- Nano Express
- Open Access
Sensitive Cross-Linked SnO2:NiO Networks for MEMS Compatible Ethanol Gas Sensors
Nanoscale Research Letters volume 15, Article number: 35 (2020)
Nowadays, it is still technologically challenging to prepare highly sensitive sensing films using microelectrical mechanical system (MEMS) compatible methods for miniaturized sensors with low power consumption and high yield. Here, sensitive cross-linked SnO2:NiO networks were successfully fabricated by sputtering SnO2:NiO target onto the etched self-assembled triangle polystyrene (PS) microsphere arrays and then ultrasonically removing the PS microsphere templates in acetone. The optimum line width (~ 600 nm) and film thickness (~ 50 nm) of SnO2:NiO networks were obtained by varying the plasma etching time and the sputtering time. Then, thermal annealing at 500 °C in H2 was implemented to activate and reorganize the as-deposited amorphous SnO2:NiO thin films. Compared with continuous SnO2:NiO thin film counterparts, these cross-linked films show the highest response of ~ 9 to 50 ppm ethanol, low detection limits (< 5 ppm) at 300 °C, and also high selectivity against NO2, SO2, NH3, C7H8, and acetone. The gas-sensing enhancement could be mainly attributed to the creating of more active adsorption sites by increased stepped surface in cross-linked SnO2:NiO network. Furthermore, this method is MEMS compatible and of generality to effectively fabricate other cross-linked sensing films, showing the promising potency in the production of low energy consumption and wafer-scale MEMS gas sensors.
Volatile organic compound (VOC) sensing has been attracting more and more attention due to its significance in environment monitoring, production safety, and human health care [1,2,3,4,5]. As one of the most common and important VOCs, ethanol is the main component to be detected in drunk driving test. The resistive ethanol sensors used semiconducting metal oxides (MOS) as sensing materials are popular due to their advantages, such as cheap, nontoxic, stable, simple processing, and higher sensitivity performance [6,7,8]. Typically, various nanostructured MOS including nanowires, nanoplates, hollow spheres, and heterostructures can greatly enhance the diffusion of analyte gases and facilitate the charge transport, leading to high sensitivity and fast sensing-recovery process [9,10,11,12,13,14,15,16,17,18]. However, most of the reported sensors are fabricated by drop-coating or screen printing the nanostructured MOS solution onto ceramic tubes or plates, which results in large sensor-to-sensor variations, large size, and high power consumption of 200–1000 mW [7, 19,20,21,22,23]. Another challenge is the agglomeration between nanostructures by strong van der Waals attractions, which leads to decreased sensitivity and low uniformity . To avoid these disadvantages, substrates with low energy dissipation and new technology of sensing material integration are required before their practical commercial applications.
Nowadays, microelectrical mechanical system (MEMS) sensors developed with microfabrication methods can accomplish the device miniaturization, low power consumption, good consistency, and wafer-scale device production. Microheaters allow for high sensing temperatures to be reached with low input power by the design of a small and suspend heater area thermally isolated from the bulk substrate [25,26,27,28]. Various traditional MOS thin films can be integrated on the microheaters also by MEMS techniques such as spraying, thermal evaporation, sputtering, physical vapor deposition (PVD), atomic layer deposition (ALD), chemical vapor deposition (CVD), etc. [29,30,31,32]. The collaboration of different MEMS sensors can facilitate the development of array technology to detect gases in complex contexts, which is the prototype of electronic nose (e-nose) [33,34,35]. Despite of these advantages, challenges still exist in the following three aspects. First, the traditional MOS thin films by MEMS techniques often show poor sensitivity to target gases due to the compact surface structure and low crystallinity. For example, Kang et al. reported a sputtered Pt-doped SnO2 thin film on microheater with a sensitivity of less than 4 to 25 ppm toluene at 450 °C . All the sputtered SnO2:NiO thin films in our previous research showed low sensor response of < 2 to 5 ppm NO2 at 200 °C before incorporating the self-assembled Au nanoparticle array . Second, some researchers have tried to integrate high-performance MOS nanomaterials onto microheaters, but it is difficult to control and cast the slurry-based MOS nanomaterials onto the suspending heating area of microheaters. Several groups have reported the fabrication of nanomaterial-based MEMS sensors via ink-jet printing, polymeric mask centrifugation, and dip pen nanolithography (DPN) methods [12, 36,37,38,39]. However, the low yield and large device-to-device deviation hampers the sensor fabrication in a large scale. Third, it is also complicated to improve the adhesion between microheater and sensing nanomaterials in order to get stable parameters especially at high temperature > 350 °C. In our previous research, we found that the mix of dielectric glass dust with hollow SnO2 nanospheres was required to improve adhesion between SnO2 sensing membrane and MEMS microheater, resulting in decreased sensing performance and low stability . Fabricating sensing films with high sensitivity using MEMS compatible methods is an urgent goal.
