Nanostructured Resistive-Based Vanadium Oxide Gas Sensors

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1		Ali Mirzaei	--	2824	2023-07-20 16:12:05	\|
2	format change	Peter Tang	Meta information modification	2824	2023-07-21 09:10:53	\| \|
3	format change	Peter Tang	Meta information modification	2824	2023-07-21 09:11:20	\|

This entry is adapted from the peer-reviewed paper 10.3390/chemosensors8040105

Vanadium pentoxide (V₂O₅) is a transition metal oxide with features such as high availability, good catalytic activity, unique electrical properties and high conductivity which are appropriate for gas sensing applications.

V2O5 gas sensor morphology sensing mechanism toxic gas

1. Introduction

Vanadium (V) is a well-known transition metal which can form different oxides. The principal oxides of vanadium are vanadium monoxide (VO, violet color), vanadium sesquioxide (V₂O₃, green color), vanadium dioxide (VO₂, blue color), and vanadium pentoxide (V₂O₅, yellow color). Presence of oxygen vacancies leads to formation other oxides such as V₃O₇, V₄O₉, and V₆O₁₃ (a mixture of V⁵⁺ and V⁴⁺), and a series of oxides such as V₆O₁₁, V₇O₁₃, and V₈O₁₅ (a mixture of V⁴⁺ and V³⁺). In general, the mixing phases can be categorized into two series of phases namely the Magnéli phase (V_nO_2n-1) and the Wadsley phase V_nO_2n+1 ^[1]^[2]. Among different phases, V₂O₅ is thermodynamically the most stable oxide and it exist in different polymorphs namely the most stable α-V₂O₅ (orthorhombic), metastable β-V₂O₅ (tetragonal or monoclinic), γ-V₂O₅ (orthorhombic) and δ-V₂O₅ (monoclinic) ^[3]. Each polymorph is stable at a temperature and pressure range. For example, β-V₂O₅ is stable at high pressure and temperatures ^[4].

The orthorhombic V₂O₅ has a layered structure and it is comprised of the distorted polyhedra of six oxygen atoms which form octahedral polyhedra with central V atoms ^[5]. There are three different oxygen positions in the V₂O₅ crystal structure. The VO₆ octahedra are linked, sharing edges through the chain (O_c) and corners via the bridging oxygens (O_b). Two vanadyl oxygen atoms (O_v) form the vertices of the octahedra along the c-axis ^[6].

V₂O₅ is highly abundant in nature, it has low price and has several oxidation states ^[7]^[8]. Accordingly, due to its relatively open layered structure and its unique properties, V₂O₅ has been used in different applications such as water splitting ^[9], field effect transistors ^[10]^[11], supercapacitors ^[12], IR detectors ^[13], photodetectors ^[14], UV sensors ^[15], optical sensors ^[16], amprometric gas sensors ^[17], potentiometric sensors ^[18] electrochemical sensors ^[19]^[20], cataluminescence sensors ^[21], resistance gas sensors ^[22]^[23], gasochromic sensors ^[24] and humidity sensors ^[25].

V₂O₅ with an n-type semiconducting behavior, has a relatively high conductivity (0.5 S·cm⁻¹) at room temperature ^[26]. At high temperatures, stoichiometric V₂O₅ spontaneously converts to V₂O_5−x as follows:

Values of “x” vary depending on annealing temperature and oxygen partial pressure during synthesis. As a result, oxygen vacancies form in the oxygen sub-lattice and n-type semiconducting is induced. To be neutral, some V⁵⁺ ions will be reduced to V⁴⁺ ions. Electrical conductivity in V₂O_5−x is due to jumping (hopping) of the electrons from V⁴⁺ ions to the neighboring V⁵⁺ ions ^[26].

Compared with bulk V₂O₅, nanostructured V₂O₅ materials have unique electrical and chemical properties and due to their ultrafine sizes, they offer a high surface area which is extremely beneficial for sensing studies ^[27]^[28]^[29]^[30].

Nowadays gas sensors have become widely used in different areas for detection of toxic, hazardous, explosive and greenhouse gases and vapors ^[31]^[32]. There are many types of gas sensors. However, resistive-based gas sensors using metal oxides are the most widely used gas sensors due to their unique features such as low price, high sensitivity, high stability, fast dynamics and simple fabrication and operation ^[33]^[34]. In a typical gas sensor, the front side of substrate is equipped with conductive electrodes such as with Pt and its back side is equipped with a heater ^[35].

