preparation of hexagonal wo3 from hexagonal ammonium tungsten bronze for sensing nh3

Preparation of hexagonal WO 3 from hexagonal ammonium tungsten bronze for sensing NH 3 Imre Miklo ´ s Szila ´ gyi a, * , Lisheng Wang b , Pelagia-Irene Gouma b , Csaba Bala ´ zsi c ,Ja ´ nos Madara ´ sz d , Gyo ¨ rgy Pokol d a Materials Structure and Modeling Research Group of the Hungarian Academy of Sciences, Budapest University of Technology and Economics, H-1111 Budapest, Szt. Gelle ´ rt te ´ r4, Hungary b Department of Materials Science and Engineering, 314 Old Engineering Building, SUNY, Stony Brook, NY 11794-2275, USA c Ceramics and Nanocomposites Laboratory, Research Institute for Technical Physics and Materials Science, H-1121 Budapest, Konkoly-Thege u ´ t 29-33, Hungary d Department of Inorganic and Analytical Chemistry, Budapest University of Technology and Economics, H-1111 Budapest, Szt. Gelle ´ rt te ´ r 4, Hungary 1. Introduction As sensors to various gases (NH 3 ,NO 2 ,H 2 S, etc.) [1–3], chromogenic (electro-, photo- and thermochromic) materials [4–6] and catalysts in several acid-catalysed [7] or photocatalytic [8] reactions, tungsten oxides are attracting continuous attention. Among a series of polymorphs of tungsten oxides, the hexagonal phase, h-WO 3 has drawn special interest due to its open-tunnel structure and intercalation chemistry, which is quite different from ReO 3 -like stable phases. The h-WO 3 is usually prepared by acidification and hydrothermal treatment (with various promoting reactants) of alkali tungstates [9–13]. However, since a hydrothermal step is involved, the small dimension of autoclaves used for research purposes limits the yield of h-WO 3 powders. In addition, these methods are time consuming because the hydrothermal reaction can take hours or days, and very often calcination is needed to obtain crystalline products. Besides wet chemical methods, thermal annealing of ammo- nium polytungstates [14,15] or hexagonal ammonium tungsten bronzes [16,17] is also a viable way to prepare h-WO 3 .Thislatter route has the advantage that it requires less time and larger batches of h-WO 3 can be produced. However, it must be mentioned that t hermal annealing yields a h-WO 3 structure, whi ch is not comp letely the same as t he one produced by hydrothermal synthesis. This is shown by that the differently produced h-WO 3 samples have different XRD reference cards: ICDD 33-1387 and 75-2187 for h- WO 3 prepared hydrothermally and ICDD 85-2460 for h-WO 3 prepared by thermal annealing. Neverthel ess, a comparison of the published atomic coordinates [10,14] of these differently prepared h-WO 3 samples show that the structures are basically the same (i.e. both are built up by corner sharing octahedra, which form hexagonal and trigonal channels along the c-axis), and the differences between them are minor. Therefore the application characteristics of the h-WO 3 samplespreparedbythesetwowaysshouldnotdifferfromeach other significantly. Up to now, among the several application possibilities of h-WO 3 prepared by thermal annealing, only the ion intercalation was studied [14,16]. However, as gas sensors they were not tested and it was still unknown whether thermal annealing of ammonium polytungstates and hexagonal ammonium tungsten bronzes could yield nanosize h-WO 3 . Materials Research Bulletin 44 (2009) 505–508 ARTICLE INFO Article history: Received 3 June 2008 Received in revised form 2 July 2008 Accepted 5 August 2008 Available online 12 August 2008 Keywords: A. Oxides Semiconductors C. X-ray diffraction Electron microscopy D. Electrical properties ABSTRACT Hexagonal tungsten oxide (h-WO 3 ) was prepared by annealing hexagonal ammonium tungsten bronze, (NH 4 ) 0.07 (NH 3 ) 0.04 (H 2 O) 0.09 WO 2.95 . The structure, composition and morphology of h-WO 3 were studied by XRD, XPS, Raman, 1 H MAS (magic angle spinning) NMR, scanning electron microscopy (SEM), and BET- N 2 specific surface area measuremen t, while its therm al stability was investigated by in situ XRD. The h- WO 3 sample was built up by 50–100 nm particles, had an average specific surface area of 8.3 m 2 /g and was thermally stable up to 450 8C. Gas sensing tests showed that h-WO 3 was sensitive to various levels (10–50 