Optimization of the Synthesis of Nanostructured Tungsten-MolybdenumBimetallic Oxide

International Scholarly Research Network ISRN Nanomaterials Volume 2012, Article ID 909647, 13 pages doi:10.5402/2012/909647 Research Article Optimization of the Synthesis of Nanostructured Tungsten-Molybdenum Bimetallic Oxide H. Hassan,1 T. Zaki,1 S. Mikhail,1 A. Kandil,2 and A. Farag2 1 Petroleum Refining Division, Department of Catalysis, Egyptian Petroleum Research Institute, Cairo 11727, Egypt of Chemistry, Faculty of Science, Helwan University, Helwan 11421, Egypt 2 Department Correspondence should be addressed to H. Hassan, hebachem@yahoo.com Received 16 May 2012; Accepted 10 June 2012 Academic Editors: R. Azimirad, C. Li, and F. Miao Copyright © 2012 H. Hassan 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. Mo0.5 W0.5 O3 nanoparticles were prepared through the Pechini process and were characterized using X-ray diffraction (XRD), transmission electron microscopy (TEM), FT-IR spectrometer, and differential thermal analysis (TG-DSC) analyses. The polyesterification reaction, as the starting step, has a profound influence on the dispersion of the resulting nanoparticles. The molar ratios CA : TM = 2 and EG : CA = 1.5 are favorable for the preparation of Mo0.5 W0.5 O3 nanoparticles having average particles size ranging from 2 to 9 nm. Meanwhile, the molar ratios CA : TM = 4 and EG : CA = 0.19 are favorable for the preparation of Mo0.5 W0.5 O3 nanoparticles having an average particles size ranging from 11 to 29 nm. For the calcination step, increased calcination time (eight hours) at 500◦ C is advantageous for allowing the monometallic phases enough time to transform into the desired bimetallic Mo0.5 W0.5 O3 phase. 1. Introduction Molybdenum trioxide (MoO3 ) and tungsten trioxide (WO3 ) are well-known metal oxides with similar physical and chemical properties. They show n-type semiconducting properties related to the presence of lattice defects, mainly oxygen defects [1, 2], and they have been extensively studied for their potential applicability in gas sensing devices [3, 4] and catalysis [5, 6]. Additionally, due to the unique activity of trioxides of W and Mo in nonstoichiometric forms, they have been extensively studied as electrochemical materials [7]. The Mox Wl−x O3 system exhibits “displacive” or “reconstructive” phase transitions induced by hydrogen intercalation and temperature, respectively, leading to rearrangement in the local electronic and atomic structures [8]. Polycrystalline Mox Wl−x O3 (x = 0.1, 0.2, 0.3, 0.5, 0.7, and 0.9) solid solutions were obtained by high-temperature synthesis [9]. With the progress in nanotechnology, nanoparticles have attracted increasing attention to their unique properties [10]. One of the recently investigated methods for the simple preparation of nano-oxide composites that include molybdenum or tungsten atoms is the Pechini method [11, 12]. However, research into the catalytic activity of molybdenum-tungsten bimetallic oxides is rare despite their promising gas sensing potential [13, 14]. In this work, the synthesis of molybdenum-tungsten oxide nanoparticles is presented. The procedure includes the formation of composites containing both molybdenum or tungsten atoms in a 1 : 1 ratio using the polymeric method. The influence of citric acid and ethylene glycol concentrations, as well as total metal molar ratios, on the properties of the final products was studied. In addition, the effect of the sequence of the synthetic steps (i.e., polymerization and chelation) was explored. Furthermore, the impacts of the temperature and time of calcination were examined. 