To Thi Nguyeta,
Dang Thi Thanh Lea,
Nguyen Van Duya,
Chu Thi Xuana,
Sven Ingebrandtb,
Xuan Thang Vub and
Nguyen Duc Hoa
*a
aInternational Training Institute for Materials Science (ITIMS), Hanoi University of Science and Technology (HUST), No 1 Dai Co Viet, Hai Ba Trung, Ha Noi, Vietnam. E-mail: ndhoa@itims.edu.vn; hoa.nguyenduc@hust.edu.vn
bInstitute of Materials in Electrical Engineering 1, RWTH Aachen University, Sommerfeldstr. 24, Aachen 52074, Germany
First published on 26th April 2023
As a source of clean energy, hydrogen (H2) is a promising alternative to fossil fuels in reducing the carbon footprint. However, due to the highly explosive nature of H2, developing a high-performance sensor for real-time detection of H2 gas at low concentration is essential. Here, we demonstrated the H2 gas sensing performance of Ag/Pd nanoparticle-functionalized ZnO nanoplates. Bimetallic Ag/Pd nanoparticles with an average size of 8 nm were prepared and decorated on the surface of ZnO nanoplates to enhance the H2 gas sensing performance. Compared with pristine ZnO, the sensor based on ZnO nanoplate doped with Ag/Pd (0.025 wt%) exhibited an outstanding response upon exposure to H2 gas (Ra/Rg = 78 for 500 ppm) with fast response time and speedy recovery. The sensor also showed excellent selectivity for the detection of H2 over the interfering gases (i.e., CO, NH3, H2S, and VOCs). The superior gas sensing of the sensor was dominated by the morphological structure of ZnO, and the synergistic effect of strong adsorption and the optimum catalytic characteristics of the bimetallic Ag/Pd enhances the hydrogen response of the sensors. Thus, bimetallic Ag/Pd-doped ZnO is a promising sensing material for the quantitative determination of H2 concentration towards industrial applications.
In the scientific literature, there are many approaches, such as the use of electrochemical,5 optical,6 acoustic,7 and resistive sensors,8 that have been applied to monitor H2 gas. Among these techniques, the resistive sensor is an attractive device for real-time gas monitoring because of its compact size, low cost, operating stability over longer periods, and ease of use in practical circumstances.9 Semiconducting metal oxides (SMOs), such as zinc oxide (ZnO), tin(IV) oxide (SnO2), and indium oxide (In2O3), with different morphologies have been used as gas sensing layers because of their good sensing capabilities such as low detection limit, high sensitivity with fast response and recovery time, and can be integrated into portable devices.10 As an n-type semiconductor with a wide band gap (3.7 eV), ZnO is an appropriate material for gas sensors because of its known superior sensing properties and its facile manufacturing technology.11 Various nanostructures of ZnO (i.e., nano lily-bud garden,12 nanoparticles,13 nanowires,14 and nanorods15) have been used as sensing materials in gas sensors. Among the different morphologies, ZnO nanomaterial has been extensively studied by enhancing the gas adsorption rate and electron transport on an ultrathin surface, making it capable to sense various gases.16,17 For instance, porous ZnO nanosheet with a thickness of 80 nm has been reported to exhibit the best response to NO2 gas at 200 °C.16 The ZnO nanosheet sensor reached a response value of 175.5 toward 100 ppm of tetraethylammonium.17 Some other hazardous gases (i.e., ethanol, CO, NO2, and H2S) could also be detected by the ZnO nanomaterial.18,19 Recently, ZnO nanostructures have also been used to detect H2 gas leaks, where the ZnO nanorods exhibited a low response of 9.2 to 1000 ppm of H2 at 225 °C.20 However, pure ZnO-based sensors showed low sensitivity and poor selectivity. Thus, many significant studies have been performed to overcome these limitations.21
