Journal of Nanotechnology
Volume 2016 (2016), Article ID 7016926, 5 pages
http://dx.doi.org/10.1155/2016/7016926

Research Article

Flame Spray Synthesis and Ammonia Sensing Properties of Pure α-MoO₃ Nanosheets

Gagan Jodhani, Jiahao Huang, and Perena Gouma

Department of Materials Science and Chemical Engineering, Stony Brook University, 100 Nicolls Road, Stony Brook, NY 11794, USA

Received 30 June 2016; Accepted 8 November 2016

Academic Editor: Carlos R. Cabrera

Copyright © 2016 Gagan Jodhani et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

This paper highlights the flame spray synthesis of α-MoO₃ using ammonium molybdate as precursor. The as-synthesized particles obtained were found to be ammonium molybdenum oxide and belonged to the triclinic crystal system. The particles crystallized to α-MoO₃ upon thermal treatment at 500°C. Sensors were prepared by drop coating the powders onto alumina substrates coated with platinum electrodes and sensing tests were conducted evaluating the detection of ammonia concentrations down to ppb level concentration in air. The flame synthesized α-MoO₃ based sensors show high sensitivity towards ammonia and may potentially be used in breath ammonia gas diagnostics.

1. Introduction

The orthorhombic phase of MoO₃, commonly known as α-MoO₃, has been used for variety of applications in gas sensing of ammonia [1, 2], Li-ion intercalation in batteries [3–5], pseudocapacitors [6–8], and hydrogen absorption [9]. Recent studies have led to development of α-MoO₃-polymer composite electrodes with a greatly improved cycling behavior for use in aqueous lithium [10] and sodium [11] rechargeable batteries. The layered structure of the material consists of MoO₆ octahedra held together by Van der Waals forces. The layered structure and the ease of Mo(VI)/Mo(V) coupling enable MoO₃ to be of interest in electrochemical systems [12]. For gas sensing, this polymorph has shown high specificity to detecting ammonia gas through a reaction process involving the reduction of the oxide [13, 14].

α-MoO₃ was synthesized by our research group through various different routes (sol-gel process, sputtering, electron beam deposition, electrospinning, etc. [2, 13, 15]). Also it was studied in diverse configurations (nanoparticles and nanowires [2, 13]). However, in order to be able to manufacture ammonia sensors based on nanostructured α-MoO₃ in large quantities, a scalable nanomanufacturing process needs to be used for the materials synthesis. Flame spray pyrolysis is such a process, and it is explored here for the synthesis of MoO₃. The methodology used to produce particles at a laboratory based FSP setup can be transferred to a foundry for bulk synthesis of the material. Aeroxide P25 Titania from Evonik Industries is an example of commercial Titania nanopowder synthesized via flame aerosol technique. Apart from the commercial aspect, the advantage of flame spray synthesis lies in ease of fabrication, elimination for the use of expensive raw materials, uniform size distribution, and high purity of product. Flame synthesized particles offer small particle size along with high surface-area-to-volume ratios; these characteristics make them desirable for gas sensing and electrochemical applications.

Earlier synthesis by other workers of MoO₃ via flame spray pyrolysis relied on TiO₂ doping to stabilize the α-phase [16]. However, doping agents tend to create long-term stability issues in sensing materials [17] and thus pure α-MoO₃ is the desirable product of FSP processing.

2. Experimental Method

MoO₃ particles were synthesized via flame spray pyrolysis (Tethis nps 10) technique. A 0.68 M solution of ammonium molybdate tetrahydrate (Sigma-Aldrich 277908) was prepared in a mixture of distilled water and dimethylformamide in a ratio of 5 : 1, respectively. The solution was vigorously stirred to obtain a homogenous mixture. The solution was then filled in a syringe and fed into the FSP system at a rate of 5 mL/min. The flame was comprised of 1.5 slm (standard liters per minute) methane and 3.0 slm oxygen gas. A 5 slm oxygen gas flow was used as dispersion gas. The particles obtained after FSP process (as-synthesized particles) were black in color; upon thermal treatment at 500°C for 5 hours, the color of the particles changed to white (calcined).

