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Effects of SO2 and H2O on low-temperature NO conversion over F-V2O5-WO3/TiO2 catalysts
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Effect of water in a non-aqueous electrolyte on electrochemical Mg2+ insertion into WO3
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Data from Reactive Species and Reaction Pathways for the Oxidative Cleavage of 4-Octene and Oleic Acid with H2O2 over Tungsten Oxide Catalysts
Oxidative cleavage of carbon–carbon double bonds (C═C) in alkenes and fatty acids produces aldehydes and acids valued as chemical intermediates. Solid tungsten oxide catalysts are low cost, nontoxic, and selective for the oxidative cleavage of C═C bonds with hydrogen peroxide (H2O2) and are, therefore, a promising option for continuous processes. Despite the relevance of these materials, the elementary steps involved and their sensitivity to the form of W sites present on surfaces have not been described. Here, we combine in situ spectroscopy and rate measurements to identify significant steps in the reaction and the reactive species present on the catalysts and examine differences between the kinetics of this reaction on isolated W atoms grafted to alumina and on those exposed on crystalline WO3 nanoparticles. Raman spectroscopy shows that W–peroxo complexes (W–(η2-O2)) formed from H2O2 react with alkenes in a kinetically relevant step to produce epoxides, which undergo hydrolysis at protic surface sites. Subsequently, the CH3CN solvent deprotonates diols to form alpha-hydroxy ketones that react to form aldehydes and water following nucleophilic attack of H2O2. Turnover rates for oxidative cleavage, determined by in situ site titrations, on WOx–Al2O3 are 75% greater than those on WO3 at standard conditions. These differences reflect the activation enthalpies (ΔH‡) for the oxidative cleavage of 4-octene that are much lower than those for the isolated WOx sites (36 ± 3 and 60 ± 6 kJ·mol–1 for WOx–Al2O3 and WO3, respectively) and correlate strongly with the difference between the enthalpies of adsorption for epoxyoctane (ΔHads,epox), which resembles the transition state for epoxidation. The WOx–Al2O3 catalysts mediate oxidative cleavage of oleic acid with H2O2 following a mechanism comparable to that for the oxidative cleavage of 4-octene. The WO3 materials, however, form only the epoxide and do not cleave the C–C bond or produce aldehydes and acids. These differences reflect the distinct site requirements for these reaction pathways and indicate that acid sites required for diol formation are strongly inhibited by oleic acids and epoxides on WO3 whereas the Al2O3 support provides sites competent for this reaction and increase the yield of the oxidative cleavage products.
Materials Data on W4NO12 by Materials Project
(WO3)8N2 crystallizes in the trigonal P-31m space group. The structure is three-dimensional and consists of three ammonia molecules and one WO3 framework. In the WO3 framework, there are two inequivalent W+5.25+ sites. In the first W+5.25+ site, W+5.25+ is bonded to six O2- atoms to form corner-sharing WO6 octahedra. The corner-sharing octahedra tilt angles range from 0–28°. There are a spread of W–O bond distances ranging from 1.87–2.02 Å. In the second W+5.25+ site, W+5.25+ is bonded to six O2- atoms to form corner-sharing WO6 octahedra. The corner-sharing octahedra tilt angles range from 0–28°. There are a spread of W–O bond distances ranging from 1.87–2.02 Å. There are five inequivalent O2- sites. In the first O2- site, O2- is bonded in a linear geometry to two equivalent W+5.25+ atoms. In the second O2- site, O2- is bonded in a linear geometry to two equivalent W+5.25+ atoms. In the third O2- site, O2- is bonded in a linear geometry to two W+5.25+ atoms. In the fourth O2- site, O2- is bonded in a bent 150 degrees geometry to two equivalent W+5.25+ atoms. In the fifth O2- site, O2- is bonded in a bent 150 degrees geometry to two equivalent W+5.25+ atoms.
Materials Data on W2O7 by Materials Project
(WO3)4O2 crystallizes in the cubic Fd-3m space group. The structure is three-dimensional and consists of eight water molecules and one WO3 framework. In the WO3 framework, W is bonded to six equivalent O atoms to form corner-sharing WO6 octahedra. The corner-sharing octahedral tilt angles are 37°. All W–O bond lengths are 1.94 Å. O is bonded in a bent 150 degrees geometry to two equivalent W atoms.
