# CTAB-Assisted Hydrothermal Synthesis of WO3 Hierarchical Porous Structures and Investigation of Their Sensing Properties

Authors: Dan Meng; Guosheng Wang; Xiaoguang San; Yanbai Shen; Guodong Zhao; Yajing Zhang; Fanli Meng
Journal: Journal of Nanomaterials
 (2015)

---

## Abstract

WO3 hierarchical porous structures were successfully synthesized via cetyltrimethylammonium bromide- (CTAB-) assisted hydrothermal method. The structure and morphology were investigated using scanning electron microscope, X-ray diffractometer, transmission electron microscopy, X-ray photoelectron spectra, Brunauer-Emmett-Teller nitrogen adsorption-desorption, and thermogravimetry and differential thermal analysis. The result demonstrated that WO3 hierarchical porous structures with an orthorhombic structure were constructed by a number of nanoparticles about 50–100 nm in diameters. The H2 gas sensing measurements showed that well-defined WO3 hierarchical porous structures with a large specific surface area exhibited the higher sensitivity compared with products without CTAB at all operating temperatures. Moreover, the reversible and fast response to H2 gas and good selectivity were obtained. The results indicated that the WO3 hierarchical porous structures are promising materials for gas sensors.


---

## Body

## 1. Introduction

Metal oxide semiconductors are widely used for the solar cells, photocatalysts, sensors, and so forth [1–4]. It is well known that the physical and chemical properties of most metal oxides are strongly dependent on their grain size, morphology, surface areas, and structure [5, 6]. Therefore, controlling these factors of the metal oxide materials is one of the most challenging issues in order to achieve reliable performance. Porous materials have attracted considerable attention because they have potentials in various promising applications owing to their higher specific area and an effective gas diffusion path via well-aligned porous structures [7–10]. Great efforts have been made to explore new synthesis methods and control the formation of porous structures to satisfy certain applications.Tungsten oxide (WO3), an n-type semiconductor, has been widely investigated due to its unique optical and electrical properties. Therefore, it is regarded as a promising materials for gas sensors, photocatalysts, electrode materials for secondary batteries, solar energy devices, and so forth [11–15]. For these applications, great interest arises in synthesis of high surface area WO3 nano/micro-structures such as nanowires [16], nanoplates [17], and hierarchical architectures [18] to obtain enhanced performance. Recently, WO3 porous structures with various morphologies have drawn extensive research attention since porous materials with high surface area usually exhibit unique chemical and physical properties different from solid structures, which make them critically important in technological applications [19]. Therefore, the controlling fabrication of ordered WO3 porous structures through a facile, mild, and low cost method still has importantly scientific and practical significance.In this paper, we reported a simple hydrothermal synthesis of WO3 hierarchical porous structures constructed by nanoparticles, using sodium tungstate (Na2WO4·2H2O) as a tungsten source and CTAB as an assistant agent. The morphologies and structures and their H2 gas sensing properties were investigated. The result showed that the sensor fabricated from WO3 porous structures exhibited excellent H2 sensing properties, demonstrating potential of these unique hierarchical porous structures for gas sensor application.