2. Pristine Nanostructured V₂O₅ Gas Sensors

Pristine V₂O₅ gas sensors with different morphologies have been reported in the literature. The gas sensing characteristics of V₂O₅ hierarchical architectures, especially for hollow spheres are rarely reported in the literature. In this regard, V₂O₅ hollow spheres (500–550 nm in diameter and a shell thickness of 55 nm) were synthesized through a solvothermal route. The hollow spheres were comprised of nanoplates with thicknesses of 50–80 nm and lengths of 70–120 nm. Moreover, for comparison solid nanostructured spheres were fabricated. The maximum responses (R_a/R_g) to trimethylamine (TEA) at 370 °C were 9.7 for V₂O₅ hollow spheres and 3.08 for V₂O₅ solid spheres, respectively. In fact, the hollow sphere hierarchical architecture with a higher surface area offered more adsorption sites for TEA molecules and a higher response for hollow spheres resulted. The sensing mechanism of the sensor to TEA was related to the reduction of V⁵⁺ ions to V⁴⁺ ions in the presence of TEA. Furthermore, based on XPS studies there was a slight shift to lower binding energy values after exposure of the sensor to TEA gas, confirming formation of V⁴⁺ ions. In addition, a color change from yellow to dark blue was observed, further confirming the formation of V⁴⁺ ions. V₂O₅ is an acidic oxide, which is highly suitable for the adsorption of basic molecules, such as TEA and consequently a larger response of the V₂O₅ hollow spheres sensor to TEA resulted ^[36].

Generally, resistive based gas sensors work at high temperatures, which need external heaters and increase the power consumption. Therefore, development of room temperature gas sensors not only solves above problems, but also integration with flexible substrates become easier. Furthermore, possible risk of explosion during sensing of explosive gases such as H₂ gas significantly decreases. Hollow spheres comprising numerous nanocrystals of V₂O₅ as a shell were synthesized by a facile polyol approach for room temperature hydrogen gas sensing. The surface area of hollow spheres was about 356 m²/g and, therefore, it provided a large active surface area for adsorption of target gases. Furthermore, its porous structure led to further enhancement of gas reactions. Furthermore, the sharp corners as well as the edges of the tiny building blocks of hollow spheres were reported as highly active sites for enhancement of the sensing reactions during hydrogen sensing ^[37].

Another room temperature gas sensor was realized from V₂O₅ nanoneedles which were synthesized by a physical vapor deposition method ^[38]. The sensor exhibited a response (R_a/R_g) of 2.37 to 140 ppm acetone at room temperature. The relevant reaction was as follows:

The most energetically favorable gas reaction is that a surface oxygen atom attacks the carbonyl carbon to form a C-O bond. Acetone contains the carbonyl group and because of the greater electronegativity of oxygen; a carbonyl group is a polar functional group and, therefore, it has a larger dipole moment (D = 2.88), relative to other tested gases, leading to the higher response of the gas sensor to acetone.

Trimethylamine (TMA; (CH₃)₃N)) is generated from dead fish and, therefore, the concentration of TMA is an indicator of the freshness of fish ^[39]. Furthermore, exposure to TMA vapor can cause nausea, headaches, and irritation to the eyes ^[40]. In this regard, spherical V₂O₅ hierarchical nanostructures comprised of plenty of nanosheets were produced through a hydrothermal method. The optimal sensor based on spherical V₂O₅ hierarchical nanostructures displayed a response of ~2.8 to 100 ppm TMA along with fast response/recovery times (5/28 s) at 240 °C. The spherical V₂O₅ nanostructures were comprised of numerous monocrystalline nanosheets, and therefore they have a unique three-dimensional hierarchical structure which provided plenty of active sites for gas molecules. Accordingly, the reaction between chemisorbed oxygen ions and TMA molecules, resulted in a decrease in electrical resistance and contributed to the sensor signal.

In addition, in a monocrystalline structure free electrons were able to transfer faster than in a polycrystalline structure, which results in fast response and recovery times of gas sensors and improvement of sensing properties ^[41].

Table 1 presents the gas sensing characteristics of pristine V₂O₅ gas sensors, where different morphologies of V₂O₅ prepared using various methods have been successful for sensing of different gases.

Table 1. Gas sensing properties of pristine V₂O₅ gas sensors.