2. Experimental For most of the prepared samples, aqueous ethylene glycol (EG) solutions of different concentrations were added to an aqueous solution of citric acid (CA) for polymerization under constant stirring and at 60◦ C for 1 h. Second, the polyester was heated to 80◦ C with stirring, and then 500 mL of a TM solution (1 : 1 Mo : W metal ratio of ammonium 2 heptamolybdate and ammonium metatungstate precursors) was added and stirred for an additional hour. Accordingly, molybdic and tungstic acids were created, and the pH of the medium decreased to 1.4. In the third step, the solutions were slowly heated to 140◦ C until the water was completely removed (∼2.5 hours). The gels obtained were dried at 150◦ C overnight in an electrical furnace to yield solid resins. The resulting resins were ground in an agate mortar and subjected to a pyrolysis process at 450◦ C for 4 h in glazed alumina crucibles. Finally, the pyrolyzed product was subjected to calcination at 500◦ C for 4 h in the presence of purified air. The MoWO3 samples were named MWRC RE (RC is CA : TM, and RE is EG : CA) corresponding to the ratios used. To understand the influence of the sequence of the preparation steps, MW2–1.5 was also prepared in the reverse fashion (i.e., the TM solution was added to the CA solution at 60◦ C first, and then, the EG solution was added at 80◦ C). This sample was named RMW2–1.5. To study the role of the calcination step on the final characteristics of the produced bimetallic oxides, two factors were investigated. The first factor was the calcination temperature, and the second was the calcination duration. The molybdenum-tungsten samples selected for thermal treatment temperature evaluation were named MWRC RE (T) (RC is CA : TM, RE is EG : CA and T is calcination temperature) corresponding to the preparation and treatment conditions used. At relatively high calcination temperatures, that is, 750, 850, and 950◦ C, a physically separated needled sample was collected in addition to the ordinary final powder product, and the separated samples were coded MWRC -RE (S750), MWRC -RE (S850), and MWRC -RE (S950), respectively. The bimetallic oxide samples subjected to different calcination times were labeled MWRC -RE (8) and MWRC RE (12), which referred to calcination for eight and twelve hours, respectively. The sample calcined for four hours was named MWRC -RE . The evolution of the samples was followed by X-ray powder diffraction (XRD) on a Bruker AXS D8 Advance equipped with Ni-filtered copper Kα1 radiation (λ = 1.5404 Å) in the range 2θ = 20–80◦ . Transmission electron microscopy images were recorded on a JEOL-1400 TEM at 120 kV. FTIR spectra were recorded using an FT-IR spectrometer, model 960M000 g, ATI Mattson Infinity Series. Differential thermal analysis was recorded on a Labsys TGDSC16 apparatus manufactured by Setaram Instrumentation. The sample was ground to 20 mesh, and α-alumina was used as an inert reference material. The experiments were carried out at a heating rate of 10◦ C/min in an argon atmosphere. 3. Results and Discussion 3.1. The Role of Reactant Molar Ratios 3.1.1. Influence of EG Molar Ratio. Figure 1 presents the XRD patterns of MoW oxides samples with increasing EG ISRN Nanomaterials molar fractions and a constant CA : TM molar ratio. The XRD patterns show one main phase, which is Mo0.5 W0.5 O3 (JCPD: 28–0667), and two secondary phases, monoclinic MoO3 (JCPD: 80–0347) and cubic WO3 (JCPD: 41–0905), in all the samples tested. TEM images (Figures 2(a) and 2(b)) reveal that the average particle size increased (from 3–10 nm to 10–16 nm) as the EG molar fraction increased (from MW1–3 to MW1–6). With increasing EG molar fractions, the average particle size continued to increase up to 18 nm (Figure 2(c), MW1– 12), and aggregates started to appear. Both particle enlargement and aggregation became more obvious in the MW1–24 sample (Figure 2(d)), which was prepared using the highest molar fraction of EG. 3.1.2. Influence of CA Molar Ratio. According to previous experimental data, the MW1–3 sample has bimetallic nanoparticles that were prepared using the optimum EG molar ratio, so this sample was selected. Thus, the EG molar ratios versus TM and CA of 1 and 3, respectively, were selected as the initial values for studying the influence of the CA molar ratio on the properties of the produced bimetallic