitrate (AN), Urea, Sulfur, etc. There are various kinds of detection techniques for explosives at present [6][7][8][9][10][11][12][13]. Among these, dog sniffing method is one traditional detection method for tracing explosives, and its sensitivity is able to reach the parts per trillion (ppt) range. However, it has low efficiency. Police dogs generally need to rest for 15 to 30 min after continuously working for 30 min, and the training cost is high. In addition to the dog sniffing method, detection methods of explosives with more mature technology include the fluorescence detection method [14], electrochemical detection [15], ion spectroscopy [16], X-ray spectrometry, and so on [17]. However, these techniques also have disadvantages; for example, for ion spectroscopy and X-ray imaging technology, the equipment is heavy with high costs. Meanwhile, chromatographic analysis is limited to laboratory detection and cannot meet the requirements of field detection. In addition, most detection techniques cannot achieve the detection of non-standard explosives, and these disadvantages restrict the application in the actual detection of explosive. Moreover, several technologies have been discovered for the detection of trace amounts of TATP (Table S1).
Inspired by the dog sniffing method, a material used in gas-sensitive sensors for detecting explosives is produced by making use of the inherent properties of metal oxide semiconductors. In addition, gas-sensitive sensors are the most suitable for manufacturing portable explosive detection devices for explosives [17][18][19]. The detection of explosives is determined based on the electrical signal of the gas-sensitive sensor. One feasible way of improving the detection speed, sensitivity, accuracy and other attributes of the sensor is to magnify the contact area between the gas molecules and the sensor. TiO 2 has good gas sensitivity and TiO 2 nanoarray can effectively enhance the contact area. Wang et al. [20] successfully prepared highly ordered aligned nitrogen-doped titania nanotube array films by liquid phase deposition (LPD) method, obtaining a new band gap corresponding to 2.17 eV in the visible region (570 Nm). Jie et al. [21] fabricated the silver ion-modified titanium nanotube array (AG/TiO 2 -NT) by electrochemical anodization as an electrochemical energy storage electrode for supercapacitors. Jain et al. [22] developed sensors using gold nanoparticles (GnPs) and tubular TiO 2 for the detection of glycated hemoglobin in blood. The group of Hu [23] used anatase TiO 2 arrays with different crystal faces in different solvents by low-temperature solvothermal synthesis, which is mainly used in the field of photocatalysis. Cheng et al. [24] organized Pd nanoparticles on the surface of a carbon-coated TiO 2 nanowire array substrate using the potentiostatic pulse method, which is also used in the field of photocatalysis. Zhang et al. [25] developed TiO 2 /ZnFe-LDH photoanode by photo-assisted electro deposition on TiO 2 nanoarray for the cracking performance of PEC water.
Although TiO 2 nanoarrays can be prepared by different methods, the above methods were not simple or effective in detecting gas sensing. In this work, the hydrothermal method is used to prepare a titanium dioxide nanoarray and to analyze the phase, morphology, ultraviolet absorption spectrum and gas-sensitive properties of the titanium dioxide nanoarray.

Experimental
Preparation of TiO 2 -FTO: FTO glass was subjected to ultrasonic cleaning in acetone, ethyl alcohol and deionized water for 15 min and dried. The FTO glass was vertically fixed on the Teflon-lined stainless autoclave wall. 10 mL of concentrated hydrochloric acid and 1 mL of titanium tetrachloride was continually stirred for 10 min. Then the above resulting mixture is transferred into a Teflon-lined stainless autoclave and maintained at 180 • C for 4 h. The system was then naturally cooled to ambient temperature. After that, the precipitation was sequentially washed with ethanol and distilled water to obtain TiO 2 -FTO. Preparation of TiO 2 -FTO-HJ: The preparation process was similar to the process for TiO 2 -FTO. The difference is that the FTO glass was horizontally fixed on the bottom of the Teflon-lined stainless autoclave.
The preparation process of TiO 2 -ITO and TiO 2 -FTO-HJ was similar to the process for TiO 2 -FTO and TiO 2 -FTO-HJ. The difference was that the FTO glass was replaced by ITO glass.