## 2. Experimental

WO3 hierarchical porous structures were synthesized by the hydrothermal method. In a typical procedure, 1.32 g Na2WO4·2H2O was dissolved in 20 mL distilled water under magnetic stirring to get a clear solution. Subsequently, 3 M HCl aqueous solution was slowly dropped into the solution under continuous stirring until the pH value of the solution reached 1. Then 0.8 g CTAB was added into the solution. After stirring 30 min, the mixture was transferred into a 50 mL Teflon-lined stainless autoclave with filling about 80% of the whole volume by mixing distilled water. The autoclave was maintained at 180°C for 12 h and then cooled down to room temperature naturally. The precipitate was collected and washed with distilled water and ethanol for three times, respectively, and dried in an oven at 80°C for 4 h. To observe the effect of CTAB, the product without assistance of CTAB was synthesized maintaining the same condition. Finally, the products were annealed at 400°C in air for 4 h for investigating the crystal structure, morphology, and gas sensing properties. The final product without assistance of CTAB was named as SW, while that with assistance of CTAB was named as SW-CTAB.The obtained products were characterized using an X-ray diffractometer (XRD, PANalytical X’Pert Pro), a field emission scanning electron microscope (FESEM, ZEISS Ultra Plus) equipped with energy dispersive X-ray spectroscopy (EDS), a transmission electron microscopy (TEMJEOL EM002B), an X-ray photoelectron spectra (XPS, JEOL JPS9010MC), and Brunauer-Emmett-Teller (BET) nitrogen adsorption-desorption (TristarII3020M). The pore size distribution was calculated from the adsorption branch of the nitrogen adsorption-desorption isotherms using the Barrett–Joyner–Halenda (BJH) method. Thermogravimetry and differential thermal analysis (TG-DTA) was also carried out using a Shimadzu, DTG-60H apparatus. The sample was heated from room temperature to 800°C at a rate of 10°C/min in air.In order to prepare gas sensors, the obtained products were mixed with ethanol to form a paste, which was then coated onto the outside surface of an alumina tube with a pair of Au electrodes and four Pt wires. A Ni–Cr alloy coil inserted into the tube was used as heater; the temperature of coated tube could be controlled by regulating heating voltage. Then, the sensors were annealed at 350°C for 4 h in ambient air to improve their stability and repeatability. The gas sensing measurements were performed on a static system (WS-30A, Hanwei Electronics Co. Ltd., Henan Province, China) with the constant loop voltage of 5 V. Figure1 shows the schematic diagrams of the sensor and measurement electric circuit. The sensitivity of the sensor is defined as the ratio of the electrical resistance in air (Ra) to the electrical resistance in the mixture of test gas and air (Rg), which is given by the equation S=Ra/Rg.Figure 1
Schematic illustration of the gas sensor and measurement electric circuit (Vh: heating voltage, Vc: circuit voltage, and Vout: signal voltage).


