Tuning of WO3 Phase Transformation and Structural Modification by Reactive Spray Deposition Technology

1Department of Materials Science and Engineering, University of Connecticut, 97 North Eagleville Road, Unit 3136 Storrs, CT 06269. 2Department of Chemical and Biomolecular Engineering, University of Connecticut, 191Auditorium Road, Unit 3222 Storrs, CT 06269. 3Center for Clean Energy Engineering, University of Connecticut, 44 Weaver Road, Unit 5233 Storrs, CT 06269. 4Institute of Materials Science, University of Connecticut, 97 North Eagleville Road, Unit 3136 Storrs, CT 06269. Research Open Access


Reactive Spray Deposition Technology
tual e --h + recombination [46,47]. Polycrystalline WO 3 film has almost no photochromic sensitivity whereas amorphous WO 3 has high photochromic and electrochromic sensitivity due to high surface area [48,49]. However, some phases of WO 3 such as ε-monoclinic is metastable at room temperature and higher temperature, thereby making it challenging to obtain such phase by the traditional synthesis processes. Here we have demonstrated a one-step flame-based direct deposition technique to engineer a particular required phase by changing the length of the reaction zone in the flame, flow rate of quench air, and the substrate temperature. RSDT is a type of flame spray pyrolysis system which is employed for synthesizing nano scale materials with high efficiency and reduced solvent waste. Here we will give a brief description of the RSDT process and, the conditions required to achieve a particular phase, and we will provide characterization results obtained by Raman spectroscopy, SEM, TEM, and XRD that prove the existence of the phases. The motivation of this research was to study the particle size, crystallinity and crystal structure of the WO 3 films grown by RSDT by varying the conditions of the experiments. It is assumed that the results from this study can be used to obtain the configuration of WO 3 film demanded by its application.
Reactive Spray Deposition Technology (RSDT) was developed by Maric et al. for synthesis of nanoparticle thin films with atomic-level precision and control of properties such as phase, structure, shape, particle size distribution (0.5-100 nm), density and porosity, which can employ a broader selection of precursors compared to conventional vapor-fed flame reactors [50][51][52][53][54][55][56][57][58][59][60][61][62][63][64][65][66]. RSDT is a single-step, open atmosphere flame process for synthesizing nano-materials, whereby nano-particles are synthesized in the reaction zone of the flame and directly deposited on the substrate as a film or collected as particles [50][51][52][53][54][55][56][57][58][59][60][61][62][63][64][65][66], thereby eliminating the intermediate steps of filtration, drying, and calcination. No waste is generated because the solvent is combusted in the flame, yielding CO 2 and H 2 O. Precise control of particle size and crystallinity can be achieved by adjusting flame setup conditions, including precursor concentration, chemistry, and flow rate; length of reaction zone; equivalence ratio (stoichiometric oxidant and fuel flow rate to actual oxidant and fuel flow rate); downstream quench air flow rate, and the substrate temperature [53]. In addition to these conditions, flame dynamics is also dependent on the solvent boiling point, enthalpy of combustion of solvent and the combustion nozzle geometry. Results from Roller, et al. [51][52] using RSDT, for Pt based electro-catalysts has clearly shown that the process can be adjusted to give precise control (< 1 nm) on metallic nanoparticle diameters directly deposited onto Nafion® membranes with thickness from ~100 nm to 10 μm. The reactive spray synthesis of nanoparticles relies on combustion of a solvent which also acts as a fuel and aids in the decomposition of a precursor to form nanoparticles. RSDT provides adjustable process variables such as flame temperature, stoichiometry, residence time, and downstream quenching rates that coupled with solvent and metal precursor concentrations, affect particle: nucleation, growth, annealing, and oxidation. Since the droplets produced by this process are mostly sub-micron -due to energetic inputs of heat, pressure, and supercritical propane diluent -the precursor is confined to the nanoscale regime during formation. During the particle formation process the precursor heats up, decomposes, and then undergoes a phase transition to vapor followed by concurrent reduction of the metal ions to metal or metal oxides.