One of the techniques that can remarkably improve the four factor “S” sensitivity, selectivity, stability, and response speeds of gas sensors is the use of noble metals to functionalize the surface of a metal oxide by utilizing the spillover effect and unique catalytic property of these nanoparticles.19–21 For instance, Kim et al.22 synthesized Pd-decorated ultrathin ZnO nanosheets in detecting hydrogen in a gaseous mixture with benzene. ZnO thin film decorated with Pt nanoparticles was used to detect H2 gas in the mixture with humidity.21 Agarwal et al.23 used Ag/ZnO hollow tube as sensing material to enhance the H2 gas sensing performance. Ag catalyst nanoparticles were functionalized on the metal–organic framework-derived ZnO hollow nanocages.24 However, the use of single-metal material as catalyst in enhancing the gas sensing performance have some limitations. For instance, when operating at high temperature, metal catalysts undergo oxidation, leading to reduced catalytic activity and deterioration of sensing performance.25 Alloying nanoparticles with two or more metal elements have recently been reported to show superior sensing properties in terms of electronic and geometric parameters compared with monometal doping catalyst for gas sensors.26,27 The alloy of Pt/Pd ultrathin film has been deposited on the surface of ZnO nanorods to enhance H2 gas sensitivity.28 Le et al.29 reported efficient H2 gas sensor by using PdAu@ZnO core–shell nanostructure. However, the PdAu nanoparticles were prepared by a sodium citrate reduction method with CTAB as surfactant, which may cause contamination of the sensing materials. Zamora Zeledón et al. have recently reported enhanced electrocatalyst approach by tuning the electronic structure of Ag/Pd alloys for reducing alkaline oxygen but not sensing application.30 Given that silver (Ag) is much cheaper (by 110-folds) than Au or Pt, using the Ag/Pd alloy as the catalyst is more economical. The use of Ag/Pd alloy also utilize the synergic catalytic effect of both metals.29 Furthermore, the alloy is thermal stable over oxidation, maintaining its catalytic activity thus enable the long-term stability of the sensor. However, few studies have used Pd/Ag nanoparticle-decorated ZnO nanoplates to enhance the H2 gas sensing performance.31
Here, Ag/Pd nanoparticles were uniformly functionalized on the surface of hydrothermally grown ZnO nanoplates to enhance H2 gas sensing properties. The Ag/Pd–ZnO nanoplate sensors were fabricated by simple and straightforward drop-casting onto interdigital electrodes, which were previously patterned using photolithography and a sputtering approach, followed by an annealing treatment at 600 °C. The resistive-type gas sensors were tested for hydrogen detection and showed sensing properties with sensitivity and selectivity to other gases (i.e., ethanol, methanol, isopropanol, triethylamine, NH3, CO, and H2S). The device could detect low concentration of H2 from 25 ppm to 500 ppm with ultrafast response and recovery times. The role of the Ag/Pd nanoparticle decoration in the enhancement of the gas sensing performance of ZnO was also discussed intensively.
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Fig. 1 (A) Schematic diagram of the synthesis of pristine ZnO nanoplate, (B) Ag/Pd-doped ZnO nanoplates, (C) and the gas sensor fabricated by the drop-casting process. |
The fabricated sensors were characterized via a laboratory-made gas sensing measurement system.35 H2 (10.000 ppm) diluted in N2 was used as the standard test gas. A series of mass flow controllers were used to mix the standard gas with dry air to achieve the desired gas concentrations ranging from 25 ppm to 500 ppm. Prior to the measurements, the sensor was preheated at 600 °C for 2 h to stabilize the contact between the Pt electrode and Ag/Pd–ZnO nanoplates. The gas concentration was controlled by modifying the flow rate of air and standard gas, but the total flow rate introduced in the measuring chamber was fixed at 400 sccm. The sensor resistance versus testing time was recorded using a source measurement unit instrument (Keithley 2602B). The response value of the sensor was determined by the ratio of Ra/Rg toward reducing gases or Rg/Ra in the case of oxidizing gas, where Ra and Rg were the resistances of the sensor in air and target gas, respectively. The response time (τres) and recovery time (τrec) were determined as the times to reach 90% saturation of the response after exposure to the analyte gas and air, respectively. The detection limit (DL) was calculated using the slope of the linear regime as described before.36
The structure, morphology, and composition of the prepared materials were characterized using a scanning electron microscope (SEM, JEOL 7600F), energy-dispersive X-ray spectroscope (EDS), X-ray diffractometer (XRD, D2 Phaser, Bruker) with Cu Kα radiation, and high-resolution transmission electron microscope (HRTEM, JSM 2100 F).