nanoparticles. Figure 3 presents the XRD patterns of MoW oxide samples prepared using different CA molar ratios versus both TM and EG. According to Figure 3(b), Mo0.5 W0.5 O3 was the only phase in MW2–1.5. However, the other samples (MW1– 3, MW4–0.75, MW8–0.38, and MW16–0.19) contained secondary phases of MoO3 and WO3 in addition to the major phase (Mo0.5 W0.5 O3 ). The XRD patterns did not reveal any change in the intensities of the Mo0.5 W0.5 O3 reflections with an increasing CA molar ratio. TEM images (Figures 4(a) and 4(b)) indicated that the average particle size increased from 3–10 nm to 4–16 nm as the CA molar ratio increased (from MW1–3 to MW2– 1.5). However, when the CA molar ratio increased four and eight times, as in the case of MW8–0.38 and MW16– 0.19, respectively, the average particle size increased from 4–16 nm (Figure 4(b)) to 11–19 nm (Figure 4(c)) and 20– 36 nm (Figure 4(d)). Despite the slightly increased size of the MW2–1.5 nanoparticles in comparison to the MW1–3 nanoparticles (Figures 4(a) and 4(b)), the presence of the Mo0.5 W0.5 O3 phase as a mono-phase gave this sample unique properties. 3.1.3. Influence of the Sequence of Preparation Steps. Figure 5 presents XRD patterns of both MW2–1.5 and RMW2–1.5 samples. This figure shows that starting with the chelation reaction (i.e., the reaction between TM and CA) did not alter the nature of the final phase when Mo0.5 W0.5 O3 was the only phase (e.g., MW2–1.5). However, the crystallinity of the produced phase decreased with a change to the sequence of preparation steps. The TEM images of both samples (Figure 6) did not reveal the average particle size shift due to the rearranged order of the preparation steps. However, in RMW2–1.5, the prepared Mo0.5 W0.5 O3 appeared as aggregations, while the ISRN Nanomaterials 3 120 120 (MW1–3) (MW1–6) 100 Relative intensity Relative intensity 100 80 60 40 20 80 60 40 20 0 0 20 30 40 50 2θ 60 70 80 20 30 40 (a) 60 70 80 60 70 80 (b) 120 120 (MW1–12) (MW1–24) 100 Relative intensity 100 Relative intensity 50 2θ 80 60 40 20 80 60 40 20 0 0 20 30 40 50 2θ 60 70 80 20 30 40 (c) 50 2θ (d) Figure 1: XRD patterns of (a) MW1–3 (b) MW1–6, (c) MW1–12 and (d) MW1–24. (a) (c) (b) (d) Figure 2: Transmission electron micrographs of nanocrystalline particles of (a) MW1–3, (b) MW1–6, (c) MW1–12, and (d) MW1–24. 4 ISRN Nanomaterials 120 120 (MW1–3) (MW2–1.5) 100 Relative intensity Relative intensity 100 80 60 40 80 60 40 20 20 0 0 20 30 40 50 60 70 80 20 30 40 50 2θ 2θ (a) 70 80 60 70 80 (b) 120 120 (MW4–0.75) (MW8–0.38) 100 Relative intensity 100 Relative intensity 60 80 60 40 80 60 40 20 20 0 0 20 30 40 50 60 70 80 20 30 40 50 2θ 2θ (c) (d) 120 (MW16–0.19) Relative intensity 100 80 60 40 20 0 20 30 40 50 2θ 60 70 80 (e) Figure 3: XRD patterns of (a) MW1–3, (b) MW2–1.5, (c) MW4–0.75, (d) MW8–0.38, and (e) MW16–0.19. MW2–1.5 sample showed the Mo0.5 W0.5 O3 as well dispersed nanoparticles. 3.1.4. Influence of TM Molar Ratio. To investigate the influence of the TM molar ratio on the properties of the produced nanoparticles, a reactant mixture with excess citric acid was chosen because the CA plays the main role in the chelation step. Accordingly, CA molar ratios versus TM and EG of 16 and 0.19, respectively (MW16–0.19), were selected for studying the influence of the TM molar fraction on the properties of the produced bimetallic nanoparticles. Figure 7 presents the XRD patterns of MoW oxide samples prepared using regular increments of TM molar ratios against CA and EG. In Figure 7(b), the XRD pattern of MW8–0.19 indicated duplication of the intensities of the reflections related to the Mo0.5 W0.5 O3 phase. The same reflections were seen in the pattern of MW16–0.19 (Figure 7(a)), but the WO3 and MoO3 phases were still present in the prepared sample. ISRN Nanomaterials 5 (a) (b) (c) (d) Figure 4: Transmission electron micrographs of nanocrystalline particles of (a) MW1–3, (b) MW2–1.5, (c) MW8–0.38, and (d) MW16– 0.19. 