Characterization
The scanning electron microscope used in the experiment was JEOL's JSM-6106LV (Tokyo, Japan). The Bruker Corporation's X-ray diffractometer D8 Advance (Billerica, MA, USA) was used to analyze the sample, and Kα radial of the Cu target material was used (Wavelength λ = 1.5418 Å. voltage V = 40 kV and electricity I = 40 mA). Thermo Electron's Fourier transform infrared spectrum analyzer Nicolet 6700 (Waltham, MA, USA) was used to measure the infrared absorption spectrum. The measurement range was 4000-400 wavenumber (cm −1 ). The UV-Vis absorption spectrum was determined using UV-4802S of Unico Instrument Co., Ltd. (Dayton, OH, USA), with a testing range of 300-800 nm. The Raman spectrum was recorded on Renishaw's microscopic confocal Raman spectrometer RM2000 (Gloucestershire, UK) with a laser wavelength of 514 nm.
The different analytes were evaporated in a 50 mL transparent chamber and the test was conducted at room-temperature in saturated ammonium nitrate (AN), urea and sulfur (S) vapor. Since the TATP has very high vapor pressure at room temperature, it is diluted by air to 600 ppb. The time-dependent photoresponse of the sensor film was determined in a conventional two electrode configuration and recorded by Keithley 4200A-SCS Parameter Analyzer (Portland, ME, USA) under the simulating natural light.

Morphology of TiO 2 Nanoarray
The FTO and ITO conducting glass is horizontally or vertically put into the reaction still in order to construct a TiO 2 nanoarray by a simple hydrothermal method. Figure 1 is the SEM images of TiO 2 nanoarray that puts FTO conducting glass into the reaction vessel vertically at 180 • C for 4 h.  Figure 1a,c respectively. As can be seen from Figure 1a,b, the TiO 2 nanoarray is rod-shaped with uniform growth, and the length of the nanoarray is basically consistent. Combined with Figure 1c,d, the uniformity of the nanoarray can be clearly seen. The two sides of the nanoarray are basically parallel, and the thickness of the nanoarray is about 10.8 µm. The TiO 2 nanoarray grown on FTO conducting glass is recorded as TiO 2 -FTO. Figure 2 is the SEM images of the TiO 2 nanoarray that places the ITO conducting glass into the reaction vessel vertically at 180 • C for 4 h.   Figure 1a,c respectively. As can be seen from Figure 1a,b, the TiO2 nanoarray is rod-shaped with uniform growth, and the length of the nanoarray is basically consistent. Combined with Figure 1c,d, the uniformity of the nanoarray can be clearly seen. The two sides of the nanoarray are basically parallel, and the thickness of the nanoarray is about 10.8 µm. The TiO2 nanoarray grown on FTO conducting glass is recorded as TiO2-FTO.     Figure 3 shows the microtopography of TiO2 nanoarray that places the FTO conducting glass into the reaction vessel vertically at 180 °C for 4 h. Figure 3a,b shows the front view of TiO2 nanoarray grown on conducting glass substrate. As can be seen in Figure 3a,b, there are stacked sea urchinshaped TiO2 nanoarrays on the surface, with different sizes and dense arrangement. The length and diameter of the nanorods are basically equal in the same urchin-shaped TiO2 nanoarray. The inset in Figure 1a is the cross-section diagram and enlarged view of TiO2 nanoarray generated on the FTO conducting glass. It can be clearly seen that the TiO2 grown on the horizontally placed conducting glass is composed of TiO2 nanorod arrays and urchin-shaped TiO2 nanoarrays that are in contact with the bottom surface. The two kinds of nanoarrays with different morphologies are combined to form the homojunction of the TiO2 nanoarray (recorded as TiO2 -HJ, HJ: Homojunction), and the thickness of the homojunction of the TiO2 nanoarray is between 150 and 200 mm. Figure 3c,d shows the reverse side of the TiO2 grown on the FTO conducting glass and their enlarged views. The reverse side indicates the contact surface between TiO2 nanoarray and conducting glass. As can be seen in Figure  3c,d, the nanorods are arranged in order with the diameter of 600 nm and the vertical extent of the TiO2 nanorod array is obviously improved when the FTO conducting glass is placed vertically.  