Synthesis of WO 3
An explanation of the RSDT equipment and process is described in detail by Roller, et al. [51] . Tungsten hexacarbonyl (W(CO) 6 ) was obtained from Sigma Aldrich (Catalogue #AC221040100) and was dissolved in a tetrahydrofuran (THF) (Fisher Scientific # SHBD3901V). 20 wt% sulfur free liquefied propane (Airgas catalogue # PRCP350S) was added to the above to form a precursor solution resulting in a final concentration of 5 mM/L W(CO) 6 , and 16.5 wt% propane. Propane assists in the atomization of the precursors by increasing the enthalpy of the solution mixture and reducing the droplet size due to supercritical expansion. The flow rate of 4 mL/min was maintained by using a syringe pump. The precursor solution was atomized by a gas-assisted external mixing nozzle (combustion nozzle) by oxygen (5 L/min). Six methane-oxygen flamelets (methane and oxygen at 0.5 L/min each) surround the capillary end, which ignites the combustible precursor mist. Prior to atomization, the precursor solution was heated to approximately 50-60 ˚C by enclosing the capillary by a heating coil. The precursor mist was ignited with a propane torch to obtain a bluish-white flame. At approximately 9-14 cm from the flame, a circular air quench (Exair, Super Air Wipe®) with a compressed air flow rate of 28-56 L/min at room temperature was positioned. A stainless steel substrate holder mounted on an x-y-z platform and having the option of water cooling was used for collection of WO 3 particles. On the substrate holder was mounted a zero diffraction background quartz plate (MTI®) on which the film was grown. Quartz was selected for various reasons: it can withstand the high temperature required during in-situ XRD, it can be imaged in an SEM, it does not have an interfering background in a Raman spectrometer, and the film can be scraped off for TEM analysis.

Role of air quench
A schematic of the air quench is shown in figure 2. The air quench is a circular ring with an internal annular chamber. The compressed air at room temperature enters the two nozzles and is directed towards that chamber. The chamber has a narrow ring nozzle through which the air adopts the coanda profile and flows along the angled surface of the air quench. This also creates a low pressure region behind the air quench causing the entrainment of the surrounding air into the primary air stream. A 360˚ cone of cold air is formed which cools the nanoparticles instantly and prevents growth, agglomeration, and sintering, thereby keeping the particle size small and increasing the active surface area. The distance between the combustion nozzle and the air quench is considered the reaction zone and the length of the reaction zone is proportional to the residence time of the nano-particles in the zone. Adjusting the length of the reaction zone and the flow rate of compressed air gives unique conditions to obtain an assortment of phases and structures of WO 3.

Characterization
In-situ X-ray diffraction patterns of WO 3 film were recorded in air at 30 ˚C, 150 ˚C, 250 ˚C, 300 ˚C, 350 ˚C, 400 ˚C and 500 ˚C on a Bruker D8 advanced powder diffractometer using CuKα radiation. Heating rate of 5 ˚C /min was used with a hold time of 1 hr at the temperature of the scan. Crystallite size was measured by using Debye Scherrer method. Raman spectra were obtained with a Renishaw Ramascope micro-Raman spectrometer fitted with a reflected light microscope using a 50 mW laser (514.5 nm) and exposure time of 30 s at ambient conditions. Instrument alignment was optimized using a 519 cm -1 signal of a silicon wafer. Raman measurements were performed since this technique is well known to give the "fingerprint" of WO 3 material [67]. The spectra were obtained at room temperature in ambient atmosphere in the spectral range between 100 and 1000 cm −1 . SEM micrographs were collected on an FEI ESEM Quanta 250 with a field emission gun with an EDAX XEDS system. TEM micrographs and selected area electron diffraction (SAED) pattern of WO 3 particles were obtained on a 120 kV FEI Technai T12 S/TEM with a LaB 6 source equipped with an EDAX XEDS system. 300 mesh Cu grids coated with holey/thin carbon films (Pacific Grid Tech Cu-300HD) were used. A small portion of the film was scraped off from quartz plate and was sonicated with ethanol. Few drops of the resulting solution were dropped on the grids and air dried before they were placed in the UHV chamber of the TEM. The TEM sample was prepared from the crystalline WO 3 film.