120 120 (MW2–1.5) (RMW2–1.5) 100 Relative intensity Relative intensity 100 80 60 40 80 60 40 20 20 0 0 20 30 40 50 60 70 80 20 30 40 50 2θ 60 70 2θ (a) (b) Figure 5: XRD patterns of (a) MW2–1.5 and (b) RMW2–1.5. (a) (b) Figure 6: Transmission electron micrographs of nanocrystalline particles of (a) MW2–1.5 and (b) RMW2–1.5. 80 6 ISRN Nanomaterials 120 120 (MW16–0.19) (MW8–0.19) 100 Relative intensity Relative intensity 100 80 60 40 80 60 40 20 20 0 0 20 30 40 50 60 70 80 20 30 40 50 2θ (a) 80 60 70 80 120 (MW4–0.19) (MW2–0.19) 100 Relative intensity 100 Relative intensity 70 (b) 120 80 60 40 80 60 40 20 20 0 60 2θ 0 20 30 40 50 60 70 80 20 30 40 50 2θ 2θ (c) (d) Figure 7: XRD patterns of (a) MW16–0.19, (b) MW8–0.19, (c) MW4–0.19, and (d) MW2–0.19. (a) (c) (b) (d) Figure 8: Transmission electron micrographs of nanocrystalline particles of (a) MW16–0.19, (b) MW8–0.19, (c) MW4–0.19, and (d) MW2– 0.19. ISRN Nanomaterials On the other hand, the Mo0.5 W0.5 O3 phase became the unique phase with further increases in the molar ratio of TM, whereas the XRD pattern of MW4–0.19 (Figure 7(c)) indicated the absence of WO3 and MoO3 reflections. Furthermore, the reflections related to the Mo0.5 W0.5 O3 phase increased in comparison with the XRD pattern of MW8–0.19 (Figure 7(b)). Further increasing the TM molar ratio versus CA and EG (i.e., the CA molar ratios versus TM and EG became 2 and 0.19, resp., (MW2–0.19)), the secondary phases WO3 and MoO3 returned to the final product along with Mo0.5 W0.5 O3 (Figure 7(d)). Consequently, the reflection intensity of the main phase decreased in comparison with the MW4–0.19 sample (Figure 7(c)). TEM images (Figures 8(a) and 8(b)) of the same samples demonstrated that the average particle size decreased from 20–36 nm to 15–32 nm as the TM molar ratio increased. Upon further increases in the TM molar ratio (MW4–0.19), the average particle size gradually decreased to 11–29 nm (Figure 8(c)). In the highest TM molar ratio sample (MW2–0.19), the average particle size was drastically smaller than that of the other samples. The TEM images of the samples illustrated nanoparticles with average sizes in the range of 4–7 nm (Figure 8(d)). In addition, nonmeasurable ultra-fine nanoparticles with diameters smaller than 2 nm appeared as dark gray patches distributed around the larger nanoparticles, which appeared as black spots. 3.2. The Role of the Thermal Treatment. The products of the polymerization-chelation reactions were subjected to two different types of thermal treatment. The first thermal treatment was pyrolysis in a nitrogen atmosphere at 450◦ C for four hours. The second treatment was calcination, which varied by temperature and time. At relatively high calcination temperatures (i.e., 750, 850, and 950◦ C), physically separated needle samples were collected in addition to the ordinary powdered final products, and the new separated samples were named MW1–3(S750), MW1–3(S850), and MW1– 3(S950), respectively. 3.2.1. Influence of Calcination Temperature. The X-ray diffraction patterns of nanoparticles produced at different thermal treatment temperatures (Figure 9) showed that for the lowest calcination temperature (450◦ C, MW1–3(450), Figure 9(a)) and the sample calcined at 600◦ C (Figure 9(c)), the intensity of the strongest reflection (monoclinic MoO3 (JCPD: 80–0347) and cubic WO3 (JCPD: 41–0905) at a distance of 3.71 Å) increased. Meanwhile, the intensity of the strongest reflection (Mo0.5 W0.5 O3 , JCPD: 28–0667 at a distance of 3.783 Å) decreased with respect to the XRD pattern of the MW1–3 sample, which was calcined at 500◦ C (Figure 9(b)). Nevertheless, the previously mentioned phases were the only phases created on the final product. As the calcination temperature increased to 750◦ C (Figure 9(d)), a thermal deformation of the bimetallic nanoparticles occurred where the expected phase Mo0.5 W0.5 O3 disappeared 7 and was replaced by two deformed phases: W0.47 Mo0.53 O3 (JCPD: 32–1392) and W0.4 Mo0.6 O3 (JCPD: 76–1280). The monometallic nanoparticles, which were monoclinic MoO3 (JCPD: 80–0347) and