The powders were characterized using Scanning Electron Microscopy (SEM, LEO 1550) and Transmission Electron Microscopy (TEM, JEOL 1400) and selected area electron diffraction was carried out on both as-synthesized and calcined samples. Thermogravimetric analysis (TGA, Perkin Elmer Diamond) was conducted on the as-synthesized samples. The particles, both as-synthesized and calcined, were also characterized using XRD (Rigaku MiniFlex II) and FTIR (Thermo Scientific Nicolet 6700).

For sensing experiments, sensors were prepared by drop coating a slurry of as-synthesized particles in ethanol on sensor substrates. The sensors were then thermally treated at 500°C for 5 h. Sensing data was collected using a gas flow bench and multimeter. A stable baseline was obtained for the sensors in extra dry air; 485°C was used as the operating temperature. Sensing data was collected for ammonia in the concentration of 4, 2.5, 1, and 0.5 ppm.

3. Results and Discussion

3.1. Phase Characterization and Thermal Stability

XRD data for powders before and after thermal treatment was obtained (Figure 1(a)). The XRD pattern obtained for as-synthesized powders coincides with JCPDS file 80-0757, which is for triclinic ammonium molybdenum oxide (NH₄)₂(Mo₄O₁₃). The formation of compound can be attributed to the flame degradation of precursor, ammonium molybdate tetrahydrate, and entrapment of ammonia and water vapors inside the powders during particle formation. In case of XRD for powders upon calcination the peaks observed coincide with JCPDS file 05-508, which is for α-MoO₃. The FTIR analysis of the powders is shown in Figure 1. In case of the FTIR spectrum for as-synthesized powders, peaks are noticed at 840, 850, 980, 1400, 1640, and 3140 cm⁻¹. The peaks at 3140 and 1640 cm⁻¹ can be attributed to water as per NIST database [18]; the peaks at 840 and 980 cm⁻¹ relate to N-H bonds and inclusion of NH₃ in the sample [18]. Only one peak found at 850 cm⁻¹ relates to the Mo-O-Mo [19]. For powders received upon thermal treatment, peaks were noticed at 818, 850, and 999 cm⁻¹. The strong peak at 850 and the weak peak at 818 cm⁻¹ are a result of Mo-O-Mo bond, with the weak peak being a resultant of asymmetric molybdenum stretching [19]. The strong peak at 999 cm⁻¹ is a result of Mo=O [19, 20], which indicates a layered structure. No peaks were obtained for water, indicating that the water molecules included in the precursor were decomposed during processing.

(a)

(b)

Figure 1: (a) XRD pattern on as-synthesized and calcined MoO₃ powders. (b) FTIR pattern on as-synthesized and calcined MoO₃ powders.

Thermogravimetric analysis was performed on the as-synthesized powders from room temperature to 580°C under oxygen atmosphere. Figure 2 shows the effect of temperature on the powders. A sharp drop in the weight is noticed at 325°C, indicating the decomposition of ammonium salt and formation of α-MoO₃. The decomposition temperature for (NH₄)₂(Mo₄O₁₃) was found to be in accordance with the literature [21], where an endothermic reaction was reported at 317°C; NH₃  and H₂O were the decomposition products and α-MoO₃ was reported as the final product. No change was noticed upon further increasing the temperature to 550°C or during the cooling process indicating formation of a thermally stable phase.

Figure 2: TGA analysis of as-synthesized powders.

3.2. Particle Morphology

Figure 3 shows the Scanning Electron Micrographs obtained for as-received (Figures 3(a) and 3(b)) and calcined (Figure 3(c)) MoO₃ powders. Metal oxides in the form of nanorods (20–40 nm diameter covering spheres (~1 µm diameter)) were observed for the as-received powders. Since the morphology of α-MoO₃ is usually in the form of nanorods/nanosheets/nanoribbons, due to its layered structure, the nanorods found on spherical particles of as-synthesized material were characterized using TEM and SAED (Figure 3(d)). The nanorods were found to be amorphous; SAED pattern picked up signals from lowly crystalline particles in the background. However, no evidence was found for the existence of α-MoO₃ in as-synthesized samples. The micron sized particles, which were spherical in nature, were of ammonium molybdenum oxide and a product of the FSP synthesis.