Figure 3 shows the microtopography of TiO 2 nanoarray that places the FTO conducting glass into the reaction vessel vertically at 180 • C for 4 h. Figure 3a,b shows the front view of TiO 2 nanoarray grown on conducting glass substrate. As can be seen in Figure 3a,b, there are stacked sea urchin-shaped TiO 2 nanoarrays on the surface, with different sizes and dense arrangement. The length and diameter of the nanorods are basically equal in the same urchin-shaped TiO 2 nanoarray. The inset in Figure 1a is the cross-section diagram and enlarged view of TiO 2 nanoarray generated on the FTO conducting glass. It can be clearly seen that the TiO 2 grown on the horizontally placed conducting glass is composed of TiO 2 nanorod arrays and urchin-shaped TiO 2 nanoarrays that are in contact with the bottom surface. The two kinds of nanoarrays with different morphologies are combined to form the homojunction of the TiO 2 nanoarray (recorded as TiO 2 -HJ, HJ: Homojunction), and the thickness of the homojunction of the TiO 2 nanoarray is between 150 and 200 mm. Figure 3c,d shows the reverse side of the TiO 2 grown on the FTO conducting glass and their enlarged views. The reverse side indicates the contact surface between TiO 2 nanoarray and conducting glass. As can be seen in Figure 3c,d, the nanorods are arranged in order with the diameter of 600 nm and the vertical extent of the TiO 2 nanorod array is obviously improved when the FTO conducting glass is placed vertically.  Figure 4 shows the microtopography of TiO2 nanoarray that places ITO conducting glass into the reaction vessel vertically at 180 °C for 4 h. Figure 4a,b shows the front view of the homojunction of the TiO2 nanoarray grown on the ITO conducting glass substrate. There are stacked urchin-shaped TiO2 nanoarrays on the surface, with different sizes and dense arrangement. The morphology of the growth of the ITO conductive glass is similar to that of the nanoarray formed when the FTO conductive glass is the substrate, and the nanorods are arranged radially. The urchin-shaped TiO2 nanoarrays are substantially equal. The inset in Figure 4a is the cross-section diagram and enlarged view of TiO2 generated on ITO conducting glass. It can be clearly seen that the urchin-like nanospheres are supported by TiO2 nanoarrays. The thickness of the homojunction of the TiO2 nanoarray is between 150 and 200 mm. Figure 4c,d shows the reverse side of TiO2 grown on ITO conducting glass. It can also be seen from the back view that the compactness of the TiO2 nanorod array, which is generated by taking the ITO, is lower than that of the TiO2 nanorod array that takes the FTO conducting glass as the substrate. The morphology of nanorods grown on various conducting glasses are different, which may be due to the different crystal structures of the conducting glasses. The ITO glass is composed of 10 wt.%  Figure 4 shows the microtopography of TiO 2 nanoarray that places ITO conducting glass into the reaction vessel vertically at 180 • C for 4 h. Figure 4a,b shows the front view of the homojunction of the TiO 2 nanoarray grown on the ITO conducting glass substrate. There are stacked urchin-shaped TiO 2 nanoarrays on the surface, with different sizes and dense arrangement. The morphology of the growth of the ITO conductive glass is similar to that of the nanoarray formed when the FTO conductive glass is the substrate, and the nanorods are arranged radially. The urchin-shaped TiO 2 nanoarrays are substantially equal. The inset in Figure 4a is the cross-section diagram and enlarged view of TiO 2 generated on ITO conducting glass. It can be clearly seen that the urchin-like nanospheres are supported by TiO 2 nanoarrays. The thickness of the homojunction of the TiO 2 nanoarray is between 150 and 200 mm. Figure 4c,d shows the reverse side of TiO 2 grown on ITO conducting glass. It can also be seen from the back view that the compactness of the TiO 2 nanorod array, which is generated by taking the ITO, is lower than that of the TiO 2 nanorod array that takes the FTO conducting glass as the substrate.  