Materials Data on W3NO9 by Materials Project
(WO3)6N2 crystallizes in the hexagonal P6_3/mcm space group. The structure is three-dimensional and consists of two ammonia molecules and one WO3 framework. In the WO3 framework, W5+ is bonded to six O2- atoms to form corner-sharing WO6 octahedra. The corner-sharing octahedra tilt angles range from 0–29°. There are a spread of W–O bond distances ranging from 1.87–2.02 Å. There are two inequivalent O2- sites. In the first O2- site, O2- is bonded in a bent 150 degrees geometry to two equivalent W5+ atoms. In the second O2- site, O2- is bonded in a linear geometry to two equivalent W5+ atoms.
Materials Data on W2NO6 by Materials Project
(WO3)4N2 crystallizes in the cubic Fd-3m space group. The structure is three-dimensional and consists of eight ammonia molecules and one WO3 framework. In the WO3 framework, W+4.50+ is bonded to six equivalent O2- atoms to form corner-sharing WO6 octahedra. The corner-sharing octahedral tilt angles are 36°. All W–O bond lengths are 1.94 Å. O2- is bonded in a bent 150 degrees geometry to two equivalent W+4.50+ atoms.
Materials Data on PH24W12C6N3O40 by Materials Project
(WO3)12((CH3)2NH2)3PO4 crystallizes in the trigonal R-3m space group. The structure is zero-dimensional and consists of eighteen dimethylazanium molecules, six phosphoric acid molecules, and six WO3 clusters. In each WO3 cluster, there are three inequivalent W sites. In the first W site, W is bonded in a 5-coordinate geometry to five O atoms. There is one shorter (1.73 Å) and four longer (1.95 Å) W–O bond length. In the second W site, W is bonded in a 5-coordinate geometry to five O atoms. There are a spread of W–O bond distances ranging from 1.74–1.95 Å. In the third W site, W is bonded in a 5-coordinate geometry to five O atoms. There are a spread of W–O bond distances ranging from 1.74–1.95 Å. There are nine inequivalent O sites. In the first O site, O is bonded in a bent 120 degrees geometry to two equivalent W atoms. In the second O site, O is bonded in a bent 150 degrees geometry to two equivalent W atoms. In the third O site, O is bonded in a bent 120 degrees geometry to two equivalent W atoms. In the fourth O site, O is bonded in a bent 150 degrees geometry to two W atoms. In the fifth O site, O is bonded in a single-bond geometry to one W atom. In the sixth O site, O is bonded in a single-bond geometry to one W atom. In the seventh O site, O is bonded in a bent 120 degrees geometry to two W atoms. In the eighth O site, O is bonded in a bent 150 degrees geometry to two equivalent W atoms. In the ninth O site, O is bonded in a single-bond geometry to one W atom.
Structure-Activity Relationships of Hydrothermally Aged Titania-Supported Vanadium-Tungsten Oxide Catalysts for SCR of NOx Emissions with NH3
Supported V2O5-WO3/TiO2 materials employed as selective catalytic reduction (SCR) catalysts for NOx emission control from power plants. Fresh SCR catalysts usually receive exposure to harsh treatments in industry to accelerate catalyst activation (calcination in air at 650oC) and catalyst aging (hydrothermal aging at 650oC) in a way that represents various points in the catalyst/product lifetime. The present study investigates the catalyst structural and chemical changes occurring during such harsh treatments. Three series of supported V2O5-WO3/TiO2 catalysts were prepared by incipient-wetness impregnation of aqueous ammonium metavanadate and metatungstate precursors. The catalysts were subsequently dried and calcined at 550oC in O2, 650oC in O2, and hydrothermal conditions (10% O2, 8% H2O, 7% CO2 and 75% N2) at 650oC. The resulting catalysts were physically characterized by numerous techniques (in situ Raman, in situ IR, in situ High Field-High Spinning solid-state 51V MAS NMR, in situ EPR, XRD, BET surface area and ICP) and chemically probed with adsorbed ammonia, SCR-TPSR, and the SCR reaction. The surface WOx sites on the TiO2 support behave as a textural promoter that stabilizes the TiO2 (anatase) phase from sintering and transforming to the undesirable crystalline TiO2 (rutile) phase that can lead to formation of a Ti1-xVxO2 (rutile) solid solution with reduced V4+ cations (~7-15%). The surface VOx sites are mostly oligomerized as surface V+5Ox sites (~50-85% oligomers) and the extent of oligomerization tends to increase with surface WOx coverage and calcination temperature. A major difference between the calcined and hydrothermally treated catalysts was the low concentration of surface NH3* species on Lewis acid sites for the hydrothermally treated catalysts, yet the SCR activity was almost comparable for both catalysts. This finding suggests that surface NH4+*, primarily associated with the surface VOx sites, are able to efficiently perform the SCR reaction. Given that multiple catalyst parameters were simultaneously varying during these treatments, it was difficult to correlate the SCR activity with any single catalyst parameter. A correlation, however, was found between the SCR TOF/activity and the sum of the surface NH3* and NH4+* species, which is dominated by the surface NH4+* species.