Design of nanostructures with large surface area in the traditional MEMS thin films is the key strategy, because the sensor sensitivity is positively attributed to surface adsorption of the sensing film. A low enthalpy of the adsorbed phase is often expected when a gaseous molecule is adsorbed on the sensing film with lots of stepped and kinked surfaces . Therefore, sensing materials like three-dimensional pore arrays and cross-inked networks tend to adsorb more gaseous molecules and realize sensitive gas-sensing [40,41,42]. The use of sacrificial templates such as self-assembled polystyrene (PS) spheres array is one of the effective, relatively cheaper, and MEMS compatible ways to form large-scale uniform step-rich morphology on sputtered MOS thin films [9, 42]. And the size, period, and shape of the PS nanostructures can be controlled by further plasma etching. For example, triangle array or cross-linked network can be formed depending on the plasma etching time of PS spheres through the same processes: (i) self-assemble PS spheres, (ii) plasma etching of PS spheres, (iii) deposit MOS thin film, and (iv) remove PS spheres. Apart from creating more active adsorption sites, forming heterostructure to improve the sensing performance of MOS-based gas sensors has been intensively studied, which is a low cost, environmental-friendly, and easy-to-implement method [25, 43,44,45,46,47,48]. The sputtering target can be designed by mixing two or more MOS elements, such as SnO2/NiO, SnO2/ZnO, SnO2/WO3, etc. Besides, the component and element ratio of hybrid sensing films can be flexibly controlled by co-sputtering two targets at different sputtering power. Considering the easy accessibility of nanostructured morphology and heterostructures by templates and sputtering techniques, new type of MEMS sensors with high sensor response can be put forward.
In this work, by the MEMS compatible colloidal-monolayer-based method, a series of cross-linked SnO2/NiO networks were prepared with different periodic structures. The self-assembled close-packed PS microsphere (diameter ~ 1 μm) arrays were explored as templates, the size of which could be in wafer-scale when assembled in Langmuir-Blodgett (LB) troughs. To fabricate cross-linked SnO2/NiO networks, the ball-to-ball gaps of PS microspheres templates were tuned by plasma etching for different time (0–30 min), and then SnO2/NiO thin layers were sputtered onto the etched templates followed by removing PS microspheres. Compared with continuous SnO2/NiO films, the prepared heterostructured cross-linked networks exhibited a significantly enhanced response to ethanol vapor (~ 9 to 50 ppm) and a wide working temperature range (300–375 °C). A detection limit of 5 ppm was realized at a working temperature of 300 °C. These results demonstrate that the creation of stepped surfaces in cross-linked structure can effectively enhance the gas-sensing of traditional sputtered thin films. As a proof of concept, this work provides a flexible strategy for designing other cross-linked thin films for practical MEMS gas sensors and sensor arrays.
Materials and Methods
Fabrication of PS Microspheres Array Template
Clean substrates with 300-nm-thick Si3N4 on both sides of p-type Si (Jingyifang Electronics Co., Ltd.) were used and cut into two sizes of small pieces (1 cm × 1 cm and 2 cm × 4 cm). The use of Si3N4 substrate instead of SiO2 is necessary, because Si3N4 can serve as the mask when fabricating the hollow cavity by wet etching technique in KOH solution, as shown in Figure S1 in our previous work . Polystyrene (PS) microspheres (250 mg/ml, BIOPEONY) with 1.0 μm in diameter were used after diluted by 50% in ethanol (99.99%, Beijing Chemical Reagent Co. Ltd.). Cetyltrimethyl ammonium bromide (CTAB, ≥ 99%, SIGMA) was used to control the surface wettability.