The TEM and HRTEM analyses were employed to further study the nanostructure and presence of Ag/Pd nanoparticles on the surface of the ZnO nanoplates. The TEM micrographs in Fig. 3A revealed the plate-like features of the ZnO nanoplates with different shapes. Fig. 3B also shows the existence of the Ag/Pd nanoparticles as black dots with small size of eight nm and distributed randomly on the surface and at the edge of the ZnO nanoplates. The HRTEM micrographs of the prepared sample shown in Fig. 3B and C confirmed that the ZnO nanoplate was a polycrystal, while the Ag/Pd nanoparticle was a single crystal. As shown in the inset of Fig. 3B, the corresponding selected area electron diffraction patterns of the Ag/Pd-doped ZnO nanoplates confirmed that the bright rings showed the nature of the ZnO polycrystals. A zoomed out HRTEM image of the Ag/Pd-doped ZnO sample established the coexistence of Ag/Pd and ZnO nanocrystals with interplanar spacing of 0.28 nm (Fig. 3D), 0.23 nm (Fig. 3E), and 0.225 nm (Fig. 3F), corresponding to the lattice fringes of (100) planes of hexagonal ZnO, (111) planes of Ag, and face-centered cubic Pd.38,39 Thus, the HRTEM images confirmed the successful decoration of the surface of ZnO nanoplates with bimetallic Ag/Pd nanoparticles.
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Fig. 3 (A) Low and (B–F) high magnification TEM images of the 0.025 wt% Ag/Pd-doped ZnO nanoplates. Inset (B) shows the corresponding selected area electron diffraction. |
The effect of incorporating Ag/Pd nanoparticles on the microstructure and crystalline features of the ZnO nanoplates was also investigated by X-ray diffraction. As shown in Fig. 4, typical diffraction peaks of the pure ZnO nanoplates after annealing at 600 °C in 2 h were indexed to the wurtzite (hexagonal) phase of ZnO (JCPDS 36-145) without significant impurity peak. The major peaks were located at 2θ of 31.75°, 34.35°, 36.12°, 47.59°, 56.59°, 62.83°, 66.36°, 67.93°, 69.0°, 72.61°, and 76.86°, corresponding to the (100), (002), (101), (102), (110), (103), (200), (112), (201), and (202) crystal planes.40 The distinct peak indicated the successful preparation of single-phase ZnO nanoplates. The XRD pattern of the Ag/Pd nanoparticles dispersed on the Si substrate with thermal treatment at 150 °C for 2 h is shown in Fig. 4. The diffraction peaks of the face-center cubic Ag and Pd were observed at 2θ of 39.67°, 40.28°, 46.06°, 65.25°, 67.30°, and 76.65° indexed to (111)Ag, (111)Pd, (002)Pd, (220)Ag, (220)Pd, and (311)Ag crystallographic planes of Ag (JCPDF 89-3722) and Pd (JCPDF 46-1043).41 Here, the (111) peak of Ag/Pd nanoparticles lines between the (111) peaks of face-centered cubic crystals Ag and Pd, indicating the successful formation of the Ag/Pd alloy.30 The well-defined diffraction peaks indicated that the Ag/Pd alloy was formed as a solid solution. Meanwhile, the Ag/Pd-doped ZnO exhibited additional peaks of Ag/Pd along with the typical diffractions of hexagonal ZnO crystal. All additional peaks detected in the XRD analyses indicated the formation of the alloying metal Ag/Pd nanoparticles on the surface of ZnO nanocrystals. Using the Scherrer formula, the crystal size of the ZnO nanoplates can be calculated to about 21.44 nm,42 which is approximately the Debye length of ZnO. Therefore, a high gas sensitivity can be expected from this material because metal oxide with crystal size comparable with the Debye length enable the fully electron depletion, leading to the maximum sensor response.