Direct Observation of Tungsten Oxidation Studied by In Situ Environmental TEM
In this study, in situ environmental transmission electron microscopy (ETEM) was applied, for the first time, to investigate the thermal oxidation of a pristine and a self-ion irradiated polycrystalline tungsten, using a MEMS-based gas cell at 500 oC to 900 oC in a 1 bar 2%O2/N2 gas mixture. By tracking the dynamic evolution of the tungsten oxide scale as it initiates, grows, and sublimates during a consecutive thermal oxidation experiment, we observed two distinctive tungsten oxide microstructure – one nanocrystalline o-WO3 scale grown on W{27-1 } and W{1-1 8} and another o-WO3 scale exhibits a novel highly textured nanostructure. While the two oxide microstructures shared a similar thickness of ~200 nm after 40-minute early-stage oxidation, the nanocrystalline scale on the W{27-1 } grew much more rapidly at 800 oC than the highly textured oxide at a higher temperature of 900 oC. This suggests both the microstructure of these tungsten oxide scales as well as their oxidation kinetics are highly sensitive to the tungsten surface orientation, and such correlations also change dynamically in the course of oxidation. We also discuss the tungsten oxidation mechanism, the effects of the TEM foil thickness, and the focused ion beam (FIB) Ga+ damage on in situ ETEM oxidation.
Materials Data on AlWO3 by Materials Project
WO3Al is (Cubic) Perovskite structured and crystallizes in the tetragonal P4/mmm space group. The structure is three-dimensional and consists of one aluminium molecule and one WO3 framework. In the WO3 framework, W3+ is bonded to six O2- atoms to form corner-sharing WO6 octahedra. The corner-sharing octahedral tilt angles are 0°. There are four shorter (2.00 Å) and two longer (2.05 Å) W–O bond lengths. There are three inequivalent O2- sites. In the first O2- site, O2- is bonded in a linear geometry to two equivalent W3+ atoms. In the second O2- site, O2- is bonded in a linear geometry to two equivalent W3+ atoms. In the third O2- site, O2- is bonded in a linear geometry to two equivalent W3+ atoms.
Materials Data on WO5 by Materials Project
WO5 crystallizes in the monoclinic P2_1 space group. The structure is one-dimensional and consists of four hydrogen peroxide molecules and two WO3 ribbons oriented in the (0, 1, 0) direction. In each WO3 ribbon, W is bonded in a 5-coordinate geometry to five O atoms. There are a spread of W–O bond distances ranging from 1.73–2.18 Å. There are three inequivalent O sites. In the first O site, O is bonded in a distorted trigonal planar geometry to three equivalent W atoms. In the second O site, O is bonded in a single-bond geometry to one W atom. In the third O site, O is bonded in a single-bond geometry to one W atom.
Emulation of Synaptic Plasticity in WO 3 ‐Based Ion‐Gated Transistors
Neuromorphic systems, inspired by the human brain, promise significant advancements in computational efficiency and power consumption by integrating processing and memory functions, thereby addressing the von Neumann bottleneck. This paper explores the synaptic plasticity of a WO3-based ion-gated transistor (IGT) in [EMIM][TFSI] and a 0.1 mol L −1 LiTFSI in [EMIM][TFSI] for neuromorphic computing applications. Cyclic voltammetry (CV), transistor characteristics, and atomic force microscopy (AFM) force–distance (FD) profiling analyses reveal that Li + brings about ion intercalation, together with higher mobility and conductance, and slower response time (τ). WO 3 IGTs exhibit spike amplitude-dependent plasticity (SADP), spike number-dependent plasticity (SNDP), spike duration-dependent plasticity (SDDP), frequency-dependent plasticity (FDP), and paired-pulse facilitation (PPF), which are all crucial for mimicking biological synaptic functions and understanding how to achieve different types of plasticity in the same IGT. The findings underscore the importance of selecting the appropriate ionic medium to optimize the performance of synaptic transistors, enabling the development of neuromorphic systems capable of adaptive learning and real-time processing, which are essential for applications in artificial intelligence (AI).
Dehydration of fatty alcohols on zirconia supported tungstate catalysts
Zirconia supported tungstates catalyze octadecanol dehydration, an important step in the carbon preserving conversion of triglycerides to fuels.