V₂O₅ Morphology	Synthesis Method	Target Gas	Conc. (ppm)	Response (R_a/R_g) or (R_g/R_a)	T (°C)	Response time/Recovery Time(s)	Ref.
Hollow spheres Solid spheres	Solvothermal	C₃H₉N	500 500	9.7 3.08	370	20/83 45/150	^[36]
Hollow spheres	Chemical synthesis	H₂	200	2.8	RT	50/10	^[37]
Nanoneedles	PVD	C₃H₆O	140	2.35	RT	67/-	^[38]
Hierarchical nanostructures	Hydrothermal	C₃H₉N	10–200	1.13-3.57	240	5/28	^[41]
Flower-like	Hydrothermal	C₃H₉N	5	2.25	200	13/13	^[42]
Nanorods	CVD	NH₃	100	235 *	400	-/-	^[43]
Nanorods	Solvothermal	C₂H₅OH NH₃	500	1.04 1.02	RT	-/-	^[44]
Spherical	Precipitation	C₂H₅OH NH₃	500	1.04 1.06	RT	-/-	^[45]
Flower-like	Hydrothermal	1-butylamine	100	2.6	140	9/49	^[46]
Nanofibers	Electrospinning		9.5	500 *	RT	-/-	^[47]
Flower-like Sheet-like	Hydrothermal		100	3.6 2.8	300	25/14 17/14	^[48]
Nanofibers	Sol–gel	NH₃	2.1	11 *	200	50/350	^[49]
Flower-like	DC sputtering	CH₄	500	11 *	100	206/247	^[50]
Flower-like	Hydrothermal	C₈H₁₀	500	3	300	44/74	^[51]
Nano stars	Hydrothermal	He	300	53 *	RT	9/10	^[52]
Nanorods	Chemical spray pyrolysis	NO₂	100	24.2 *	200	13/140	^[53]
Nanofibers	Chemical spray pyrolysis	C₈H₁₀	100	27	RT	80/50	^[54]
Nanowires	Melt quenching	C₂H₅OH	1000	9.09	330	-/-	^[55]
Thin film	Plasma focus method	H₂	1000	50 *	275	-/-	^[56]
Thin film	Chemical spray pyrolysis	NO₂	100	41 *	200	20/150	^[57]

* Response = $\frac{Δ R}{R a} \times 100$ ; RT: Room temperature; PVD: Physical vapor deposition; CVD: Chemical vapor deposition.

3. Decorated/Doped V₂O₅ Gas Sensors

Based on the above section about pristine V₂O₅ gas sensors, pristine V₂O₅ nanostructures suffer from low sensitivity and selectivity, which hinder their applications for sensing applications ^[58]. Accordingly, different strategies, such as p-n heterojunction formation ^[59], n-n heterojunction formation ^[60]^[61] and noble metal decoration ^[62] have been proposed to enhance their sensing properties.

V₂O₅ decoration is a good strategy to enhance the sensing properties of gas sensors. V₂O₅-decorated α-Fe₂O₃ composite NRs were prepared by an electrospinning technique and they had a high surface area of 30.5 m²/g. The composite exhibited a response (R_a/R_g) of 9 to 100 ppm diethylamine along with good selectivity to diethylamine gas and a fast response time of 2 s at 350 °C ^[63]. Improved sensing performance was related to the formation of V₂O₅-Fe₂O₃ heterojunctions and catalytic effect of V₂O₅ to diethylamine.

Porous silicon (PS) is a good candidate for sensing studies due to its offering of a high surface area and a porous structure. In addition it can be simply prepared by a chemical etching process ^[64]. Therefore, composites between V₂O₅ and PS can be promising for gas sensing studies. In a relevant study, thin V films were decorated on the PS by sputtering at different times of 30 and 60 min and then, the samples were annealed at 600 °C ^[65]. The PS/V₂O₅ NRs structure provided a better response than pristine PS at 25 °C, and the sensor sputtered for 60 min exhibited the highest response of 7.4 to 2 ppm NO₂ gas. Both the PS and V₂O₅ NRs had plenty of dangling bonds, oxygen vacancies and defects, leading to high adsorption of oxygen molecules even at room temperature. In the interfaces between PS and V₂O₅, p-n heterojunctions formed and, upon exposure to NO₂ gas, the significant modulation of electrical resistance in the heterojunctions led to the appearance of a sensing signal.