## 3. Results and Discussion

### 3.1. Structure Characterizations

Figure2 shows the TG-DTA curves of the nonannealed SW-CTAB product. It is found that the total weight loss is only 1.1% from room temperature to 400°C, which is attributed to the loss of surface adsorbed water and the combustion of the organics adsorbed on the surface of the product. There was no obvious weight loss between 400°C and 800°C, indicating that all the organics were completely removed. A broad exothermic peak between 400°C and 800°C of the DTA curve is associated with the further crystallization of WO3 [20]. Thus, the annealing temperature for the product was set at the 400°C to maintain the porous structure.Figure 2
TG and DTA curves of the nonannealed SW-CTAB product.The XRD patterns observed for the SW and SW-CTAB products are shown in Figure3. It is clearly seen that all the diffraction peaks of two products are in good agreement with JCPDS cards 71-0131, which could be indexed to orthorhombic crystal structure. The peaks of other impurity phases were not observed in the XRD patterns, indicating the obtained products are pure WO3 structures under the hydrothermal conditions. The strong and sharp diffraction peaks indicate the good crystallinity of the products.Figure 3
XRD patterns of the SW and SW-CTAB products.FESEM images of the SW and SW-CTAB products are shown in Figures4(a)–4(e). Figures 4(a) and 4(b) indicate that SW products are composed of particles with heterogeneous morphology in shape of irregular sphere-like structures and plate-like structures. The size of sphere-like structures is approximately 20–100 nm, while the size of plate-like structures is approximately 50 nm in thickness and 100–500 nm in length. It is interesting that the morphologies of the SW-CTAB products vary dramatically, showing porous structures (Figure 4(c)). Many large pores with around 1–3 μm are observed. The high-magnification FESEM image, as shown in Figure 4(d), reveals that these porous structures consisted of interconnected spherical nanoparticles, which are self-assembled layer by layer and the large pores are bound between the big particles. Carefully observation in Figures 4(e) and 4(f) demonstrates that the particle diameter is in the range of 50–100 nm. The irregular pores and unambiguous grain boundaries between the nanoparticles are obviously observed. The EDS spectrum for the SW and SW-CTAB products shown in Figures 4(g) and 4(h), respectively, indicate that only oxygen and tungsten elements exist in two products with an atomic ratio of nearly 3 : 1.Figure 4
(a)–(e) FESEM images and EDS pattern of the SW and SW-CTAB products: (a) and (b) FESEM images of the SW product, (c)–(e) FESEM images of the SW-CTAB product. (f) TEM image of the SW-CTAB product, (g) and (h) EDS pattern of the SW product and SW-CTAB product, respectively.