Figure 4 shows the microtopography of TiO2 nanoarray that places ITO conducting glass into the reaction vessel vertically at 180 °C for 4 h. Figure 4a,b shows the front view of the homojunction of the TiO2 nanoarray grown on the ITO conducting glass substrate. There are stacked urchin-shaped TiO2 nanoarrays on the surface, with different sizes and dense arrangement. The morphology of the growth of the ITO conductive glass is similar to that of the nanoarray formed when the FTO conductive glass is the substrate, and the nanorods are arranged radially. The urchin-shaped TiO2 nanoarrays are substantially equal. The inset in Figure 4a is the cross-section diagram and enlarged view of TiO2 generated on ITO conducting glass. It can be clearly seen that the urchin-like nanospheres are supported by TiO2 nanoarrays. The thickness of the homojunction of the TiO2 nanoarray is between 150 and 200 mm. Figure 4c,d shows the reverse side of TiO2 grown on ITO conducting glass. It can also be seen from the back view that the compactness of the TiO2 nanorod array, which is generated by taking the ITO, is lower than that of the TiO2 nanorod array that takes the FTO conducting glass as the substrate. The morphology of nanorods grown on various conducting glasses are different, which may be due to the different crystal structures of the conducting glasses. The ITO glass is composed of 10 wt.%  The morphology of nanorods grown on various conducting glasses are different, which may be due to the different crystal structures of the conducting glasses. The ITO glass is composed of 10 wt.% SnO 2 doped In 2 O 3 . SnO 2 have rutile structure, while In 2 O 3 has cubic ferromanganese crystal structure. TiO 2 epitaxial grow on the ITO surfaces to obtain loose nanoarray with rutile structure due to the low content of SnO 2 . By comparison, the FTO glass is only composed of rutile SnO 2 . TiO 2 epitaxial grow on the external surfaces of the SnO 2 to obtain more orderly and denser rutile nanorod arrays.
Moreover, it can be found that under the same hydrothermal conditions, the homojunction is formed when the conducting glass is placed horizontally in the reaction vessel, while only nanoarray is formed when the conducting glass is placed vertically. Under certain temperature conditions, the TiO 2 generated by hydrolysis nucleates on the conducting glass and continues to grow into nanorods after nucleation. When the nanorods grow to a certain length, the hydrolysis reaction continues to produce a large amount of TiO 2 . TiO 2 grows into urchin-shaped-like TiO 2 nanoballs in solution. A large amount of TiO 2 exceed the growth rate of TiO 2 nanorods along the vertical direction on the conducting glass and falls directly on the TiO 2 nanorods that have been already generated, which forms the titanium dioxide nanoarray homojunction. The schematic diagram of the formation mechanism is shown in Figure 5a shows the schematic diagram of the formation of TiO 2 nanoarray when the conducting glass is placed vertically. Figure 5b indicates the schematic diagram of the homojunction of TiO 2 nanoarray when conducting glass is placed horizontally.
Coatings 2020, 10, 409 6 of 12 SnO2 doped In2O3. SnO2 have rutile structure, while In2O3 has cubic ferromanganese crystal structure. TiO2 epitaxial grow on the ITO surfaces to obtain loose nanoarray with rutile structure due to the low content of SnO2. By comparison, the FTO glass is only composed of rutile SnO2. TiO2 epitaxial grow on the external surfaces of the SnO2 to obtain more orderly and denser rutile nanorod arrays. Moreover, it can be found that under the same hydrothermal conditions, the homojunction is formed when the conducting glass is placed horizontally in the reaction vessel, while only nanoarray is formed when the conducting glass is placed vertically. Under certain temperature conditions, the TiO2 generated by hydrolysis nucleates on the conducting glass and continues to grow into nanorods after nucleation. When the nanorods grow to a certain length, the hydrolysis reaction continues to produce a large amount of TiO2. TiO2 grows into urchin-shaped-like TiO2 nanoballs in solution. A large amount of TiO2 exceed the growth rate of TiO2 nanorods along the vertical direction on the conducting glass and falls directly on the TiO2 nanorods that have been already generated, which forms the titanium dioxide nanoarray homojunction. The schematic diagram of the formation mechanism is shown in Figure 5a shows the schematic diagram of the formation of TiO2 nanoarray when the conducting glass is placed vertically. Figure 5b indicates the schematic diagram of the homojunction of TiO2 nanoarray when conducting glass is placed horizontally.     Figure 6 shows the Raman spectrum of TiO 2 nanoarray, which shows well-resolved peaks of TiO 2 -FTO-HJ located at 240.35 cm −1 , 443.13 cm −1 , and 610.42 cm −1 , and the well-resolved peaks of TiO 2 -ITO-HJ located at 235.29 cm −1 , 444.82 cm −1 and 610.42 cm −1 . From these results, it can also be concluded that the crystal structures of the two homojunctions are rutile [26].