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Fig. 4 XRD patterns of the bimetallic AgPd, pristine ZnO nanoplates, and Ag/Pd-doped ZnO nanoplates. |
Metal oxide semiconductor gas sensors doped with mono-metallic metals are known to show low sensing performance, limited response time as well as low selectivity toward H2 detection.43 To resolve these limitations, ultrathin ZnO nanoplates were modified on the surface by using bimetallic Ag/Pd nanoparticles. The results showed significant sensitivity at the temperature range of 200–400 °C. In this study, three different types of sensors corresponding to the different weight ratios of bimetallic Ag/Pd nanoparticles and ZnO nanoplates were tested toward H2 gas in the concentration range of 25–500 ppm. The sensor response to the reducing gas was determined as S = Ra/Rg. In each pulse measurement, the sensor was exposed to H2 for 200 s, then recovered by 400 sccm air flow until the baseline resistance was reached.
Controlling the amount of the noble metal dopant into the ZnO nanoplates that were deposited on the sensing film region is crucial to optimize the fabricated parameter and study the gas sensing features. Fig. S3A (ESI†) shows the dynamic response/recovery transient versus the time of the 0.05 wt% Ag/Pd–ZnO sensor obtained in the presence of various concentrations of H2 gas from 25 ppm to 500 ppm. The resistance of the sensor decreased and reached a saturation value upon a certain value of H2 exposure because of the natural behavior of an n-type semiconductor. Then, the response had a sharp drop immediately and turned to the baseline after the removal of H2 from the measuring chamber. The response speed was found to be slow at 200 °C with a time response of ∼190 s and decreased to 6 s when the operating temperature increased to 350 °C. This enhancement in response time was attributed to the desorption of target gas molecules and catalytic activity. The gaseous molecules became easy to remove from the surface sensing layer at higher temperature. The response value was defined at a certain H2 concentration, as shown in Fig. S3B (ESI†). The 0.05 wt% Ag/Pd-doped ZnO sensor exhibited a response value that tended to increase with increasing temperature. The highest response of the sensor reached 50.6 upon exposure to 500 ppm of H2 at 350 °C and 1.2 at 200 °C. This difference was attributed to the nature of H2 gas that enhanced the surface interaction at higher temperatures and numerous adsorbed oxygen species on the sensing layer generated after taking electrons from the conduction band.
The response of the sensor improved significantly when the weight percentage of Ag/Pd nanoparticles modified on the ZnO was reduced to 0.025 wt%. Fig. 6A show the dynamic response curve of the sensor to H2 gas. As mentioned in the previous section, the base resistance of the sensor is changing with temperature, where the sensor resistance increased immediately in the range of 5.3–53 kΩ as the temperature increased from 200 °C to 400 °C. This result is interesting after doping the notable metal nanoparticles. The competition between two dominant conductivity mechanisms led to the unusual natural behavior of semiconductors. In all measured conditions, the sensor recover completely to the initial regime after removing H2 gas. Fig. 6B showed that the response value reached 78 times upon exposure to 500 ppm H2 at 400 °C, which was higher than that of 0.05 wt% Ag/Pd-doped ZnO sensor. Thus, the sensing performance of the sensor was enhanced remarkably after reducing the mass ratio of catalytic bimetallic.
In the case of continuous decreasing the weight percentage of the Ag/Pd alloying (i.e., 0.0125 wt%), the sensor exhibited lower sensitivity compared with the 0.05 and 0.025 wt% Ag/Pd-decorated ZnO, as shown in Fig. S4A and B (ESI†). In detail, the response value reached 35 at the optimized temperature of 350 °C with a lower reactive speed. This phenomenon could be attributed to the co-catalytic phenomena and synergy effect of the bimetallic Ag/Pd in gas sensing of ZnO-based sensor tend to reduce.