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)The above observations indicate that the presence of CTAB is favorable for forming WO3 porous structures. CTAB is a cationic surfactant, which is suitable for scattering, self-assembly and pore-making [21–24]. In the present work, the reason for the formation of the hierarchical porous architectures is most likely due to the interaction between CTAB molecular layers adsorbed on the particle surface and oriented aggregation of nanocrystals. Initially, the tungstate acid (H2WO4·nH2O) was formed rapidly and precipitated from solution after HCl solution was added dropwise into Na2WO4 solution (shown in formula (1)). When CTAB was introduced into aqueous solution, CTAB molecules could adsorb on the surfaces of H2WO4·nH2O tiny particles. During the continuous hydrothermal process, these tiny particles in the presence of CTAB could dissolve, decompose into different shapes of WO3 nuclei, and regrow to nanoparticles through Ostwald ripening process [24]. In this process, the adsorption of CTAB on crystal planes may account for the inhibition of the epitaxy growth of the particles and thus the formation of small sizes nanoparticles. As the reaction went on, these nanoparticles further oriented aggregate with each other to minimize the total surface free energy of the system [25]. The reaction in the solution can be shown below [23, 24]:(1)Na2WO4·2H2O+HCl+H2O⟶H2WO4·nH2O+NaCl(2)H2WO4·nH2O⟶WO3+n+1H2OThe nitrogen adsorption-desorption measurement isotherm and pore size distribution as the inset of the SW and SW-CTAB products are shown in Figure5. According to the IUPAC classification, both SW and SW-CTAB products exhibit type IV form with a type H3 hysteresis loop. The type H3 loops appear at the relative pressure (P/P0) range of 0.8–1.0 and indicted that the pore size is relatively large. The pore size distributions of both SW and SW-CTAB products distribute in the long range of 2–110 nm. The BET surface of SW-CTAB product is 28.3 m2g−1, which is higher than that of SW product (4.5 m2g−1).Figure 5
Nitrogen adsorption-desorption measurement isotherm and the corresponding pore size distribution (inset) of the SW and SW-CTAB products.The typical XPS spectrum for the SW-CTAB product is shown in Figure6. Wide scanning spectrum in Figure 6(a) indicates that the W, O, and C are present in the product and no other impurities are found. Elements W and O belong to the WO3 product and C may be attributed to the sample handling and exposure to the atmosphere prior to XPS measurements. Narrow scan XPS spectra of W 4f and O 1s are shown in Figures 6(b) and 6(c). The well-resolved W 4f doublet peaks are due to spin orbit coupling of electrons. Peaks locating at 35.46 and 37.58 eV correspond to W 4f7/2 and W 4f5/2, respectively, agreeing well with the W6+ state from WO3. The O 1s peak at 529.81 eV corresponds to the lattice oxygen O2− bonded to W. The above observation demonstrates that the product is close to the chemical stoichiometry of WO3 [22, 26].Figure 6
XPS spectrum for the SW-CTAB product: (a) wide scan spectrum, (b) W 4f spectra, and (c) O 1s spectra.
(a)
(b)
(c)