First of all, all the Si3N4 substrates and water containers were treated by a radio frequency plasma source (YZD08-5C, Saiaote Technology Co. Ltd.) for 30 s at a power of 200 W to create hydrophilic surfaces. Two drops of diluted PS microspheres solution were cast onto a 2 cm × 4 cm Si3N4 substrate (Fig. 1a). As the ethanol evaporated, PS microspheres self-assembled into an irregular monolayer (Fig. 1b). Then, a 20 μl 5 g/L CTAB solution was added to 100 ml deionized water in a glass container to modify the surface tension of water. As the above Si3N4 substrate slid slowly into the water in the flume, the irregular PS microspheres reassembled into a close-packed PS microspheres array floating on the water surface, as shown in Fig. 1c, d. Another clean 1 cm × 1 cm Si3N4 substrate was then inserted to carefully pick up the close-packed PS microspheres array (Fig. 1e). Finally, the size of PS microspheres was tuned by changing the plasma etching time at a constant input power of 200 W (Fig. 1f).
Fabrication of Cross-Linked SnO2/NiO Networks
The SnO2/NiO (NiO 1%, SnO2 99%) MOS target material for magnetron sputtering (Kurt J. Lesker, LAB 18) was purchased from Jiangxi Ketai New Material Co. Ltd. Thin SnO2/NiO films with the thickness of 20 nm, 50 nm, and 100 nm on the etched PS microspheres array templates were obtained by sputtering the same target for 430 s, 1075 s, and 2150 s at a power of 80 W (Fig. 1g). Cross-linked SnO2/NiO networks were then formed after removing the PS microspheres in acetone, as shown in Fig. 1h. As most of the as-deposited thin films by sputtering are non-crystalline, the network films were post-annealed at high temperature of 500 °C in reduction condition (5% H2, 95% Ar) for 2 h.
Characterization of Cross-Linked SnO2/NiO Networks
The overall structure and morphologies of PS microspheres and cross-linked sensing networks were investigated by a scanning electron microscope (SEM, JEOL JSM-6700F) operated between 10 and 20 kV. The crystalline phase of sensing films was studied by small-angle X-ray scattering (SAXS, Panalytical X’pert Pro) with a Cu Kα radiation source (wave length = 1.5406 Å) at 2θ angles ranging from 20° to 80°. In addition, the elements and chemical states on surface of the films were investigated by X-ray photoelectron spectroscopy (XPS, Thermo Fisher ESCALAB 250Xi) with monochromatic Al Kα radiation (hν = 1486.6 eV; h is Planck’s constant and ν is frequency). All binding energies were calibrated with respect to the signal adventitious carbon C1s peak with a binding of 284.7 eV. The fitted peaks in the XPS spectra were separated using the XPSPeak 4.1 software.
Device Fabrication and Measurement
Gold electrodes (Cr/Au∼10/80 nm) were then fabricated on the cross-linked network by lithography (SUSS MicroTec, MA6) and electron beam evaporator technique (OHMIKER-50B), as shown in Fig. 1i. Wafer-scale cross-linked MOS gas sensors can also be fabricated by subsequent photolithography and etching techniques, according to the technological process in our previous paper . For gas response, the gas-sensing property of our prepared SnO2/NiO network sensors in Fig. 1i was measured in a homemade dynamic instrument, as shown in Fig. 2a. In detail, the probes of Pt wires on the instrument were connected with gold electrodes of sensors by an intermediate ceramic chip. Micro-sized gold electrodes on sensors were firstly connected with the gold pads (Ti/Au 10/200 nm) on the ceramic chip by a wire-bonding machine (aluminum wires, Shenzhen Shunyu Automatic Equipment Co. LTD., WL2046). The Pt wire probes were then electrically contacted with the gold pads on the ceramic chip by silver paste (Wuhan Youle Optoelectronics Technology Co., LTD.). The current-time curves were measured using a sourcemeter at a constant bias of 5 V (Keithley, 2620B). All the used gases were purchased from Beijing Hua Yuan Gas Chemical Industry Co., Ltd. To prepare a targeted gas with a specific concentration, the synthetic air and standard gas (ethanol, NO2, NH3, and other gases in synthetic air) were mixed at a certain ratio controlled by two digital mass flow controllers (Tianjin Zhonghuan Experimental Furnace Co. LTD.) at a total flow rate of 500 ml min−1. The testing temperature was varied from 200 to 400 °C. The response of the sensors was calculated by the resistance ratio between in the air (Ra) and in the target gas (Rg), (Rg/Ra-1) for NO2 and (Ra/Rg-1) for other gases.