A proper calibration of the gas sensor in practical application is essential to interpolate the different concentrations in the monitoring area. As shown in Fig. 7A, the Ag/Pd-doped ZnO-based gas sensor depicted a linear fitting, the H2 concentration showed a first-order function behavior. The response slope was 0.1396 ppm−1, and the fitting quality of R2 was 0.98%. Thus, the theoretical DL of the H2 gas sensors was determined using the signal-to-noise ratio and the sensitivity value, which were extracted from the linear extrapolation, as follows:44
The response and recovery times of the sensor were determined from the response curve versus reaction time; that is, its value reached 90% saturated resistance. Fig. 7B shows the response and recovery times of the Ag/Pd(0.025 wt%)-doped ZnO nanoplate sensor, which were calculated at 400 °C at different H2 concentrations. The sensor indicated ultrafast reaction speed, and its value is of several seconds. For instance, the response and recovery times for the detection of 500 ppm H2 gas were 2 s and 13 s, respectively. The response time increased with the decrease in introduced concentration. By contrast, recovery time would be reduced upon exposure to lower H2 concentration. This phenomenon was due to the adsorption and desorption gaseous mechanism. That is, the target molecules were easily transported into the surface of sensing material at high H2 gas concentration. However, the target molecules were desorbed easily from the surface of the sensing layer at low concentration after being refreshed by airflow. The results are in good agreement with other reports.44,45
To demonstrate the enhancement in H2 sensing performance after modifying the Ag/Pd nanoparticles, the pure ZnO nanoplates and the Ag/Pd-doped ZnO nanoplate-based sensors were tested toward the detection of 500 ppm H2 in the temperature range of 150–450 °C. As shown in Fig. 8A, the Ag/Pd-doped ZnO nanoplate sensor exhibited superior gas sensing performance with a response value of 47-fold larger than that of the pure ZnO counterpart at its optimized temperature.
To evaluate the selectivity of the H2 gas sensor, the Ag/Pd-doped ZnO sensor was measured to various interfering gases, namely, CO, NH3, C2H4, and VOCs (triethylamine, ethanol, methanol, and acetone), under concentration of 500 ppm at 400 °C. As seen in Fig. 8B, the sensor exhibited an excellent response to H2 compared with those to other gases due to the unique interaction between the notable metal and H2 gas molecules during the adsorption process. This result suggested that the Ag/Pd-doped ZnO nanoplate-based sensor is a potential candidate for monitoring and/or alarming H2 leakage over the contamination with other gases.
In addition to the short-term stability was evaluated by testing the sensor over eight cycles on/off of 100 ppm of H2 gas. No obvious decay in response was observed during the testing process as shown in Fig. 9A, indicating a fascinating repeatability in terms of response and recovery capability. The long-term stability was also tested continuously to 100 ppm of H2 in four weeks. As shown in Fig. 9B, the dynamic resistance had good long-term stability with small variation in response values for a week of testing.
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Fig. 9 (A) The short-term and (B) long-term stability of the 0.025 wt% Ag/Pd–ZnO sensor after 4 continuous weeks of testing at 400 °C. |
The previously discussed gas sensor behavior of Ag/Pd-doped ZnO toward H2 was observed under dry air conditions. Nevertheless, in practical applications, such as storage and transport places, the presence of humidity in the atmosphere results in the noise signal at the different periods of recorded data. To outstanding the behavior of humid condition to the dynamic response of sensor, the Ag/Pd–ZnO based sensor is investigated in the presence of water vapor. Fig. 10A show the response of the 0.025 wt% Ag/Pd–ZnO based sensor toward 500 ppm H2 in the temperature range of 200–450 °C with various relative humidity. There is marginal fluctuation in response when the sensor operates in the high humid condition (i.e., 90% RH). The decrease in response was attributed to the water molecules adsorbed on the surface which prevented numerous H2 gas molecules to be adsorbed and react with previously generated oxygen species. The dynamic resistance of sensor in the range H2 concentration of 25–500 ppm were given in Fig. 10B. The sensor recovered completely to initial baseline; however, it is getting slow reaction with H2 gas molecules when increasing the humidity level. Additionally, the base resistance of the Ag/Pd-doped ZnO sensor decreased with increasing relative humidity. In terms of the pure ZnO material under humid conditions, the OH− group comprehensively adsorbed on the ZnO surfaces and O− species adsorption was perturbed by the presence of OH−. The water molecules operated as the electron acceptor, resulting in a decrease in the number of electrons in ZnO materials. Otherwise, the resistance of the pure ZnO sensor tended to increase. However, when decorated with Ag/Pd nanoparticles, the adsorption of O−2 species on the metal catalyst prevented OH−. This phenomenon reduced the number of the extracted electron from the conduction band caused by the water molecules.46 The calibration curves were extracted from resistance response graph and fitted with first-order equation at 30, 60 and 90% RH at 400 °C (Fig. 10C). The figure shows good linear characteristic between H2 concentration and sensor response. Besides, the sensitivity of sensor is estimated approximately 0.14, 0.15, and 0.12 ppm−1, corresponding with 30, 60, and 90% RH. Inspire of working in the humid circumstance, the sensor was subjected to seven consecutive cycles of 50 ppm H2, the data is shown in Fig. 10D. The graph shows that the sensor reaches fascinating repeatability and small drift.