Coatings 2020, 10, 409 6 of 12 SnO2 doped In2O3. SnO2 have rutile structure, while In2O3 has cubic ferromanganese crystal structure. TiO2 epitaxial grow on the ITO surfaces to obtain loose nanoarray with rutile structure due to the low content of SnO2. By comparison, the FTO glass is only composed of rutile SnO2. TiO2 epitaxial grow on the external surfaces of the SnO2 to obtain more orderly and denser rutile nanorod arrays. Moreover, it can be found that under the same hydrothermal conditions, the homojunction is formed when the conducting glass is placed horizontally in the reaction vessel, while only nanoarray is formed when the conducting glass is placed vertically. Under certain temperature conditions, the TiO2 generated by hydrolysis nucleates on the conducting glass and continues to grow into nanorods after nucleation. When the nanorods grow to a certain length, the hydrolysis reaction continues to produce a large amount of TiO2. TiO2 grows into urchin-shaped-like TiO2 nanoballs in solution. A large amount of TiO2 exceed the growth rate of TiO2 nanorods along the vertical direction on the conducting glass and falls directly on the TiO2 nanorods that have been already generated, which forms the titanium dioxide nanoarray homojunction. The schematic diagram of the formation mechanism is shown in Figure 5a shows the schematic diagram of the formation of TiO2 nanoarray when the conducting glass is placed vertically. Figure 5b indicates the schematic diagram of the homojunction of TiO2 nanoarray when conducting glass is placed horizontally.      Figure 7. It can be seen that the TiO 2 with four morphologies have crystal faces of (110), (101), (002), (301) and (112), which indicates that the crystal structures of TiO 2 -FTO, TiO 2 -ITO, TiO 2 -FTO-HJ and TiO 2 -ITO-HJ are tetragonal rutile phase [27]. The (101) diffraction peak of TiO 2 grown on FTO conducting glass substrate is the strongest and sharpest, which suggests that the structure order degree of TiO 2 -FTO was improved by FTO [26,27].

X-ray diffraction (XRD) characterization is presented in
Coatings 2020, 10, 409 7 of 12 3.1.2. The Structure of the TiO2 Nanoarray X-ray diffraction (XRD) characterization is presented in Figure 7. It can be seen that the TiO2 with four morphologies have crystal faces of (110), (101), (002), (301) and (112), which indicates that the crystal structures of TiO2-FTO, TiO2-ITO, TiO2-FTO-HJ and TiO2-ITO-HJ are tetragonal rutile phase [27]. The (101) diffraction peak of TiO2 grown on FTO conducting glass substrate is the strongest and sharpest, which suggests that the structure order degree of TiO2-FTO was improved by FTO [26,27]. It can be seen from the FT-IR spectrum of TiO2 nanoarrays in Figure 8 that a weak absorption appears at the wavenumber of 3400 cm −1 the TiO2 grown on the FTO and ITO conducting glass substrates. The weak absorption of 3400 and 1600 cm −1 is the characteristic absorption of hydroxy (-OH), which may be due to the incomplete hydrolysis of titanium tetrachloride (TiCl4) to generate TiO2 and residual -OH. The characteristic bands at 550 cm −1 are attributed to vibrations of Ti-O in TiO2 nanocrystal. Figure 9a is the ultraviolet-visible absorption spectrograms of four nanoarrays and their band gap diagrams. The homojunction of the TiO2 nanoarrays generated by the horizontally placed FTO and ITO conducting glasses are basically the same; we can see that TiO2-FTO, TiO2-ITO and ITO-HJ absorption wavelength in the ultraviolet region from 400 nm, while TiO2-FTO-HJ has an absorption band edge at the about 750 nm. It can be seen from Figure 9b that the band gap of TiO2-FTO is 3.02 eV, and the band gap of TiO2-ITO, FTO-HJ, ITO-HJ is 3.04 eV, respectively, suggesting that these TiO2 nanostructures may be promising for sensing [28].  