Results and Discussion
Morphological, Component, and Chemical States Characterization
Figure 2b shows the SEM image of a typical device, characterized after all gas-sensing measurements. To make the cross-linked structure more prominent, the source and drain electrodes were separated by 100 μm, so that an amount of 80 holes can be included along the channel. The fine structure with a resistance of 10 GΩ also provides an adequate base line for gas-sensing tests. The 10 nm/80-nm-thick Cr/Au pads were designed with the size of 200 μm × 200 μm, large enough for wire-bonding by silver paste. Figure 2c shows the magnified SEM image of the area framed by the rectangle in Fig. 2b. It is clear that the sensing film in the channel is composed of cross-linked SnO2/NiO networks.
The line width and the diameter of holes in cross-linked SnO2/NiO networks were tuned by changing the plasma etching process. Figure 3a demonstrates the SEM image of an ordered PS microspheres superlattice in hexangular close-packed structure, which was prepared without plasma etching. As the time of etching treatment increased, the size of PS microspheres decreased obviously, as shown in Fig. 3b–e. Adjacent PS microspheres began to separate after plasma etching for 10 min, leaving narrow interconnecting wires which were attributed to the glass transition of PS microspheres. Only discrete triangular SnO2/NiO patterns can be formed if we use this type of PS microspheres template, in which no conductive path exists. In Fig. 3d, the interconnecting wires began to break as the plasma etching time increased to 15 min, in which case the corresponding cross-linked SnO2/NiO networks began to form. After 20 min of etching, the interconnecting wires around PS microspheres disappeared, as shown in Fig. 3e. Displacements were observed in PS microspheres array etched for 30 min due to the high power accumulation, which leads to a disorder PS array in Fig. 3f. Figure 3g–i shows the corresponding SnO2/NiO networks fabricated by the PS microspheres templates etched for 15 min, 20 min, and 30 min. The line widths for 15 min and 20 min etching templates are 400 nm and 500 nm, respectively. The SnO2/NiO network fabricated by 30 min etching templates is also disordered, as shown in Fig. 3i.
Most of the thin films deposited by sputtering, evaporation, CVD, PVD, or ALD techniques require a post-annealing process to reorganize and stabilize the original non-crystalline structure [25, 29, 30]. Thus, the cross-linked networks were post-annealed at high temperature of 500 °C in H2 for 2 h. The change of grain size and surface roughness were hard to distinguish due to the poor conductivity of SnO2/NiO for SEM characterization, whereas the SAXS patterns shows more details of the crystallinity in Fig. 4. The data of Si/Si3N4 substrate was included to deduct the impact of the background. The peaks in the SAXS pattern of the Si:Si3N4 substrate are attributed to Si3N4. (PDF 33-1160). Clearly, there is no obvious peaks appeared in as-deposited SnO2:NiO films indicating the amorphous structure. After activated by annealing in H2, obvious peaks were observed at 51.7°, 33.9°, and 26.6° corresponding to (211), (101), and (110) (JCPDS File no.41–1445), which indicated the formation of rutile SnO2. No characteristic peak of NiO was observed because of the little proportion.