Enhancement of Superconductivity in WP via Oxide-Assisted Chemical Vapor Transport
Tungsten monophosphide (WP) has been reported to superconduct below 0.8 K, and theoretical work has predicted an unconventional Cooper pairing mechanism. Here we present data for WP single crystals grown by means of chemical vapor transport (CVT) of WO3, P, and I2. In comparison to synthesis using WP powder as a starting material, this technique results in samples with substantially decreased low-temperature scattering and favors a more three-dimensional morphology. We also find that the resistive superconducting transitions in these samples begin above 1 K. Variation in Tc is often found in strongly correlated superconductors, and its presence in WP could be the result of influence from a competing order and/or a non-s-wave gap.
WO 3 /CuWO 4 Ratio Controls Open-Circuit Photovoltage and Photocurrent in Type II Heterojunction Solar Fuel Photoelectrodes
WO 3 /CuWO 4 photoelectrodes for the oxygen evolution reaction benefit from a type II heterojunction for charge separation. However, the impact of the WO 3 /CuWO 4 ratio on the photocurrent and the photovoltage is not clear. To probe the effect of composition, Cu x W 1-x O y thin films with variable W:Cu ratio were prepared on FTO by reactive magnetron co-sputtering of W and Cu, followed by air annealing at 500ºC. EDS, XRD, Rietveld refinement, and Raman spectroscopy confirm the presence of crystalline WO 3 and CuWO 4 in the W rich films and increasing amounts of amorphous copper oxides in the Cu rich films. Bandgaps were determined by optical absorption spectroscopy, surface photovoltage spectroscopy (SPS), and photoaction spectra and are found to decrease from 2.7 eV to 1.2 eV with increasing copper oxide content. SPS reveals n-type semiconductor photoanode behavior for WO 3 /CuWO 4 samples and p-type photocathode behavior for CuO x rich films. Photoelectrochemical experiments confirm stable water oxidation with Faraday efficiency near unity for all W rich films and photocurrents that are increasing with CuWO 4 content. Optimal performance is seen for WO 3 /CuWO 4 mixed phases containing 47-75 mass% CuWO 4 . These compositions maximize charge separation at the type II heterojunction interface between the two materials. Additionally, according to incident photon to current efficiency (IPCE) data, the WO 3 improves photon conversion below 350 nm, while CuWO 4 improves conversion at 450-525 nm. Overall, this work shows for the first time how the WO 3 /CuWO 4 ratio controls the photovoltage and the photocurrent in type II heterojunction solar fuel photoelectrodes, and how copper oxides in the copper rich films severely degrade the performance. Furthermore, these results are useful in the context of bulk-heterojunction electrodes for the conversion of solar energy into fuels.
Sputter-Coated TiO 2 Films as Passivation and Hole Transfer Layers for Improved Energy Conversion with Solar Fuel WO 3 /CuWO 4 Photoanodes
Atomic layer deposited (ALD) “leaky” TiO 2 have gained interest as charge-selective protection layers for semiconductor solar fuel electrodes. Here we demonstrate the use of sputter-deposited TiO 2 layers as hole selective contacts for WO 3 /CuWO 4 type 2 heterojunction water oxidation photoanodes for the first time. TiO 2 protection layers with varying thicknesses (2 to 128 nm) were deposited using the RF magnetron sputtering technique. The resulting TiO 2 films are amorphous based on Raman spectroscopy and powder XRD. Photoelectrochemical scans and Vibrating Kelvin probe photovoltage spectroscopy show that 2-8 nm TiO 2 layers nearly double the photocurrent to 0.97 mA cm -2 under AM 1.5 illumination (19% AQE at 350 nm), increase the surface photovoltage signal by 25%, and increase the WO 3 /CuWO 4 bandgap. These effects can be attributed to the selectivity of TiO 2 for photoholes. Additionally, SPV data suggest that TiO 2 overlayers suppress copper-based surface recombination defects. Reduced photocurrent and the photovoltage are seen in thicker TiO 2 films (16 to 128 nm) as a result of an increasing hole transfer resistance and because of light shading effects according to photoaction spectra. The TiO 2 films also improve the stability of the WO 3 /CuWO 4 photoelectrodes, allowing nearly constant O 2 evolution over 3 hours after an initial 20-35% loss. Overall, this work establishes RF magnetron sputtering as a useful method to install amorphous TiO 2 passivation layers for improved WO 3 /CuWO 4 solar fuel photoelectrodes. Furthermore, we show how the combination of PEC with SPV measurements provides insight into the function of the TiO 2 coatings.