### 3.2. Sensing Properties of H2

Consider that the WO3 hierarchical porous structures possess a large active surface area and fast gas diffusion, which are beneficial for gas sensor, photochemical device, and catalysis applications. Here, the H2 sensing properties were investigated.The sensitivity of the sensors made of SW and SW-CTAB products upon exposure to 1000 ppm H2 gas is shown in Figure 7 as a function of the operating temperature. It is obvious that their sensing response largely depend on operating temperature. The highest sensitivity for the SW product is 12.8 at 300°C, while it is 26.2 for SW-CTAB product at 250°C. In addition, the sensor made of hierarchical porous structures obtained with CTAB exhibits the higher sensitivity to H2 gas at almost all the operating temperatures, indicating that the porous structures with many pores and intervals are very good candidate for gas sensor.Figure 7
Sensitivity upon exposure to 1000 ppm H2 gas at different operating temperatures.The temporal responses of the sensors made of SW and SW-CTAB products upon exposure to 1000 ppm H2 gas at different operating temperatures are shown in Figure 8. The resistance of both sensors decreases rapidly upon exposure to H2 gas and quickly recovers to its initial value when gas is out, at high temperature of 300°C. However, response and recovery rate are slow at a low temperature, especially for the SW product, and the resistant can not recover to the initial value at 100°C. Here, the response time and recovery time are defined as the time required for the resistance to reach 90% of the equilibrium value after detected gas is introduced, and the time necessary for the sensor to recover 90% of its initial resistance, respectively. With increasing the temperature, the response time and response time for the sensor made of SW-CTAB product range from 136 to 18 s and 920 to 76 s, respectively, while they range from 176 to 56 s and 1020 to 104 s, respectively, for the sensor made of SW product. Such result suggests that the sensor based on porous structures exhibits quicker response and recover characteristics, indicating the good response and recover performance.Figure 8
Temporal responses upon exposure to 1000 ppm H2 gas at different operating temperatures. (a) SW (without CTAB) and (b) SW-CTAB (with CTAB).
(a)
SW (without CTAB)
(b)
SW-CTAB (with CTAB)The gas response and recovery behavior of the sensor upon exposure to different concentration H2 (500–10000 ppm) at 250°C are shown in Figures 9(a) and 9(b). It is can be seen that both sensors exhibit good response/recovery characteristics to H2 gas pulses at different concentrations, indicating excellent reversibility and stability of the sensors. Moreover, the response and recovery rate of the SW-CTAB product are faster than those of the SW product, which can be ascribed to the hierarchical porous structures. The sensitivity as a function of H2 concentration is shown in Figure 9(c). It is noted that the sensitivity increases as H2 concentration increases for both sensors. In addition, the sensor made of the SW-CTAB product shows the higher sensitivity than the sensor made of the SW product at all H2 concentrations.Figure 9
Temporal responses upon exposure to 500–10000 ppm H2 gas measured at 250°C. (a) SW (without CTAB) and (b) SW-CTAB (with CTAB). (c) Relationship between the sensitivity and H2 concentration at 250°C.
(a)
SW (without CTAB)
(b)
SW-CTAB (with CTAB)
(c)Gas sensing responses of the sensors made of WO3 porous structures obtained with CTAB assistant to different volatile gases under concentration of 100 ppm at 250°C were measured, as shown in Figure 10. It clearly shows that the sensor is more sensitive to 1000 ppm H2 than to other interference gases, implying that selective detecting of H2 is possible.Figure 10
Selectivity of the sensor made of the SW-CTAB product exposure to different gases at 250°C. Here, the concentration of volatile gases is 100 ppm, while it is 1000 ppm for H2 gas.WO3 is a typical n-type semiconductor. Its gas sensing mechanism belongs to the surface-controlled type, and the change of resistance is dependent on the species and the amount of chemisorbed species on the surface [11]. A possible sensing mechanism is proposed in Figure 11. The oxygen molecules from the ambient atmosphere are initially adsorbed on the surface of the WO3 grain in the form of O2-, O-, and O2-, depending on the ambient temperature [27]. Thus, every WO3 particle has a depletion layer near its surface, and many boundaries are formed between particles, leading to high resistance state in air ambient. When WO3 are exposed to a reducing gas such as hydrogen, these gas molecules could react with surface oxygen species by H2(gas) + 1/2O2-(ads) → H2O(ads) + e- and H2(gas) + O-(ads) → H2O(ads) + e- [28]. This process releases the electrons back to WO3 and barrier height at the grain boundaries decreases. As a result, the resistance of WO3 particles decreases, reflecting a sensing property. The hierarchical porous structures with a large surface and high porosity may enhance the probability of absorbing target gases and providing an effective gas diffusion path via well-aligned porous structures. Therefore, the WO3 hierarchical porous structure sensor exhibits excellent sensing properties.Figure 11
Schematic illustration of gas sensing mechanism.