It can be seen from the FT-IR spectrum of TiO 2 nanoarrays in Figure 8 that a weak absorption appears at the wavenumber of 3400 cm −1 the TiO 2 grown on the FTO and ITO conducting glass substrates. The weak absorption of 3400 and 1600 cm −1 is the characteristic absorption of hydroxy (-OH), which may be due to the incomplete hydrolysis of titanium tetrachloride (TiCl 4 ) to generate TiO 2 and residual -OH. The characteristic bands at 550 cm −1 are attributed to vibrations of Ti-O in TiO 2 nanocrystal. Figure 9a is the ultraviolet-visible absorption spectrograms of four nanoarrays and their band gap diagrams. The homojunction of the TiO 2 nanoarrays generated by the horizontally placed FTO and ITO conducting glasses are basically the same; we can see that TiO 2 -FTO, TiO 2 -ITO and ITO-HJ absorption wavelength in the ultraviolet region from 400 nm, while TiO 2 -FTO-HJ has an absorption band edge at the about 750 nm. It can be seen from Figure 9b that the band gap of TiO 2 -FTO is 3.02 eV, and the band gap of TiO 2 -ITO, FTO-HJ, ITO-HJ is 3.04 eV, respectively, suggesting that these TiO 2 nanostructures may be promising for sensing [28].
Coatings 2020, 10, 409 7 of 12 3.1.2. The Structure of the TiO2 Nanoarray X-ray diffraction (XRD) characterization is presented in Figure 7. It can be seen that the TiO2 with four morphologies have crystal faces of (110), (101), (002), (301) and (112), which indicates that the crystal structures of TiO2-FTO, TiO2-ITO, TiO2-FTO-HJ and TiO2-ITO-HJ are tetragonal rutile phase [27]. The (101) diffraction peak of TiO2 grown on FTO conducting glass substrate is the strongest and sharpest, which suggests that the structure order degree of TiO2-FTO was improved by FTO [26,27]. It can be seen from the FT-IR spectrum of TiO2 nanoarrays in Figure 8 that a weak absorption appears at the wavenumber of 3400 cm −1 the TiO2 grown on the FTO and ITO conducting glass substrates. The weak absorption of 3400 and 1600 cm −1 is the characteristic absorption of hydroxy (-OH), which may be due to the incomplete hydrolysis of titanium tetrachloride (TiCl4) to generate TiO2 and residual -OH. The characteristic bands at 550 cm −1 are attributed to vibrations of Ti-O in TiO2 nanocrystal. Figure 9a is the ultraviolet-visible absorption spectrograms of four nanoarrays and their band gap diagrams. The homojunction of the TiO2 nanoarrays generated by the horizontally placed FTO and ITO conducting glasses are basically the same; we can see that TiO2-FTO, TiO2-ITO and ITO-HJ absorption wavelength in the ultraviolet region from 400 nm, while TiO2-FTO-HJ has an absorption band edge at the about 750 nm. It can be seen from Figure 9b that the band gap of TiO2-FTO is 3.02 eV, and the band gap of TiO2-ITO, FTO-HJ, ITO-HJ is 3.04 eV, respectively, suggesting that these TiO2 nanostructures may be promising for sensing [28].   The gas sensing performance diagram of TiO2-FTO-HJ, TiO2-ITO-HJ, TiO2-FTO and TiO2-ITO to TATP vapors was evaluated under simulated natural light [29]. One can see from Figure 10a that the response of TiO2-FTO-HJ to TATP vapors is nearly three times as strong as the response of TiO2 -ITO-HJ to TATP. TiO2-FTO and TiO2-ITO also respond to TATP vapors, but the response is weak compared with that of homojunction structure. As shown in Figure 10b, the responses of TiO2-FTO-HJ, TiO2 -ITO-HJ, TiO2-FTO and TiO2-ITO to TATP vapors were about 67%, 23%, 11% and 7%, respectively. Moreover, TiO2-FTO-HJ showed a quick response time to TATP of 7.2 s and a recovery time of 4.9 s (Figure 10b). This can be attributed to the homojunctions formation between the urchin-shaped TiO2 and TiO2 nanoarrays, which may be beneficial in promoting the efficient separation of photogenerated charges. As a demonstration, E-field intensity distributions of TiO2 homojunction and TiO2 nanoarrays were simulated by