Results and Discussion
X-ray diffraction γ and ε WO 3 with different phase ratio was synthesized in four different set of conditions in RSDT as described in table 1 by altering the length of the reaction zone, flow rate of quench air and temperature of substrate. Figure 3 shows the X-ray diffraction spectra for the samples A, B, C and D. It is clear from the figure that very different structures of WO 3 were obtained by changing the conditions of the flame. All four samples were monoclinic, the most dominant structure of WO 3 and which can be indexed to ICDD#00-043-1035 (space group P21/n). Sample A is the as-prepared sample with no post annealing, and it shows a well crystalline structure with (002) preferential plane oriented at 2θ = 23.1 ˚. This could be due to the high temperature of particles in the absence of quench air which can cause the migration of WO 3 atoms towards the lower energy nucleation sites [68]. All the other samples (with the exception of A) were found to be amorphous in nature because the quench was close to the nucleation site. This amorphous structure could arise because the particles are air quenched as soon as they are produced from the flame and the temperature of the particles and substrate did not exceed 200 ˚C. The amorphous samples were thermally annealed in the high temperature stage of the XRD-the crystallization steps and the corresponding XRD patterns can be found in the supplementary information. Thermal annealing of amorphous WO 3 causes the particles to become crystalline and it also changes the phase ration, grain size, porosity, density of adsorption sites and pore volume [43]. It is clear from in-situ XRD that the crystallization of the WO 3 particles started at 350 ˚C. Sample B was prepared with no air quench; however the substrate temperature was maintained at 200 ˚C by the water cooled substrate holder and the sample thereby retained an amorphous structure. By comparing the XRD pectra of sample B with that of Wang, et al. [29] and Righet-J Nanotech Smart Mater 2013 | Vol 1: 203 toni, et al. [45] it can be concluded that the sample is mostly ε-WO 3 , the metastable phase at room temperature. Sample C is oriented preferentially along the (200) direction. This preferentially-oriented crystallization was also observed by Sun, et al. [69] and Zhifu, et al. [43] who prepared their films by physical vapor deposition (PVD). Sun et al. suggested that preferential orientation along the (200) direction happened to reduce the lattice mismatch with the sapphire lattice on which the film was grown. According to Zhifu, et al. the cause of this behavior was the column-like accumulation of the WO 3 species during the sputtering process at the operating pressure 20 Pa. The (200) orientation could also form in-situ during the annealing process. Sample D is oriented along the (020) plane direction, and sample A is oriented along the (002) direction, as was also reported by Garavand, et al. [70] Guo, et al. [71] and Jing, et al. [46]. Guo, et al. evaluated the photoelectrochemical activity and photoconversion efficiency of self-assembled nanoporous WO 3 and WO 3 film with preferential orientations at (002) and (020), respectively. They found that the photocurrent of the (002) plane-oriented WO 3 was 9 times the value and the photoconversion efficiency was 4.57 times higher than those of (020) plane-oriented WO 3 . Furthermore, (002) WO 3 was more favorable in absorption and redox of pollutants than (020) WO 3 . Jing, et al. found that the (002) preferential orientation of WO 3 resulted in higher photocatalytic degradation of NO [46].  The spectra are similar to those of the monoclinic WO 3 as apparent from the strong peaks at 808 and 715 cm -1 . The peak at 450 cm -1 can be assigned to the quartz substrate as determined by the scan of quartz substrate without any film. The intensity of the substrate peak is different for the samples because of the difference in the thickness of the film. A relatively strong peak is obtained at below 150 cm -1 for all the samples which can indicate the O-O deformation mode [72]. Salje et al. has obtained the Raman spectra of the monoclinic (γ and ε) WO 3 and is reported in reference [72], [73]. After comparing with Salje, et al. it can be assumed that the peaks at 205, 310, 372, 394, 427, 645, 680, 697cm -1 can be assigned to ferroelectric ε-WO 3 while peaks at 327, and 716 cm -1 are for γ-WO 3 only. There is clearly an overlap between γ and ε WO 3 as evident from the spectra.

Electron Microscopy
Scanning Electron Microscopy Figure 5 shows the SEM micrographs of the WO 3 film as deposited (top) and after annealing at 500 ˚C. Films A and D are very homogeneous while B and C shows particle agglomeration. As is clear from the figure, the size of the grains are in the order B>D>A>C. Pores and cracks can be seen in Raman Spectroscopy J Nanotech Smart Mater 2014 | Vol 1: 203 samples A and D while samples B and C show uniform morphology. It is interesting to see that in samples A and D, the pores and cracks have grown in size after annealing at 500 ˚C. This same phenomenon was observed by Santato, et al. and could be due to the elimination of organics from the film surface after heat treatment [74]. Increase in porosity of the films is advantageous to the sensing function of WO 3 since this favors diffusion of analytes in the bulk of the film. The images indicate high quality of WO 3 films deposited by RSDT. Figure 6 shows the bright field TEM micrographs along with the SAED pattern of samples A-D after post annealing. All samples were polycrystalline, as evident from the SAED pattern and were indexed to monoclinic WO 3 . As measured from the micrographs the size of the WO 3 particles were 15-40 nm for sample A, 30-50 nm for sample B, 20-25 nm for sample C, and 20-30 nm for sample D. Different shapes and sizes of particles were seen from the micrographs, as labelled. Sample A shows faceted particles with edges and corners. Samples B and D show circular particles, whereas circular, oval, elliptical, and dumb bell shaped particles can be seen in sample D. Only sample B depicts the formation of necks between individual WO 3 particles.

Transmission Electron Microscopy
Reactive Spray Deposition Technology was employed to synthesize WO 3 (γ and ε phase) thin films of from the vapor phase.

Conclusions
The morphology, structure and preferential lattice plane orientation was tuned by changing the parameters of the flame setup including substrate temperature, quench air flow rate and length of reaction zone. It was determined that the particular structure and properties of WO 3 are a function of the synthesis process. By employing the RSDT, the properties of WO 3 can be tuned to be favorable towards a particular application. Our next publication will elaborate upon this technique for exploring the sensing function of WO 3 by changing the synthesis conditions.