For ethanol detection, gas sensing is based on the oxidation–reduction reaction of adsorbed ethanol on the surface of MOS, which leads to an abrupt conductance change in the sensing materials. Thus, the sensitivity is highly influenced by the surface elemental compositions and chemical states of annealed SnO2/NiO networks. Figure 5 shows the results of XPS analysis, in which the binding energies were calibrated by referencing the C 1s peak (284.8 eV) to reduce the sample charge effect. The full spectrum in Fig. 5a indicates the presence of Sn, O, and Ni in the SnO2:NiO composites. In Fig. 5b, two symmetric doublet peaks were observed centered at 486.2 eV (Sn 3d5/2) and 494.7 eV (Sn 3d3/2) with a spin-orbit splitting of 8.5 eV, indicating the presence of Sn in an oxidation state of + 4. Figure 5c shows that the surface oxygen species can be deconvoluted into two Gaussian component peaks centered at 530.1 and 531.2 eV, which are respectively corresponding to the lattice oxygen (Olatt) and O2− species. Given that the ethanol sensing performance is closely related to the O2− ion, the high percentage of O2− (~ 33.3%) might indicate lots of active adsorption sites in cross-linked SnO2/NiO networks. Distinct Ni 2p peaks in Fig. 5d located at 855.2 eV and 873.2 eV corresponding to Ni 2p3/2 and Ni 2p1/2 were observed, indicating the existing of Ni in the sensing composites in a valence state of 2+. This ratio of 1% between NiO and SnO2 has been optimized by balancing two aspects: the formation of effective p-n heterojunction and an adequate baseline of resistance, which has been discussed in detail in our previous work .
Gas-sensing tests to 50 ppm ethanol were carried out for sensors based on films with different structural parameters, such as annealing or not, cross-link network or continuous film, various film thicknesses, and line widths. For each case, we measured eight devices for calculating the statistical errors. First, the gas-sensing performance of sensors based on 50-nm-thick SnO2:NiO network and 50-nm-thick continuous SnO2:NiO film are compared in Fig. 6a. It is clear that the ethanol responses of all SnO2:NiO film-based sensors are extremely low (< 0.1) whether they were post-annealed or not. This is a common phenomenon for sputtered films due to the close-packed surface structure preventing the exchange of gas molecules. In contrast, the sensing response values of annealed SnO2:NiO networks gradually increased to the highest response value with the increase of the operation temperature from 200 to 300 °C. And the responses stayed around 9 at a wide temperature range of 300–375 °C. While further increasing the operation temperature from 375 to 400 °C, the responses decreased rapidly. The significantly increased responses in SnO2:NiO networks shows that creating holes is an effective way to enhance the gas-sensing properties of sputtered thin films. Second, annealing is verified to be necessary to activate the networks. During post-annealing at 500 °C, the SnO2:NiO network was reorganized to obtain crystallinity and effective surface area. Third, the influence of network thickness on the temperature-dependent sensor responses is also shown in Fig. 6a. The maximum magnitude of sensitivity was obtained for 50-nm-thick networks. This result can probably be explained considering two aspects. On the one hand, step-like surface is more prominent for thicker SnO2:NiO networks, which may create more active adsorption sites for gas-sensing. On the other hand, the gain or loss of electrons on the surface of sensing materials due to the adsorbed gas molecules becomes negligible for thicker networks, because most of the conduction paths exist in the internal part of materials. Finally, the influence of plasma etching time on gas-sensing performance is shown in Fig. 6b. The sensor responses at various working temperatures first increases with increasing etching time from 15 to 20 min, and then decreased with a large statistical error for the etching time of 30 min. This large device-to-device deviation can be attributed to the displacement of PS microspheres under constant plasma bombarding, which leads to a disordered cross-linked network. In comparison with the various nanostructured SnO2 prepared by other methods in Table 1, the cross-linked SnO2/NiO network exhibited comparable sensitivity [19, 23, 47, 49,50,51,52]. We also investigated the ethanol sensitivity of other MEMS compatible sensing materials in Table 1, such as DPN deposited Au/SnO2 nanocomposites, ZnO nanowires grown on a MEMS microplate, and ZnO tetrapods deposited on a microheater [37, 38, 51]. Apart from the comparable or better sensitivity, there are several other advantages for the cross-linked SnO2/NiO networks including high yield, low device-to-device deviation, cheap and simple processing.