ppm) of NH 3 , with the shortest response and recovery times (1.3 and 3.8 min, respectively) to 50 ppm NH 3 . To this NH 3 concentration, the sensor had significantly higher sensitivity than h-WO 3 samples prepared by wet chemical methods. ß 2008 Elsevier Ltd. All rights reserved. * Corresponding author. Tel.: +36 1 463 4047; fax: +36 1 463 3408. E-mail address: imre.szilagyi@mail.bme.hu (I.M. Szila ´ gyi). Contents lists available at ScienceDirect Materials Research Bulletin journal homepage: www.elsevier.com/locate/matresbu 0025-5408/$ – see front matter ß 2008 Elsevier Ltd. All rights reserved. doi:10.1016/j.materresbull.2008.08.003 Recently we managed to prepare hexagonal ammonium tungsten bronze (HATB), (NH 4 ) 0.07 (NH 3 ) 0.04 (H 2 O) 0.09 WO 2.95 by heating ammonium paratungstate tetrahydrate (APT), (NH 4 ) 10 [H 2 W 12 O 42 ]Á4H 2 OinH 2 for 6 h at 400 8C [18]. This has allowed us to synthesize h-WO 3 in good quality from this HATB sample and study its gas sensitivity. In this paper, h-WO 3 particles were successfully prepared in large batch and short time by heating the HATB precursor. The structure, composition and morphology of the product were studied by powder XRD, XPS, Raman, 1 H MAS (magic angle spinning) NMR and scanning electron microscopy (SEM), while its thermal stability was investigated by in situ high temperature powder XRD. Gas sensing layer was prepared from as-produced h- WO 3 , and its sensitivity was tested to NH 3 . 2. Experimental Sample h-WO 3 was prepared by heating HATB, (NH 4 ) 0.07 (NH 3 ) 0.04 (H 2 O) 0.09 WO 2.95 in air (15 l h À1 )at108C min À1 to 470 8C and then keeping it there isothermally for 3 min in an open aluminium crucible in a Du Pont 910 DSC instrument. To check the reproducibility of this preparation route, several batches of h-WO 3 were prepared, and it was found that the characteristics of different h-WO 3 batches did not differ from each other. Since it was enough for research purposes, usually 1 g of powder was produced in a batch, but the batch size can be increased easily. Therefore it was demonstrated that – compared to the common wet chemical methods – this preparation route of h-WO 3 required less time (1 h or even less), was reproducible, and could yield large batches of h-WO 3 . Powder X-ray diffraction (XRD) pattern of h-WO 3 was measured by a PANalytical X’pert Pro MPD X-ray diffractometer equipped with an X’Celerator detector using Cu K a radiation. In situ high temperature XRD patterns of h-WO 3 in static air were collected by the same X-ray diffractometer in an Anton Paar HTK- 2000 high temperature XRD chamber using Cu K a radiation. The scanning time was ca. 3 min for each pattern and the heating rate was 10 8C min À1 between XRD measurements. X-ray Photoelectron Spectroscopy (XPS) spectra were recorded by a VG Microtech instrument consisting of a XR3E2 X-ray source, a twin anode (Mg K a and Al K a ) and a CLAM 2 hemispherical analyser using Mg K a radiation. Detailed scans were recorded with 50 eV pass energy at (0.05 eV/1.5 s). The spectrometer was calibrated with the binding energy of the C1s line (284.5 eV). Raman spectra were collected by a Jobin Yvon Labram instrument attached to an Olympus BX41 microscope. Frequency doubled Nd-YAG laser (532 nm) was applied as exiting source with 1 mW applied power. The sample was located and examined with a 50Â objective, thus individual crystals could be examined (laser spot size was about 1.2 m m). The backscattered light collected by the objective was dispersed on an 1800 g/mm grating and detected by a 1024 Â 256 CCD detector. 1 H MAS NMR experiments were carried out on a VARIAN NMR SYSTEM spectrometer (600 MHz for 1 H) using a 3.2 mm HXY VARIAN/Chemagnetics probe. 1 H chemical shifts were referenced to adamantane ( d 1H = 0 ppm). Spectra were recorded under the same experimental conditions. 