The La_1−xSr_xCrO₃ (x = 0.0, 0.1, 0.2, 0.3 & 0.4) were synthesized by sol-gel method using poly ethylene glycol as a solvent. La(NO₃)₃·6H₂O, Sr(NO₃)₂, Cr(NO₃)₃·9H₂O and citrate acid (all analytically pure) were firstly dissolved in ion free water at 80˚C for 2 h. Then ethylene glycol was added under constant stirring to obtain a homogeneous and stable sol. The solution was further heated in pressure vessel at about 140˚C for 14 h. During this reaction transparent solution was transform into a gel state with very high viscosity. The material was then heated in a furnace at 350˚C for 3 h and a violent combustion was occurs which spontaneously propagates until all the gel was burnt out to form a loose powder. The powder was then calcined at 800˚C for 6 h in order to improve the crystallinity of materials.

The synthesized samples were characterized by powder XRD using a Siemens D 5000 diffractometer .The XRD data were recorded by using Cu Kα radiation (1.5406 Å). The intensity data were collected over a 2θ range of 10˚ - 70˚. The average crystallite size of the samples was estimated with the help of Scherrer equation using the diffraction intensity of all prominent lines. TEM examination of the synthesized powder was performed using an H-800 electron microscope.

For gas sensing properties, the calcined powder was then mixed with 2% PVA (polyvinyl alcohol) as a binder and 5% ethanol as a solvent; the resulting paste was coated onto an Al₂O₃ tube provided with platinum wires as electrodes at each end. The Al₂O₃ tube was about 8 mm in length, 2 mm in external diameter and 1.6 mm in internal diameter. A small Ni-Cr alloy coil was placed inside the tube to serve as a heater, which provided operating temperatures from 50˚C - 350˚C. The temperature was controlled by adjusting the heating power. Finally, the sensor was sintered at 600˚C for 1 h so that the PVA decomposes and strength of the element markedly increases. The different test gases are injected into the specimen chamber through an inlet. The sensing performance of the sensors was examined using the “flow gas sensing system”.

The gas sensing studies were carried out on a static gas sensing system under normal laboratory conditions. The electrical resistance of thick films in air (R_a) and in the presence of H₂S (R_g) was measured to evaluate the Sensitivity (S) and is given by the relation,

where R_a is the resistance of the La_1−xSr_xCrO₃ thick films in air and R_g is the resistance of the La_1−xSr_xCrO₃ thick films in H₂S atmosphere. The response of the sensor for H₂S was tested in the presence of other gases so that the selectivity can be determined. The response and recovery time of the sensor was measured.

The XRD patterns of the precursor powders LaCrO₃ and La_0.7Sr_0.3CrO₃ calcined at 800˚C for 6 h are shown in Figure 1. Figure 1(a), shows the XRD pattern of LaCrO₃, which is in good agreement with XRD results previously reported in the literature [16]. All the diffraction peaks of the phases are indexed as perovskite-type with tetragonal structure. The diffraction data is good agreement with JCPD card of LaCrO₃ (JCPDS No.24-1016). Figure 1(b), shows the XRD pattern of La_0.7Sr_0.3CrO₃ nanomaterial, which indicates that ions Sr²⁺ partially substitute for ions La³⁺ in the LaCrO₃ crystal lattice. The ionic radii of Sr²⁺ (1.21 Å) are very close to that of La³⁺ and Sr is incorporated into the LaCrO₃ lattice at the La site. The mean crystallite sizes (D) of La_0.7Sr_0.3CrO₃ powder was deduced from half height width of XRD peaks based on the Scherer’s equation, t = 0.9λ/βcosθ, where t is the average size of the particles, λ is wavelength of X-ray radiation, β the full width at half maximum of the diffracted peak and θ is the angle of diffraction [17]. Extremely broad reflections are observed indicating nanosized particle nature of the material obtained. The average particle size of the nanocrystalline La_0.7Sr_0.3CrO₃ according to the scherrer formula was in the range of 30 - 35 nm.

The TEM specimens were prepared by placing microdrops of colloid solutions on a carbon film supported by

a copper grid. The TEM images of the nanocrystalline La_0.7Sr_0.3CrO₃ calcinated at 800˚C is shown in Figure 2. It indicates the presence of La_0.7Sr_0.3CrO₃ nanoparticles with 30 - 50 nm size which form spherical type of oriental aggregation, agglomeration and polymeric linkage throughout the region.

Electrical characterization of samples La_1−xSr_xCrO₃ (x = 0.1, 0.2, 0.3 & 0.4) synthesized by sol-gel method and calcinied at 800˚C has been carried out in a gas test chamber. The resistance of the films was measured by using Equation (1). The resistance of the films decreased upon exposure to H₂S gas. Figure 3 shows gas sensing response of H₂S gas, at different operating temperatures (50˚C - 400˚C) for thick films of pure LaCrO₃. It is observed that response for pure LaCrO₃ is obtained at high operating temperature 350˚C, than decreases as increase in operating temperature. At a low operating temperature, the low response can be expected because the gas molecules do not have enough thermal energy to react with the surface adsorbed oxygen species. As the temperature increases, the thermal energy obtained was high enough to overcome the potential barrier, and a significant increase in electron concentration resulted from the sensing reaction. The response of semiconductor oxide gas sensor to the presence of a given gas depends on the speed of the chemical reaction on the surface of the grains and the speed of diffusion of the gas molecules to that surface which are activation processes, and the activation energy of the chemical reaction is higher. In this case, at low temperatures the sensor response is restricted by the speed of the chemical reaction, and at higher temperatures (above 350˚C) it is restricted by the speed of diffusion of gas molecules. At some intermediate temperature (at 350˚C), the speed, values of the two processes be-

come equal, and at that point the sensor response reaches its maximum [18].