The typical response and recovery characteristic curve of the network-based sensor to ethanol in the range of 5–100 ppm at 300 °C was shown in Fig. 7a. Obviously, the responses in these curves increased with increasing ethanol concentration. The measured responses are 3.04, 4.58, 6.39, 9.44, 11.00, 13.19, 18.53, and 22.45 for SnO2/NiO network corresponding to 5, 10, 20, 30, 40, 50, 80, and 100 ppm, respectively. It can be concluded that a low detection limit of < 5 ppm can be achieved for our network based sensors. However, the measured response and recovery time of network sensor are in the order of minutes, much longer than the nanomaterial-based sensors [53, 54]. Compared with the test system and sensing materials in the reported sensors, we believe that the long response and recovery time in our work can be attributed to the following two reasons. First, we measured the gas-sensing property in a dynamic test system instead of a static test system. The target gas was mixed in a special chamber, and then diffused for a long distance into the quartz tube (50 mm in diameter, 1 m in length) after we open the valve of chamber. It costs more than 1 min for the diffused gas to blow away the synthetic air and reach a stable concentration. Second, the design of cross-linked SnO2:NiO networks is based on sputtering films, which show much poor crystallinity and much smaller surface-to-volume ratio. Thus, the exchange of gaseous molecules in such networks is much slower than that in nanostructured sensing materials. Figure 7b shows that the gas sensor shows a linear response to the change of ethanol concentration in the relatively low concentration range (5–100 ppm).
As we all know, selectivity is a key factor for practical applications of a gas sensor. Figure 7c shows the response values of the cross-linked SnO2:NiO network upon 5 ppm ethanol and the common interfering gases such as NO2, SO2, NH3, acetone, and toluene at an operating temperature of 300 °C. This result clearly demonstrates that the sensor exhibits better selectivity to ethanol gas. On the one hand, the response of oxidizing gases like NO2 mainly depends on the adsorption-desorption of NO2 molecules, which is often low efficient at high temperature (> 200 °C). On the other hand, the oxidizing performance for reducing gases depends on their intrinsic reducing ability, which is related to their bond energies. The lower the bond energy is, the easier the reaction occurs. According to the bond energy data of 610.3, 798.9, 548, and 458.8 kJ/mol, respectively for C=C, C=O, S=O, and O-H, it is obvious that O-H bond in ethanol is the weakest . This probably explains the high selectivity to ethanol for our network sensors.
Figure 7d shows the stability of network based sensors. In our test, the sensor was exposed to 50 ppm ethanol for 4 cycles in 72 h at a working temperature of 300 °C. A relatively constant response of around 10 was obtained in the 4-cycle tests. However, the sensor broke down in the fifth cycle because of the electrical degradation under high sensing temperature. Similar problems were reported by Zeng, et al. when they measured the long-term stability of SnO2 nanowire sensors at 200 °C . The oxidation of adhesion layer like Ti or Cr leads to a rapidly increased contact resistance, especially in O2 atmosphere at high temperature. The inset figure in Fig. 7d shows the response-time curve of the same sensor after redefining gold electrodes three weeks later. The recovery of sensitivity implies the stability of cross-linked SnO2:NiO network. High quality of electrical contacts under harsh sensing conditions can be achieved probably by using heavily doped metal oxide and the nitride or carbide of transition metals, which will be investigated in the future work.
The space-charge layer model has often been applied to explain the detailed change of mobile charge carriers exposed in air and target gases. In SnO2:NiO composites, SnO2 is a typical n-type MOS with a reported work function of 3.5 eV, and NiO is a p-type material with a work function of 4.4 eV [57, 58]. Thus, p-n heterojunction forms after the post-annealing of SnO2:NiO composites, leading to the transfer of electrons from SnO2 to NiO in order to get a stable state. A depletion layer appears at the SnO2/NiO interface, as indicated by the blue rectangle in Fig. 8a. When exposed in air, the adsorbed oxygen molecules on the surface of SnO2 are transformed to oxygen ions (O−, O2−, or O2−) by capturing electrons from the conductance band of SnO2 network (Eqs. (1)–(4)). The electron-capture process leads to a wide depletion region in SnO2, and thus a high resistance state is formed, as shown in Fig. 8c. The yellow bold lines Fig. 8c indicates the wide depletion region in the holes of cross-linked SnO2:NiO network. Compared to the pure SnO2, the formation of p-n heterojunction leads to a higher sensor resistance in air and a wider depletion region due to the electron transfer from SnO2 to NiO.