cubic WO3 (JCPD: 41–0905), remained in the final powdered sample. However, a new, physically needled phase was easily separated manually from the product after cooling. This needled sample, named MW1–3(S750), was subjected to X-ray diffraction analysis in the range 2θ = 4–80◦ , which indicated that this phase consisted mainly of monoclinic MoO3 (JCPD: 47–1320), and orthorhombic MoO3 (JCPD: 05–0508) (Figure 10(a)). Upon increasing the calcination temperature to 850◦ C (Figure 9(e)), the deformed bimetallic phases in MW1– 3(750) were replaced with a new phase (W0.71 Mo0.29 O3 , JCPD: 76–1279) for the sample MW1–3(850), in which tungsten is the major component. In addition to the bimetallic oxide, the monometallic oxides monoclinic MoO3 (JCPD: 80–0347) and WO3 (JCPD: 01–0486) were still present in the final powdered product (Figure 9(e)). The crystallinity of the molybdenum oxides present in the physically separated needled sample (MW1–3(S850), Figure 10(b)), monoclinic MoO3 (JCPD: 47–1320), and orthorhombic MoO3 (JCPD: 05–0508), increased sharply, as indicated from the strong enhancement in reflection intensities with respect to MW1–3(S750) (Figure 10(a)). The decrease in the intensity of the noisy hump that occurred in the range of 2θ = 4–20◦ also indicated the increased crystallinity. Finally, at the highest calcination temperature (950◦ C), complete separation between the two metals in the oxide occurred, whereas the XRD pattern of the powdered sample, MW1–3(950), indicated that the sample contained only a triclinic WO3 (JCPD: 32–1395) phase (Figure 9(e)). Meanwhile, the XRD pattern of the needled sample, MW1– 3(S950), indicated that this sample consisted of monoclinic MoO3 (JCPD: 47–1320), and orthorhombic MoO3 (JCPD: 05–0508) phases accompanied with strongly increased crystallinity of the molybdenum oxides (Figure 10(c)). The elucidation of powdered sample XRD patterns was facilitated by using the FT-IR spectra of MW1–3 and MW1–3(950) in Figure 11. The FT-IR spectrum of MW1– 3 identified a broad band located in the range of 475– 1050 cm−1 , which had distinguishable apexes at 633, 767, 845, and 975 cm−1 (Figure 11(a)). The band located at 975 cm−1 was assigned to (W=O) and (Mo=O) terminal groups [15, 16], while the bands at 633 and 845 cm−1 were attributed to the asymmetric and symmetric stretches of W– O–W bridges, respectively [15, 17, 18]. According to the literature, vibration of the Mo–O–Mo bond should result in a band with an apex wavenumber of 882 cm−1 [16]. There was no clear band at this spot, but we could identify a broadband covering surrounding wavenumbers. The band at 767 cm−1 was assigned to Mo–O–W stretching. This assumption was possible due to its absence in the spectrum of MW1–3(950), while the broadband that covered the range of 475–1050 cm−1 was split into two apexes at 633 and 845 cm−1 (Figure 11(b)). The FT-IR spectrum of MW1–3(950) nanoparticles illustrated a narrowing in this 8 ISRN Nanomaterials 120 120 (MW1–3(450)) (MW1–3) 100 Relative intensity Relative intensity 100 80 60 40 80 60 40 20 20 0 0 20 30 40 50 2θ 60 70 20 80 30 40 120 140 (MW1–3(650)) 80 60 40 20 70 80 60 70 80 60 70 80 (MW1–3(750)) 120 100 80 60 40 20 0 0 20 30 40 50 2θ 60 70 20 80 30 40 50 2θ (c) (d) 250 300 (MW1–3(850)) (MW1–3(950)) 250 Relative intensity 200 Relative intensity 60 (b) 160 Relative intensity Relative intensity (a) 140 100 50 2θ 150 100 50 200 150 100 50 0 0 20 30 40 50 2θ 60 70 80 (e) 20 30 40 50 2θ (f) Figure 9: XRD patterns of (a) MW1–3(450), (b) MW1–3, (c) MW1–3(650), (d) MW1–3(750), (e) MW1–3(850), and (f) MW1–3(950). peak due to the absence of bands related to the vibration of the Mo–O–Mo bond at 882 cm−1 . Moreover, a new shoulder appeared at 1040 cm−1 and was attributed to the stretching of W–O bonds at the surface [18]. The band at 1620 cm−1 was assigned to the H–O–H bending vibrations of water, which is easily introduced into the system during the IR measurements [18]. The FT-IR spectrum of the needled sample, MW1– 3(S950), indicated