Table 1 shows a comparison of recent reports in the scientific literature with conductive sensors based on pristine, composite, and modified notable metal (i.e., Ag, Pd, Pt, and Co) ZnO nanomaterial. ZnO-based resistive sensors were grown by different methods to achieve various morphologies. Such morphologies exhibited different response characteristics in H2 gas monitoring. Similar to other metal oxides, ZnO-based sensors are almost applied in detecting H2 gas at high temperatures, that is, in the range of 200–450 °C with a slightly small response value and slow reaction speed. As illustrated in Fig. S5 (ESI†), the response and recovery time of the Ag/Pd–ZnO sensor are approximately 2 s and 13 s; much faster than those of the pure ZnO sensor of 77 s and 78 s, respectively. Here, the Ag/Pd–ZnO sensor is high competition with other sensors in terms of high response value, detection limit, and response/recovery speed.
Material | Method | Concentration (ppm) | Response | τres/τrec (s) | Temperature (°C) | LOD (ppm) | Ref. |
---|---|---|---|---|---|---|---|
a Response defined as Ra/Rg.b Response defined as (Rair − Rgas)/Rgas ×100 (%). | |||||||
Rose-shaped ZnO | Hydrothermal | 50 (10–150) | 50b | 360/960 | 270 | 0.01 | 47 |
Pt-decorated ZnO NPs | Magnetron sputtering | 1000 (200–1000) | 14.9b | 133/112 | 300 | 100 | 48 |
ZnO/Pt thin films | RF sputtering | 15 (0–15) | 6.3a | — | 250 | 0.15 | 21 |
Pt-decorated ZnO | RF sputtering | 1200 (75–1200) | 94b | 240/500 | 300 | 75 | 49 |
Pd capped ZnO NRs | Sputtering | 500 (100–1000) | 3.6b | 59/51 | 350 | 100 | 50 |
Pd-functionalized ZnO nanowires | Vapor–liquid–solid technique | 100 (0.1–100) | 87.17a | — | 350 | 0.1 | 51 |
Pd–ZnO nanosheet | Solvothermal method | 50 (0.1–10) | 2.514 a | 336/294 | 250 | 0.5 | 22 |
Spherical Au on ZnO thin films | RF magnetron sputtering | 50 (50–1000) | 79b | 25/55 | 250 | 100 | 52 |
In-doped ZnO thin film | Chemical solution deposition | 5 (1–1660) | 15b | — | 300 | 1 | 53 |
Ag/ZnO hollow microstructures | Chemically coprecipitation | 300 (5–300) | 479b | 175/655 | 250 | 5 | 23 |
Co3O4-loaded ZnO nanofibers | Electrospinning | 10 (1–10) | 133b | — | 300 | 1 | 54 |
ZnO/Co | Hydrothermal | 3000 (1000–3000) | 97a | 74/40 | 300 | 1000 | 55 |
0.025 wt% Ag/Pd-doped ZnO | Hydrothermal combine polyol | 500 (25–500) | 78a | 2/13 | 400 | 0.8 | This study |
The superior hydrogen sensing properties of the Ag/Pd-doped ZnO sensors with respect to the pristine ZnO could be attributed to many factors as follows: the change in the barrier height via charge transfer between Ag/Pd alloy and the ZnO surface; the spillover effect in enhancing the preabsorbed oxygen species; and the catalytic effect of Ag/Pd alloying nanoparticles in dissociation of H2 molecule.