finite element method. Figure 11a shows the electric field distributions of TiO2 homojunction. The hot spot area can be found between the interface of urchin-shaped TiO2 nanosphere and TiO2 nanoarrays. Compared with the simulation results of the urchin-free nanosphere shown in Figure 11b, the strength of the electromagnetic fields of the TiO2 homojunction at the hot spot area increase at least six orders of magnitude with respect to the TiO2 nanoarrays. This demonstrates that the interface of the urchin-shaped TiO2 nanosphere and TiO2 nanoarrays can enhance the localized electromagnetic fields intensity to a certain extent under the simulated natural light. Thus, the photoelectrons accumulate at the interface of the homojunction to provide photocatalysis active site to reduce TATP to acetone and hydrogen peroxide (Figure 11c).  [29]. One can see from Figure 10a that the response of TiO 2 -FTO-HJ to TATP vapors is nearly three times as strong as the response of TiO 2 -ITO-HJ to TATP. TiO 2 -FTO and TiO 2 -ITO also respond to TATP vapors, but the response is weak compared with that of homojunction structure. As shown in Figure 10b, the responses of TiO 2 -FTO-HJ, TiO 2 -ITO-HJ, TiO 2 -FTO and TiO 2 -ITO to TATP vapors were about 67%, 23%, 11% and 7%, respectively. Moreover, TiO 2 -FTO-HJ showed a quick response time to TATP of 7.2 s and a recovery time of 4.9 s (Figure 10b). This can be attributed to the homojunctions formation between the urchin-shaped TiO 2 and TiO 2 nanoarrays, which may be beneficial in promoting the efficient separation of photogenerated charges. The gas sensing performance diagram of TiO2-FTO-HJ, TiO2-ITO-HJ, TiO2-FTO and TiO2-ITO to TATP vapors was evaluated under simulated natural light [29]. One can see from Figure 10a that the response of TiO2-FTO-HJ to TATP vapors is nearly three times as strong as the response of TiO2 -ITO-HJ to TATP. TiO2-FTO and TiO2-ITO also respond to TATP vapors, but the response is weak compared with that of homojunction structure. As shown in Figure 10b, the responses of TiO2-FTO-HJ, TiO2 -ITO-HJ, TiO2-FTO and TiO2-ITO to TATP vapors were about 67%, 23%, 11% and 7%, respectively. Moreover, TiO2-FTO-HJ showed a quick response time to TATP of 7.2 s and a recovery time of 4.9 s (Figure 10b). This can be attributed to the homojunctions formation between the urchin-shaped TiO2 and TiO2 nanoarrays, which may be beneficial in promoting the efficient separation of photogenerated charges. As a demonstration, E-field intensity distributions of TiO2 homojunction and TiO2 nanoarrays were simulated by finite element method. Figure 11a shows the electric field distributions of TiO2 homojunction. The hot spot area can be found between the interface of urchin-shaped TiO2 nanosphere and TiO2 nanoarrays. Compared with the simulation results of the urchin-free nanosphere shown in Figure 11b, the strength of the electromagnetic fields of the TiO2 homojunction at the hot spot area increase at least six orders of magnitude with respect to the TiO2 nanoarrays. This demonstrates that the interface of the urchin-shaped TiO2 nanosphere and TiO2 nanoarrays can enhance the localized electromagnetic fields intensity to a certain extent under the simulated natural light. Thus, the photoelectrons accumulate at the interface of the homojunction to provide photocatalysis active site to reduce TATP to acetone and hydrogen peroxide (Figure 11c). As a demonstration, E-field intensity distributions of TiO 2 homojunction and TiO 2 nanoarrays were simulated by finite element method. Figure 11a shows the electric field distributions of TiO 2 homojunction. The hot spot area can be found between the interface of urchin-shaped TiO 2 nanosphere and TiO 2 nanoarrays. Compared with the simulation results of the urchin-free nanosphere shown in Figure 11b, the