Graphene and its derivations such as graphene oxide and reduced graphene oxide have high surface areas and unique electrical properties which can be beneficial for gas sensing studies ^[66]^[67]. The initial resistance of the GO is high, limiting its practical applications in pristine form ^[68]^[69]. However, after the reduction GO to RGO, there are some defects, vacancies and functional groups which are useful for gas sensing applications ^[70]. In a relevant study, an RGO surface was decorated with Mn₃O₄ and V₂O₅ NOs via a hydrothermal method for detection of H₂ gas at 30 °C. The sensor showed a high response (ΔR/R_a × 100) of 174% to 50 ppm H₂ gas at room temperature. The sheet-like structure of RGO provided a large surface area for gas sensing reactions. In addition, because of the formation of p-n (RGO-V₂O₅) and p-p (RGO-Mn₃O₄) heterojunctions, significant modulation of resistance in the presence of H₂ occurred, resulting in the generation of a sensing signal ^[71]. In another study, a V₂O₅ film was prepared by a reactive sputtering technique and then, RGO was decorated over the V₂O₅ thin film by a drop casting method for NO₂ sensing studies. The sensor showed a response of 50.7% to 100 ppm NO₂ gas at 150 °C. However, its recovery time was long (778 s). Formation and modulation of the p-n heterojunction at the interface of RGO and V₂O₅ was the main reason for the detection of NO₂ gas. Moreover, the presence of active sites such as oxygen functional groups on the RGO surface improved the sensing response ^[72].

Not only can V₂O₅-decoration be a useful technique to enhance the gas sensing properties, but decoration of other metal oxides or noble metals on the surface of gas sensor can also be a good technique to improve the gas sensing properties of V₂O₅-based gas sensors. A P-type CuO with excellent catalytic activity is extensively used for sensing studies ^[73]. The work function of CuO is 5.3 eV, which is different to that of V₂O₅ (4.7 eV). Therefore, when heterojunctions form between the CuO and V₂O₅, enhanced gas response can be expected. In this context, hollow nanostructures using CuO decorated V₂O₅ nano-strings of pearls were fabricated through an electrospinning method. The V₂O₅/CuO sensors demonstrated a response (R_a/R_g ) of 8.8 to 500 ppm acetone at 440 °C, which was more than three times higher than that of bare V₂O₅ NFs. The improved performance was related to the generation of CuO/V₂O₅ p-n heterojunctions, which provided plenty of resistance modulation sources and upon exposure to acetone gas higher response was resulted ^[74].

Table 2 shows the gas sensing properties of decorated or doped V₂O₅-based gas sensors, where different synthesis methods along with different morphologies and various materials have been reported to realize gas sensors for the sensing of toxic gases.

Table 2. Gas sensing properties of decorated or doped V₂O₅-based gas sensors.

Sensor	Synthesis Method	Target Gas	Conc. (ppm)	Response (R_a/R_g) or (R_g/R_a)	Working Temp. (°C)	Response Time/Recovery Time(s)	Ref.
Pd decorated porous Si/V₂O₅ nanopillars	DC sputtering	NO₂	2	4.5	RT	-/-	^[59]
Ru-decorated layer structure V₂O₅	Hydrothermal	NH₃	130	4 *	RT	~2/~12	^[62]
V₂O₅-decorated α-Fe₂O₃ nanorods	Electrospinning	C₄H₁₁N	300	9	350	2/40	^[63]
V₂O₅ decorated SnO₂ NWs	VLS/ALD	NO₂	200 ppb	3.6	250	-/-	^[75]
Porous Si/V₂O₅ NR composite	Galvanostatic electrochemical etching	NO₂	2	7.4	RT	-/-	^[65]
rGO/Mn₃O₄/V₂O₅ nanocomposite	Hydrothermal	H₂	50	175	RT	82/92	^[71]
Pd-decorated CuO NWs	UV irradiation	H₂S	100	1.962	100	-/-	^[72]
V₂O₅/CuO nano-string of pearls	Electrospinning	C₃H₆O	500	9	440	~40/~100	^[74]
CuO-decorated V₂O₅ NWs	Hydrothermal and wet-deposition	H₂S	23	31.86	220	130/218	^[76]
SnO₂ NP-decorated V₂O₅ NWs	Hydrothermal	C₂H₅OH	1000	1.3	RT	-/-	^[77]
Fe₂O₃ activated V₂O₅ nanotubes	Hydrolysis	C₂H₅OH	1000	2.2	270	-/-	^[78]
TiO₂-decorated V₂O₅ NWs	Hydrothermal	O₃	1.25	2.6 *	300	~180/~180	^[79]
RGO-decorated V₂O₅ thin film	Reactive sputtering and drop casting	NO₂	100	50.7	150	-/-	^[72]
Au NP-decorated V₂O₅	Two-step in-situ reduction of Au and thermal oxidization as V₂O₅	Amines	100	7.5	240	90/35	^[80]
Pd-decorated V₂O₅ thin film	DC magnetron reactive sputtering	H₂	100	5.7	100	~6/14.8	^[81]
V₂O₅- doped SnO₂ NFs	Electrospinning	C₆H₆	25	6.32	325	3/47	^[82]

* Response = $\frac{Δ R}{R a} \times 100$ ; RT: Room temperature; VLS: Vapor-liquid-solid; NR; Nanorod; NP; Nanoparticle; NF; Nanofiber.