16 transients were acquired at 12 kHz spinning rate and a recycle delay of 20 s was used. Background suppression DEPTH [19] was employed to remove signals from the probe. Scanning electron microscopy (SEM) characterization was performed by a LEO-1550 FEG SEM instrument. BET specific surface area measurement was carried on by nitrogen adsorption at 77 K (Micromeritics Gemini 2375) after degassing the sample, at least, for 1 h at 150 8C in nitrogen. For gas sensing test, as-synthesized h-WO 3 particles were well grinded into powders. The gas sensing layer was produced by spin coating 10 mg powder/5 ml n -butanol suspension of h-WO 3 on Al 2 O 3 substrates with Au-metallization. Sensing tests were carried out in the gas flow bench set-up at SUNY, Stony Brook. The gases used in the sensing setup were UHP nitrogen (Praxair), UHP oxygen (Praxair), 1000 ppm ammonia in nitrogen (BOC gases). Concentra- tion of ammonia was varied by varying its flow rate in conjunction with nitrogen/oxygen flow rates. 3. Results and discussion Based on the XRD pattern (Fig. 1), the h-WO 3 sample was identified as pure h-WO 3 (ICDD 85-2460) with a well ordered crystalline structure. Its cell parameters (a = 0.7324 nm and c = 0.7638 nm) were almost the same as the ones published by Oi et al. [14]. The Raman bands [20–22] were also typical to h-WO 3 (Fig. 2). The main bands at 783, 692, 648 cm À1 were characteristic O–W–O stretching vibrations. The bands at 325, 300 and 264 cm À1 could be assigned to O–W–O deformation vibrations. The band at 456 cm À1 was related to a small amount of reduced W atoms. The peak at 184 cm À1 was a lattice mode of h-WO 3 . In contrast with the h-WO 3 sample, the precursor HATB contained a significant amount of reduced W atoms (see XPS results below). As a consequence the absorption bands were very broad in the Raman spectrum of HATB. Fig. 1. XRD pattern of h-WO 3 . Fig. 2. Raman spectra of (a) HATB; (b) h-WO 3 . I.M. Szila ´ gyi et al. / Materials Research Bulletin 44 (2009) 505–508 506 The oxidation state of tungsten atoms was investigated by XPS. Since HATB was partly reduced, W 4+ (5.4%) and W 5+ (13.8%) atoms were also observed besides W 6+ (80.9%) atoms [18]. When HATB was heated in air at 470 8C, the product h-WO 3 showed an almost fully oxidized structure (96.8% W 6+ , 1.8% W 5+ , 1.4% W 4+ ). This was also supported by the yellow color of h-WO 3 , while the partly reduced HATB was dark blue. We measured the amount of NH 4 + ions and NH 3 molecules, which remained in the solid structure, by solid-state 1 H MAS NMR spectroscopy [18]. After curve fitting the 1 H MAS NMR spectra, the peaks at 4.5 and 5.6 ppm were assigned to NH 4 + ions and NH 3 molecules respectively. The 1 H MAS NMR results showed that the amount of NH 4 + ions and NH 3 molecules decreased significantly in h-WO 3 compared to HATB, but they were still present. Recently we determined the amounts of NH 4 + and NH 3 in h-WO 3 , which were ca. 0.11 and 0.04 wt.%, respectively [17]. The morphology of h-WO 3 was investigated by SEM. The precursor of h-WO 3 , i.e. HATB was built up by aggregated 50– 100 nm particles (Fig. 3a). The annealing of HATB did not affect the morphology significantly. Therefore the h-WO 3 sample was also built up by 50-100 nm particles, which were aggregated into m m scale blocks (Fig. 3b and c). BET measurement showed that the average specific surface area (SSA) of the particles was about 8.3 m 2 /g and the BET equivalent average diameter (d BET ) was 100 nm, which is consistent with above SEM results. Here, d BET is calculated as d BET = 6/(SSA Â r p ), where r p is the weighted density of h-WO 3 (7.16 g/cm 3 ). For gas sensing tests it was advisable to study the thermal stability of h-WO 3 . Based on in situ high temperature XRD patterns (Fig. 4), the starting h-WO 3 structure remained nearly the same up to 450 8C. Then between 500–550 8C the hexagonal structure transformed irreversibly into monoclinic (m-) WO 3 (ICDD 43- 1035), which later around 750 8C transformed reversibly into tetragonal (t-) WO 3 (ICDD 85-0807). Thus, in situ XRD study showed that h-WO 3 was stable up to 450 8C [17], which made it safe to test h-WO 3 at 300 8C as a gas sensor. The sensing response of the h-WO 3 layer to different concentrations of NH 3 gas is shown in Fig. 5. The measurements were carried out at 300 8C. The film showed a decrease in resistance on exposure to NH 3 , which is characteristic to an n-type semiconductor. If we define the sensitivity as the ratio of baseline resistance to gas-responding resistance, its value was 2 when the NH 3 concentration was 10 ppm. When we increased NH 