## 3.1. Structure Characterizations

Figure2 shows the TG-DTA curves of the nonannealed SW-CTAB product. It is found that the total weight loss is only 1.1% from room temperature to 400°C, which is attributed to the loss of surface adsorbed water and the combustion of the organics adsorbed on the surface of the product. There was no obvious weight loss between 400°C and 800°C, indicating that all the organics were completely removed. A broad exothermic peak between 400°C and 800°C of the DTA curve is associated with the further crystallization of WO3 [20]. Thus, the annealing temperature for the product was set at the 400°C to maintain the porous structure.Figure 2
TG and DTA curves of the nonannealed SW-CTAB product.The XRD patterns observed for the SW and SW-CTAB products are shown in Figure3. It is clearly seen that all the diffraction peaks of two products are in good agreement with JCPDS cards 71-0131, which could be indexed to orthorhombic crystal structure. The peaks of other impurity phases were not observed in the XRD patterns, indicating the obtained products are pure WO3 structures under the hydrothermal conditions. The strong and sharp diffraction peaks indicate the good crystallinity of the products.Figure 3
XRD patterns of the SW and SW-CTAB products.FESEM images of the SW and SW-CTAB products are shown in Figures4(a)–4(e). Figures 4(a) and 4(b) indicate that SW products are composed of particles with heterogeneous morphology in shape of irregular sphere-like structures and plate-like structures. The size of sphere-like structures is approximately 20–100 nm, while the size of plate-like structures is approximately 50 nm in thickness and 100–500 nm in length. It is interesting that the morphologies of the SW-CTAB products vary dramatically, showing porous structures (Figure 4(c)). Many large pores with around 1–3 μm are observed. The high-magnification FESEM image, as shown in Figure 4(d), reveals that these porous structures consisted of interconnected spherical nanoparticles, which are self-assembled layer by layer and the large pores are bound between the big particles. Carefully observation in Figures 4(e) and 4(f) demonstrates that the particle diameter is in the range of 50–100 nm. The irregular pores and unambiguous grain boundaries between the nanoparticles are obviously observed. The EDS spectrum for the SW and SW-CTAB products shown in Figures 4(g) and 4(h), respectively, indicate that only oxygen and tungsten elements exist in two products with an atomic ratio of nearly 3 : 1.Figure 4
(a)–(e) FESEM images and EDS pattern of the SW and SW-CTAB products: (a) and (b) FESEM images of the SW product, (c)–(e) FESEM images of the SW-CTAB product. (f) TEM image of the SW-CTAB product, (g) and (h) EDS pattern of the SW product and SW-CTAB product, respectively.
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)The above observations indicate that the presence of CTAB is favorable for forming WO3 porous structures. CTAB is a cationic surfactant, which is suitable for scattering, self-assembly and pore-making [21–24]. In the present work, the reason for the formation of the hierarchical porous architectures is most likely due to the interaction between CTAB molecular layers adsorbed on the particle surface and oriented aggregation of nanocrystals. Initially, the tungstate acid (H2WO4·nH2O) was formed rapidly and precipitated from solution after HCl solution was added dropwise into Na2WO4 solution (shown in formula (1)). When CTAB was introduced into aqueous solution, CTAB molecules could adsorb on the surfaces of H2WO4·nH2O tiny particles. During the continuous hydrothermal process, these tiny particles in the presence of CTAB could dissolve, decompose into different shapes of WO3 nuclei, and regrow to nanoparticles through Ostwald ripening process [24]. In this process, the adsorption of CTAB on crystal planes may account for the inhibition of the epitaxy growth of the particles and thus the formation of small sizes nanoparticles. As the reaction went on, these nanoparticles further oriented aggregate with each other to minimize the total surface free energy of the system [25]. The reaction in the solution can be shown below [23, 24]:(1)Na2WO4·2H2O+HCl+H2O⟶H2WO4·nH2O+NaCl(2)H2WO4·nH2O⟶WO3+n+1H2OThe nitrogen adsorption-desorption measurement isotherm and pore size distribution as the inset of the SW and SW-CTAB products are shown in Figure5. According to the IUPAC classification, both SW and SW-CTAB products exhibit type IV form with a type H3 hysteresis loop. The type H3 loops appear at the relative pressure (P/P0) range of 0.8–1.0 and indicted that the pore size is relatively large. The pore size distributions of both SW and SW-CTAB products distribute in the long range of 2–110 nm. The BET surface of SW-CTAB product is 28.3 m2g−1, which is higher than that of SW product (4.5 m2g−1).Figure 5
Nitrogen adsorption-desorption measurement isotherm and the corresponding pore size distribution (inset) of the SW and SW-CTAB products.The typical XPS spectrum for the SW-CTAB product is shown in Figure6. Wide scanning spectrum in Figure 6(a) indicates that the W, O, and C are present in the product and no other impurities are found. Elements W and O belong to the WO3 product and C may be attributed to the sample handling and exposure to the atmosphere prior to XPS measurements. Narrow scan XPS spectra of W 4f and O 1s are shown in Figures 6(b) and 6(c). The well-resolved W 4f doublet peaks are due to spin orbit coupling of electrons. Peaks locating at 35.46 and 37.58 eV correspond to W 4f7/2 and W 4f5/2, respectively, agreeing well with the W6+ state from WO3. The O 1s peak at 529.81 eV corresponds to the lattice oxygen O2− bonded to W. The above observation demonstrates that the product is close to the chemical stoichiometry of WO3 [22, 26].Figure 6
XPS spectrum for the SW-CTAB product: (a) wide scan spectrum, (b) W 4f spectra, and (c) O 1s spectra.
(a)
(b)
(c)