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(b)

(c)

(d)

Figure 3: Scanning Electron Micrographs of (a) as-synthesized molybdenum particles. (b) High magnification image of as-synthesized molybdenum particles. (c) Molybdenum particles after thermal treatment. (d) TEM image of nanorods in as-synthesized samples.

For the calcined powders, the morphology observed was nanosheets with thicknesses in the range of 20–40 nm, width in the range of 700–800 nm, and length in the range of 1–1.5 µm. Such morphology was reported earlier for flame synthesized MoO₃ in doped form [16] and by our group for MoO₃ obtained after thermal degradation of electrospun mats [2]. The formation of the nanosheets is due to the low energy configuration for α-MoO₃ particles. The thermodynamically stable form consists of 2 similar chains of MoO₆ octahedra aligned in configuration [22]. The as-synthesized particles reported here are bigger compared to those reported earlier due to higher concentration of precursor (increased agglomeration in chamber) and lower flame temperature (incomplete evaporation of particles).

3.3. Ammonia Sensing

The calcined MoO₃ particles were tested as ammonia sensor operated at 485°C in extra dry air and ammonia in the concentration (denoted by on graphs) of 4 ppm, 2.5 ppm, 1 ppm, and 0.5 ppm. The sensors showed fast response time of 40 seconds. The sensing data is plotted against time, as can be seen in Figure 4(a); (1 axis) versus time represents the change in resistance when a signal of ammonia was introduced; (2 axis) versus time represents the times when a 3-second pulse of ammonia was introduced. The sensors were found to show high sensitivity; the sensitivity of the sensors at different concentrations of ammonia is shown in Figure 4(b).

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(b)

Figure 4: (a) Sensing data for ammonia at 485°C. (b) Sensitivity plot for ammonia.

The sensors showed a fast response to ammonia, with a strong drop in resistance, even at low concentration. Most of the earlier reported MoO₃ based ammonia sensors have been shown to detect 10 ppm or higher concentrations of ammonia. Gouma et al. [15] have been able to detect concentrations of ammonia down to 50 ppb using spin coated MoO₃ synthesized through sol-gel process. The current flame synthesized sensor was not tested for such low concentration, however, when the two sensors are compared for their sensitivity for 1 ppm of ammonia; the flame synthesized sensors show a slightly better sensitivity (0.2) compared to spin coated ones (0.14). The sol-gel derived sensor showed a sensitivity of 0.012 at 50 ppb concentrations; the FSP sensor, although not tested for low ammonia concentration, can be expected to perform at the same level as the sol-gel derived sensor. The comparable performance of the FSP derived sensor to sol-gel opens the path for commercial synthesis of the sensors for breath diagnostics. In their current form, the flame synthesized sensors show a sensitivity of .05 at 500 ppb range and serve as better sensors in automotive applications [23].

4. Conclusion

Our study successfully demonstrates the synthesis of pure undoped α-MoO₃ through flame spray pyrolysis process. The sensors obtained show fast response and recovery times, good sensing resolution, and high sensitivity at low concentrations of ammonia. Moreover, the sensing results were found to be comparable to sol-gel derived sensor developed for breath diagnostics. Hence, the synthesis method opens the pathway for commercial synthesis of α-MoO₃ sensors for breath diagnostics.

Competing Interests

The authors state that there are no competing interests regarding the publication of this paper.

Acknowledgments

This project was sponsored by National Science Foundation DMR no. 1106168. Research was carried out in part at the Center for Functional Nanomaterials, Brookhaven National Laboratory, which is supported by the US Department of Energy, Office of Basic Energy Sciences, under Contract no. DE-SC0012704.

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