To understand the influence of bimetallic nanoparticles on the gas sensing mechanism, the chemical adsorption activities and energy band diagram of pure ZnO and the Ag/Pd–ZnO nanoplates in the air and H2 gas are proposed (Fig. 11). When the sensor was placed in the air, the oxygen molecules were adsorbed onto the surface of ZnO nanoplates and captured the free electrons to generate the oxygen species (eqn (1) and (2)), resulting in the formation of depletion layer with low conductivity near the surface (Fig. 11A).
O2(gas) + 2e− → O−2(ads) | (1) |
O2(gas) + 2e− → 2O−(ads) | (2) |
Upon exposure to H2 gas, the H2 molecule react with pre adsorbed oxygen species and releases free electrons back to the conduction band of ZnO, as eqn (3) and (4). As a result, the release of free electrons decreases the resistance of bare ZnO sensor.
H2 + O− → H2O + e− | (3) |
H2 + O2− → H2O + 2e− | (4) |
However, when the ZnO material was functionalized by noble metal, the spillover effect was considered. In this circumstance, the introduced gas was adsorbed on the surface of the bimetallic Ag/Pd NPs. Afterward, it dissociated and migrated to the sensing material, thus enhancing the preabsorbed oxygen species. The gas adsorption rate before and after doping the noble metal are demonstrated in (Fig. 11B). A larger number of oxygen species was generated on the surface of the Ag/Pd-doped ZnO sensor compared with pure ZnO, leading to an expansion in the space-charge region in the doped ZnO material. That is, the baseline electrical resistance of doped ZnO in air became higher than that of pristine ZnO. Once the Ag/Pd-doped ZnO sensor was exposed to H2, the H2 molecules reacted with the preabsorbed oxygen species to form water and release free electron, as following eqn (5)–(7):56
![]() | (5) |
2H + O− → H2O + e− | (6) |
2H + O2− → H2O + 2e− | (7) |
Numerous free electrons returned to the conduction band of ZnO, thereby reducing the electron depletion layer width. Thus, the resistance of the sensor decreased. For the Ag/Pd–ZnO nanoplate sample, when the H2 molecule was introduced, the sample was split into two active atoms (i.e., H atoms) due to the spillover effect of the Ag/Pd nanoparticles, according to eqn (5).57 Then, these atoms with high mobility easily reacted with the preabsorbed oxygen species, thereby enhancing the response, according to eqn (6) and (7).
In addition, the formation of the barrier height at the interface of the Ag/Pd nanoparticles and the surface of ZnO also contributed to the enhancement of gas sensing properties. The electron transfer from the ZnO nanomaterial to Ag/Pd was clearly bent at the interface between ZnO and Ag/Pd alloy due to the difference in work function (ΦZnO = 4.75 eV, ΦPd = 5.1 eV, and ΦAg = 4.9 eV). Thus, the barrier potential of the doped ZnO became higher than that of the undoped one, as shown in (Fig. 11C). When H2 gas was injected into the sensor, the barrier height tended to decrease, and the depletion layer width became smaller than that in air. However, when Ag/Pd nanoparticles were decorated on the ZnO surface, H2 molecules adsorbed on the bimetallic surface would be dissociated and chemisorbed into the metal hydride form. This metal hydride had a lower work function compared with ZnO, resulting in the transfer of electrons from the metal hydride to ZnO bulk. This phenomenon led to the return of numerous electron carriers to the conduction band of ZnO, resulting in a decrease in the resistance of the sensor.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: https://doi.org/10.1039/d3ra01436c |
This journal is © The Royal Society of Chemistry 2023 |