When the SnO2:NiO network sensors are exposed to alcohol vapors (reducing gases), the alcohol molecules adsorbed on the surfaces of SnO2 react with the chemisorbed oxygen ions forming CO2 and H2O, according to Eq. (5) and Eq. (6). The release of free electrons back into SnO2 leads to a narrow depletion region in Fig. 8d and a low resistance state. Electrons transfer from NiO back to SnO2 in Fig. 8b to get a new uniform Fermi level, because the electron concentration is lower in SnO2 than that at the initial state. This transfer of electrons leads to additional conduction paths and a lower resistance state, which probably explains the role of p-n heterojunction in enhancing the gas-sensing performance.
The creation of steps in sputtered SnO2:NiO thin films is proved a key factor to achieve high response, which is positively attributed to the enhanced surface adsorption. On the one hand, the surface of SnO2:NiO network is less compact compared with the continuous SnO2:NiO film, facilitating the adsorption of gas molecules. The cross-linked SnO2:NiO network is composed of interconnecting nanowires. Additional nanostructures like nanocracks appear in these nanowires due to the release of tensile stress in the post-annealing process, which can be demonstrated by the contrast of light and dark in the nanowires in Fig. 3h. On the other hand, sensing area rich of the stepped and kinked crystal surfaces should tend to adsorb more gaseous molecules than those on the other area, because a lower enthalpy of the adsorbed phase exists when a gaseous molecule is adsorbed on such structure. According to thermodynamical theory, the correlation between the changes in Gibbs free energy (G), entropy (S), and enthalpy (H) follow the equation ΔG = ΔH-TΔS . In the process of gas adsorption, Gibbs free energy decreases. It is clear that a lower enthalpy of the adsorbed phase (Ha) indicates a larger ΔG and more adsorbed gaseous molecules. Considering the creation of nanostructures and the steps in cross-linked network, the senor response of SnO2:NiO network is 45-fold higher than that of sputtered continuous SnO2:NiO film.
Cross-linked SnO2:NiO networks were successfully fabricated via MEMS compatible self-assembly and template sputtering techniques. The structural parameters of PS microspheres template were controlled to achieve various line widths of interconnecting nanowires in SnO2:NiO networks. Gas sensing measurements indicated that the SnO2:NiO network sensors were highly sensitive to ethanol. For the optimum structure, SnO2:NiO network with plasma etching time of 20 min, the response to 50 ppm ethanol at 300 °C was 9, 45-fold that of continuous SnO2:NiO thin film. A linear dependence of the response on the ethanol concentration in the range of 5–100 ppm was observed. The SnO2:NiO network showed only minor sensitivity to NO2 (1.2 to 5 ppm NO2) and even lower sensitivity to other interfering gases. Despite of the electrical degradation of electrodes after continuously operated for 72 h at 300 °C, the SnO2:NiO sensing network showed long-term stability of over 3 weeks. The enhanced ethanol sensing performance due to the creation of steps in SnO2:NiO network results from an less compact structure and increased adsorption sites.
Availability of Data and Materials
The authors declare that the materials, data, and associated protocols are available to the readers, and all the data used for the analysis are included in this article.
Atomic layer deposition
Cetyltrimethyl ammonium bromide
Chemical vapor deposition
Dip pen nanolithography
Microelectrical mechanical system
Semiconducting metal oxides
Physical vapor deposition
Small-angle X-ray scattering
Scanning electron microscope
Volatile organic compound
X-ray photoelectron spectroscopy
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This research was financially supported by the National Natural Science Foundation of China (no. 51602314), the National Key R&D Program of China (2016YFC0207100), and the Guangdong Innovative and Entrepreneurial Research Team Program (No. 2014ZT05C146 and 20150317025954531).
The authors declare that they have no competing interests.
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Tong, W., Wang, Y., Bian, Y. et al. Sensitive Cross-Linked SnO2:NiO Networks for MEMS Compatible Ethanol Gas Sensors. Nanoscale Res Lett 15, 35 (2020). https://doi.org/10.1186/s11671-020-3269-3
- Cross-linked SnO2:NiO network
- Gas sensor
- MEMS compatible
- Ethanol detection