## 3.2. Sensing Properties of H2

Consider that the WO3 hierarchical porous structures possess a large active surface area and fast gas diffusion, which are beneficial for gas sensor, photochemical device, and catalysis applications. Here, the H2 sensing properties were investigated.The sensitivity of the sensors made of SW and SW-CTAB products upon exposure to 1000 ppm H2 gas is shown in Figure 7 as a function of the operating temperature. It is obvious that their sensing response largely depend on operating temperature. The highest sensitivity for the SW product is 12.8 at 300°C, while it is 26.2 for SW-CTAB product at 250°C. In addition, the sensor made of hierarchical porous structures obtained with CTAB exhibits the higher sensitivity to H2 gas at almost all the operating temperatures, indicating that the porous structures with many pores and intervals are very good candidate for gas sensor.Figure 7
Sensitivity upon exposure to 1000 ppm H2 gas at different operating temperatures.The temporal responses of the sensors made of SW and SW-CTAB products upon exposure to 1000 ppm H2 gas at different operating temperatures are shown in Figure 8. The resistance of both sensors decreases rapidly upon exposure to H2 gas and quickly recovers to its initial value when gas is out, at high temperature of 300°C. However, response and recovery rate are slow at a low temperature, especially for the SW product, and the resistant can not recover to the initial value at 100°C. Here, the response time and recovery time are defined as the time required for the resistance to reach 90% of the equilibrium value after detected gas is introduced, and the time necessary for the sensor to recover 90% of its initial resistance, respectively. With increasing the temperature, the response time and response time for the sensor made of SW-CTAB product range from 136 to 18 s and 920 to 76 s, respectively, while they range from 176 to 56 s and 1020 to 104 s, respectively, for the sensor made of SW product. Such result suggests that the sensor based on porous structures exhibits quicker response and recover characteristics, indicating the good response and recover performance.Figure 8
Temporal responses upon exposure to 1000 ppm H2 gas at different operating temperatures. (a) SW (without CTAB) and (b) SW-CTAB (with CTAB).
(a)
SW (without CTAB)
(b)
SW-CTAB (with CTAB)The gas response and recovery behavior of the sensor upon exposure to different concentration H2 (500–10000 ppm) at 250°C are shown in Figures 9(a) and 9(b). It is can be seen that both sensors exhibit good response/recovery characteristics to H2 gas pulses at different concentrations, indicating excellent reversibility and stability of the sensors. Moreover, the response and recovery rate of the SW-CTAB product are faster than those of the SW product, which can be ascribed to the hierarchical porous structures. The sensitivity as a function of H2 concentration is shown in Figure 9(c). It is noted that the sensitivity increases as H2 concentration increases for both sensors. In addition, the sensor made of the SW-CTAB product shows the higher sensitivity than the sensor made of the SW product at all H2 concentrations.Figure 9
Temporal responses upon exposure to 500–10000 ppm H2 gas measured at 250°C. (a) SW (without CTAB) and (b) SW-CTAB (with CTAB). (c) Relationship between the sensitivity and H2 concentration at 250°C.
(a)
SW (without CTAB)
(b)
SW-CTAB (with CTAB)
(c)Gas sensing responses of the sensors made of WO3 porous structures obtained with CTAB assistant to different volatile gases under concentration of 100 ppm at 250°C were measured, as shown in Figure 10. It clearly shows that the sensor is more sensitive to 1000 ppm H2 than to other interference gases, implying that selective detecting of H2 is possible.Figure 10
Selectivity of the sensor made of the SW-CTAB product exposure to different gases at 250°C. Here, the concentration of volatile gases is 100 ppm, while it is 1000 ppm for H2 gas.WO3 is a typical n-type semiconductor. Its gas sensing mechanism belongs to the surface-controlled type, and the change of resistance is dependent on the species and the amount of chemisorbed species on the surface [11]. A possible sensing mechanism is proposed in Figure 11. The oxygen molecules from the ambient atmosphere are initially adsorbed on the surface of the WO3 grain in the form of O2-, O-, and O2-, depending on the ambient temperature [27]. Thus, every WO3 particle has a depletion layer near its surface, and many boundaries are formed between particles, leading to high resistance state in air ambient. When WO3 are exposed to a reducing gas such as hydrogen, these gas molecules could react with surface oxygen species by H2(gas) + 1/2O2-(ads) → H2O(ads) + e- and H2(gas) + O-(ads) → H2O(ads) + e- [28]. This process releases the electrons back to WO3 and barrier height at the grain boundaries decreases. As a result, the resistance of WO3 particles decreases, reflecting a sensing property. The hierarchical porous structures with a large surface and high porosity may enhance the probability of absorbing target gases and providing an effective gas diffusion path via well-aligned porous structures. Therefore, the WO3 hierarchical porous structure sensor exhibits excellent sensing properties.Figure 11
Schematic illustration of gas sensing mechanism.


## 4. Conclusions

In summary, high-performance WO3 hierarchical porous structures were synthesized by hydrothermal process via CTAB as surfactant. These WO3 porous structures with an orthorhombic structure were constructed by a number of nanoparticles about 50–100 nm in diameters. The H2 gas sensing properties were investigated. The result demonstrated that well-defined WO3 hierarchical porous structures with large specific surface area exhibited the higher responses compared with products without CTAB at all operating temperatures. Moreover, the reversible and fast response to H2 gas and good selectivity were obtained. These excellent sensing properties of WO3 hierarchical porous structures indicate a potential application for fabrication high-performance gas sensors.



---

*Source: 393205-2015-11-30.xml*