Thus, the pure LaCrO₃ shows response towards H₂S gas at high operating temperature 350˚C, which is rather high and practically inconvenient in view of commercial standards. Therefore, efforts were made to modify the LaCrO₃ based sensors by doping with Sr, so as to be operated at lower operating temperatures with high sensitivity and selectivity. Figure 4 shows gas sensing response of H₂S gas, for thick films of pure LaCrO₃ doped with different concentrations of Sr. From the figure it is clear that the response values of every doped sample apparently increased with increasing the operating temperature. In this figure, it is observed that the La_0.7Sr_0.3CrO₃ thick film had the largest sensing response at an operating temperature 210˚C. It is indicating that Sr doping can greatly improve the sensitivity of LaCrO₃ based sensor towards H₂S gas. We know that the semiconductor oxide gas sensors can detect different gases by changing the conductivity of their surface due to the reaction of the reducing gases with adsorbed oxygen. Sr doping in La-

CrO₃ promotes the deviation from stoichiometry and enhances the surface defect. A large surface defect concentration creates more active surface states for adsorbed oxygen [19,20].

Selectivity or specificity is defined as the ability of a sensor to respond to certain gas in the presence of other gases. Figure 5 shows the selectivity of La_0.7Sr_0.3CrO₃ for different gases. It is clear from the figure that La_0.7Sr_0.3CrO₃ sample is more selective to H₂S gas at 210˚C against all other tested gases viz: NH₃, LPG and H₂. As easily seen, the La_0.7Sr_0.3CrO₃ was most selective to H₂S among the gases tested, while it was least selective to NH₃.

The sensor selects a particular gas at a particular temperature. Thus by setting the temperature, one can use the sensor for particular gas detection. The same sensor could be used for the detection of different gases by operating it at particular temperature for a typical gas. This can be attributed to different chemical reactivity’s of different gases on the sensor surface. Different gases have different energies for adsorption, desorption, and reaction on the metal oxide surface, and therefore the response of the sensor at different temperatures would depend on the gas being sensed. The amount of oxygen adsorbed (, O^–, O^2–) on the sensor surface goes on increasing with an increase in temperature, reaches to the maximum and then decreases with a further increase in operating temperature. The response to the gas to be detected follows the same behavior. When a reducing gas comes in contact with the sensor surface, it gets oxidized. The rate of oxidation would be the function of the amount of adsorbed oxygen on the surface and the type of gas to be detected. The larger the rate of oxidation, the larger would be the number of electrons released, and in turn the larger would be the gas response. At higher temperatures, the amount of oxygen adsorbed would be smaller, leading to a slower rate of reduction of a target gas and, therefore, the smaller gas response.

Figure 6 depicts the variation of sensitivity of La_0.7Sr_0.3CrO₃ sample with H₂S gas concentrations at 210˚C temperature. It is clear from the figure that the gas response goes on increasing linearly with gas concentration up to 200 ppm and saturated beyond it. The rate of increase in gas response was relatively larger up to 200 ppm. It is observed that as the concentration of H₂S gas increases, the average sensitivity increases linearly in the beginning and later it becomes saturated. The linear relationship between sensitivity and gas concentration may be attributed to the availability of sufficient number of sensing sites. The low concentration implies a lower surface coverage of gas molecules, resulting in a lower surface reaction between the surface adsorbed oxygen species and the gas molecules. The increase in H₂S gas concentration increases the surface reaction due to a large surface coverage. Further on increasing the H₂S gas concentration, the surface reaction does not increase and eventually saturation takes place. Thus, the maximum sensitivity was obtained at higher concentration of H₂S gas, i.e., 200 ppm.

The response and recovery time is an important parameter, used for characterizing sensors. It is defined as the time required to reach 90% of the final change in voltage or resistance, when the gas is turned on or off, respectively. The response and recovery times of La_0.7Sr_0.3CrO₃ sample is represented in Figure 7. The response was quick (~20 s) to 200 ppm of H₂S while the recovery was moderate (~60 s). The quick response may be due to faster oxidation of gas. Its high volatility explains its quick response .The large recovery time would be due to lower operating temperature. At lower temperature O₂^- species is more prominently adsorbed on the surface and thus it is less reactive as compared to other species of oxygen, O^– and O².

The long-term stability is another important factor for gas sensors. The stability of the La_0.7Sr_0.3CrO₃ nanocrystalline based sensor was studied in the presence of 200 ppm H₂S gas for fifty day at 210˚C. Repeated experi-

ments were carried out and it was observed that both La_0.7Sr_0.3CrO₃ sensor showed good response performance even after 50 days (shown in Figure 8). It is observed that its resistance is stable except for a small variation for first ten days. This indicates that the present nanocrystalline La_0.7Sr_0.3CrO₃ sensor can be effectively used as H₂S gas sensor.