4. Nanocomposites/Nanohybrids of V₂O₅ Gas Sensors

Core-shell (C-S) nanocomposites are among the most promising structures for gas sensing studies, as in these structures the interfaces between two different materials are maximized, resulting in significant modulation of electrical resistance upon exposure to target gases ^[83]^[84]^[85]. Fu et al. ^[39], synthesized V₂O₅-TiO₂ core-shell (C-S) NPs for NH₃ studies. For pristine V₂O₅ NPs, the surface area was only ∼16 m²/g with a pore size of 12.9 nm, while the BET surface area of V₂O₅@TiO₂ C-S NPs was greatly increased to ∼151 m²/g, and the average pore size was ∼6.4 nm. Thus, the significant increase in surface area was an advantage for C-S NPs, which directly affected the gas sensing studies. The C-S sensor showed a response (R_a/R_g) of 8.6 to 100 ppm ammonia at 365 °C. Upon intimate contact between the V₂O₅ and TiO₂, electrons moved from TiO₂ to V₂O₅, resulting in the creation of an electron depletion layer on both sides of the TiO₂ shell layer. Upon injection of NH₃ gas into the gas chamber, the electrons released back caused the narrowing of the electron depletion layers which finally modulated the electrical resistances of the gas sensor. Moreover, based on DFT calculations, the NH₃ molecule showed the lowest adsorption energy (−1.04 eV) on the anatase TiO₂ (101) surface, which explained the higher selectivity of the gas sensor to NH₃ among other tested gases. The optimal sensing temperature of the gas sensor was registered at 365 °C. The reactions on the surface of TiO₂ can be shown as follows:

Thus, more electrons can be released when N_xO (x = 1, 2), demonstrating the high response toward NH₃ at elevated temperatures (>300 °C).

Table 3 exhibits the sensing properties of various V₂O₅-based composite gas sensors, where different materials along with various morphologies have been used for sensing of different gases.

Table 3. Gas sensing properties of V₂O₅-based composite gas sensors.

Sensing Material	Synthesis Method	Target Gas	Conc. (Ppm)	Response (R_a/R_g) Or (R_g/R_a)	T (°C)	Response Time/Recovery Time(S)	Ref.
V₂O₅/In₂O₃ core–shells	Hydrothermal	n-propylamine	200	4	190	48/121	^[86]
MoO₃-V₂O₅ thin films	Chemical spray pyrolysis	NO₂	120	80 *	200	118/1182	^[87]
(MoO₃)_0.4(V₂O₅)_0.6 sheet composite	Chemical spray pyrolysis	NO₂	100	115	200	39/453	^[88]
Au/V₂O₅/CuWO₄ composite	Hydrothermal	NH₃	5	2.7	150	35/33	^[89]
SnO₂/V₂O₅ composite	Sol-gel	C₆H₆	200	10.5	275	-/-	^[90]
V₂O₅/polyvinyl acetate NF composite	Electrospinning	NH₃	0.8	6 *	260	-/-	^[91]
V₂O₅/ZnV₂O₆ nanobelt composite	Chemical route	C₂H₅OH	2000	16.5	240	-/-	^[92]
TiO₂/V₂O₅ NF composite	Electrospinning	C₂H₅OH	100	24.6	350	6/7	^[93]
ZnO/V₂O₅ thin films	Spray pyrolysis	C₇H₈	400	2.3	27	23/28	^[94]

* Response = $\frac{Δ R}{R a} \times 100$ .

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Vahid Amiri

Hossein Roshan

Ali Mirzaei

Mohammad Hossein Sheikhi

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Update Date: 21 Jul 2023

Table of Contents

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1. Introduction

2. Pristine Nanostructured V₂O₅ Gas Sensors

3. Decorated/Doped V₂O₅ Gas Sensors

4. Nanocomposites/Nanohybrids of V₂O₅ Gas Sensors

References

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1. Introduction

2. Pristine Nanostructured V2O5 Gas Sensors

3. Decorated/Doped V2O5 Gas Sensors

4. Nanocomposites/Nanohybrids of V2O5 Gas Sensors

References

2. Pristine Nanostructured V₂O₅ Gas Sensors

3. Decorated/Doped V₂O₅ Gas Sensors

4. Nanocomposites/Nanohybrids of V₂O₅ Gas Sensors