strength of the electromagnetic fields of the TiO 2 homojunction at the hot spot area increase at least six orders of magnitude with respect to the TiO 2 nanoarrays. This demonstrates that the interface of the urchin-shaped TiO 2 nanosphere and TiO 2 nanoarrays can enhance the localized electromagnetic fields intensity to a certain extent under the simulated natural light. Thus, the photoelectrons accumulate at the interface of the homojunction to provide photocatalysis active site to reduce TATP to acetone and hydrogen peroxide (Figure 11c). Ammonium nitrate (AN), urea and sulfur (S) are also employed as improvised explosives or explosive raw materials. The sensing properties of the TiO2-FTO-HJ toward different saturated AN, urea and S vapors are depicted in Figure 12. The response of TiO2-FTO-HJ to AN, urea and S vapor is about 22%, 26% and 9%, respectively, which is lower than the response to TATP. The response time of TiO2-FTO-HJ to AN, urea and S vapors is about 11 s, 24 s and 12 s, while the recovery time is 12 s, 4 s and 3 s, respectively. Among these improvised explosives, AN, urea and S are relatively stable. However, the electron transfer process is thermodynamically and kinetically favorable for TATP reductive decomposition. Thus, TiO2-FTO-HJ shows selectivity to TATP, and this result reveals that TiO2-FTO-HJ is a potential candidate for TATP sensors. Ammonium nitrate (AN), urea and sulfur (S) are also employed as improvised explosives or explosive raw materials. The sensing properties of the TiO 2 -FTO-HJ toward different saturated AN, urea and S vapors are depicted in Figure 12. The response of TiO 2 -FTO-HJ to AN, urea and S vapor is about 22%, 26% and 9%, respectively, which is lower than the response to TATP. The response time of TiO 2 -FTO-HJ to AN, urea and S vapors is about 11 s, 24 s and 12 s, while the recovery time is 12 s, 4 s and 3 s, respectively. Among these improvised explosives, AN, urea and S are relatively stable. However, the electron transfer process is thermodynamically and kinetically favorable for TATP reductive decomposition. Thus, TiO 2 -FTO-HJ shows selectivity to TATP, and this result reveals that TiO 2 -FTO-HJ is a potential candidate for TATP sensors.

Conclusion
The TiO2 nanoarrays and sea urchin-like TiO2-covered TiO2 nanoarray epitaxial were grown on FTO and ITO conductive glass using a simple one step hydrothermal method. For the TiO2 nanoarrays grown on the FTO and ITO conducting glasses, when they were placed horizontally, the part that was in contact with the conducting glass was more orderly and uniform than when

Conclusions
The TiO 2 nanoarrays and sea urchin-like TiO 2 -covered TiO 2 nanoarray epitaxial were grown on FTO and ITO conductive glass using a simple one step hydrothermal method. For the TiO 2 nanoarrays grown on the FTO and ITO conducting glasses, when they were placed horizontally, the part that was in contact with the conducting glass was more orderly and uniform than when vertically placed. In addition, for the nanoarrays that used FTO conducting glass as the substrate, the nanoarrays were more orderly and uniform than those using ITO conducting glass as the substrate. The crystal structure of the homojunction of TiO 2 nanoarrays grown on conducting glass placed horizontally was rutile. Among the four kinds of TiO 2 nanostructure, TiO 2 -FTO-HJ showed excellent response to TATP vapors, reaching 67%, compared with the performances of TiO 2 -ITO-HJ (23%), TiO 2 -FTO (11%), and TiO 2 -ITO (7%) with respect to TATP. The response speed and recovery speed of TiO 2 -FTO-HJ to TATP were relatively fast, with a response time of 7.2 s and a recovery time of 4.6 s. The TiO 2 -FTO-HJ also showed high selectivity to TATP among ammonium nitrate, urea and sulfur, which are common homemade explosives raw materials.