3 concentration to 20 ppm and 50 ppm step by step, the sensitivity increased to 4 and 6, respectively. This means the h-WO 3 sensor is quite sensitive to different concentrations of NH 3 gas at 300 8C; in fact, it is much more sensitive than h-WO 3 prepared by the hydrothermal route, which had a sensitivity of 3 for 50 ppm NH 3 at 300 8C [23]. Besides, the response time was quite fast (3.3, 1.5, 1.3 min for 10, 20 and 50 ppm NH 3 , respectively), especially when the NH 3 concentration went higher. As the NH 3 concentration lowered down afterwards, the sensor resistance increased gradually accordingly. It is clear to see that the sensor had almost the same resistance value at the same NH 3 level as the first half part Fig. 3. SEM images of (a) HATB; (b and c) h-WO 3 . Fig. 4. In situ high temperature XRD patterns of h-WO 3 in static air recorded from r.t. to 900 8C. I.M. Szila ´ gyi et al. / Materials Research Bulletin 44 (2009) 505–508 507 of the test, respectively. This means the sensor performance is reversible and recoverable, which is important for its application. In addition, the recovery time was not long (9.0, 6.0, 3.8 min for 10, 20 and 50 ppm NH 3 , respectively). At the end of the test, the sensor went to its baseline value when we stopped the NH 3 gas flow. 4. Summary and conclusions h-WO 3 was prepared by annealing hexagonal ammonium tungsten bronze, (NH 4 ) 0.07 (NH 3 ) 0.04 (H 2 O) 0.09 WO 2.95 . Compared to the common wet chemical methods, this preparation route required less time, it was reproducible, and it could yield large batches of h- WO 3 . The as-produced h-WO 3 was pure and had a well-ordered crystalline structure. It contained small amounts of reduced tungsten atoms, as well as residual NH 4 + ions and NH 3 molecules. The h-WO 3 sample was built up by aggregated 50–100 nm particles and was thermally stable up to 450 8C. Gas sensing layers were prepared from as-produced h-WO 3 , and the gas sensor test showed that h-WO 3 was sensitive to various levels (10–50 ppm) of NH 3 .Its sensitivity to 50 ppm NH 3 (6) was significantly higher than the sensitivity (3) of h-WO 3 samples prepared by hydrothermal synthesis. The sensor had the fastest response and recovery times (1.3 and 3.8. min, respectively) also for 50 ppm NH 3 . Therefore, it was demonstrated that this preparation route resulted in a h-WO 3 sample whose gas sensing parameters were twice better than those h-WO 3 samples, which were prepared by wet chemical methods. In addition, this route required less time, it was reproducible, and large batches of h-WO 3 could be obtained. Acknowledgments A.L. To ´ th (Research Institute for Technical Physics and Materials Science, H ungarian Academy of Sciences, Budapest, Hungary), A. Szabo ´ (Department of Organic Chemistry and Technology, Budapest University of Technology and Economics, Budapest, Hungary), K. Varga-Josepovits (Department of Atomic Physics, Budapest University of Technology and Economics, Budapest, Hungary) as well as P. Kira ´ ly and G. Ta ´ rka ´ nyi (Institute of Structural Chemistry, Chemical Research Center of the Hungarian Academy of Sciences, Budapest, Hungary) are acknowledged for their help in performing the SEM, Raman, XPS and 1 H MAS NMR measurements, respectively. We are also thankful to Particle Technology Laboratory in ETH Zurich, Switzerland for providing BET surface analysis equipment. A diffractometer purchase grant from the Agency for Research Fund Management (KPI-EU-GVOP-3.2.1 2004-04-0224/3.0 KMA) is gratefully acknowledged. References [1] S. Ashraf, C.S. Blackman, R.G. Palgrave, I.P. Parkin, J. Mater. Chem. 17 (2007) 1063. [2] E.H. Espinosa, R. Ionescu, E. Llobet, A. Felten, C. Bittencourt, E. Sotter, Z. Topalian, P. 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SPIE 6769 (2007) 67690E, doi:10.1117/12.736679. Fig. 5. Sensitivity of h-WO 3 to various levels of NH 3 at 300 8C. I.M. Szila ´ gyi et al. / Materials Research Bulletin 44 (2009) 505–508 508 . Preparation of hexagonal WO 3 from hexagonal ammonium tungsten bronze for sensing NH 3 Imre Miklo ´ s Szila ´ gyi a, * ,. and it was still unknown whether thermal annealing of ammonium polytungstates and hexagonal ammonium tungsten bronzes could yield nanosize h-WO 3 . Materials