that it contained orthorhombic MoO3 , which has two significant bands at 975 cm−1 for a terminal Mo=O stretching vibration and 840 cm−1 for the vibration of the Mo–O–Mo species [17]. Bands at 492 and 533 cm−1 were most likely due to asymmetric and symmetric stretches of the monoclinic MoO3 phase (Figure 12). As previously mentioned, the bands at 1625 and 3430 cm−1 were assigned to the H–O–H bending and stretching vibrations of the hydration water [19]. It is known that molybdenum oxide (MoO3 ) melts and sublimes at approximately 800◦ C [20, 21]. However, according to the XRD patterns and the FT-IR spectra in the ISRN Nanomaterials 9 120 120 (MW1–3(S750)) (MW1–3(S850)) 100 Relative intensity Relative intensity 100 80 60 40 80 60 40 20 20 0 0 20 30 40 50 60 70 80 20 30 40 50 2θ 2θ (a) 60 70 80 (b) 120 (MW1–3(S950)) Relative intensity 100 80 60 40 20 0 20 30 40 50 60 70 80 2θ (c) Figure 10: XRD patterns of (a) MW1–3(S750), (b) MW1–3(S850), and (c) MW1–3(S950). presented case study, the decomposition of the bimetallic nanoparticles and, consequently, the sublimation process started early (i.e., at approximately 700◦ C). Such an assumption was confirmed via the thermal analysis of MW1– 3, where the thermal profile of the MoW nanoparticles (Figure 13) showed a strong decline in the DSC curve towards the endothermic direction at temperatures higher than 650◦ C. No significant endothermic peak was identified until 880◦ C, and then another endothermic peak appeared at 933◦ C. The thermal behavior of the MW1–3 sample may be explained as follows. Between 700 and 800◦ C, the decomposition and deformation of the Mo0.5 W0.5 O3 phase occurred, as did sublimation of the free MoO3 particles. The sublimation of the free MoO3 at such a relatively low temperature with respect to the normal thermal behavior of the molybdenum oxide bulk phase [20, 21] might be due to its size. On a nano-scale, the particles become more sensitive to thermal changes and, consequently, make the thermal transformation process easier than that for bulky particles. At temperatures from 800 to 900◦ C, the W0.47 Mo0.53 O3 and W0.4 Mo0.6 O3 phases deformed into W0.71 Mo0.29 O3 . This deformation was accompanied by sublimation of the produced free MoO3 phase. At 933◦ C, the final form of the MoW nanoparticles, W0.71 Mo0.29 O3 , lost its molybdenum component and transformed into triclinic WO3 . The TEM images of the MW1–3 and MW1–3(650) samples, which are similar in their phase compositions (Figures 14(a) and 4(b)), illustrated that the average particle sizes increased from 3–10 nm to 6–16 nm as the calcination temperature increased from 500 to 650◦ C. Despite a change in the type of phases created after thermal treatment at high calcination temperatures (i.e., 750 and 850◦ C), the general feature of these powdered samples was a low average particle size (6–11 nm for MW1–3(750) and 3–10 nm for MW1– 3(850); Figures 14(c) and 14(d), resp.). The TEM images of the nanoparticles of the triclinic tungsten oxide sample MW1–3(950) large agglomerates with average particle sizes from 46 to 115 nm (Figure 14(e)). By focusing on these agglomerates, the TEM image showed nanoparticles with average particle sizes from 1 to 12 nm, which appeared as black spots, in addition to nonmeasurable ultra-fine nanoparticles with diameters smaller than 1 nm (dark gray patches distributed around the larger nanoparticles, Figure 14(f)). 3.2.2. Influence of Calcination Time. As mentioned above, the optimal temperature for the calcination process was 10 ISRN Nanomaterials 140 4 Exo 2 Heat flow (µV) 120 Transmittance (%) 100 80 2943 60 1204 1382 1450 1620 0 −2 −4 870.8◦ C◦ 880.5 C −6 −8 933.4◦ C −10 0 40 100 200 633 400 500 600 700 800 900 1000 Temperature (◦ C) 20 Series1 845 0 5000 4000 3000 2000 767 1000 Figure 13: Thermal analysis (DSC) of MW1–3. 0 Wavenumber (cm−1 ) b a Figure 11: FTIR spectra of (a) MW1–3 and (b) MW1–3(950). 140 120 100 Transmittance (%) 300 1055 1375 1625 974 80 60 40 796 840 20 0 5000 533 492 4000 3000 Wavenumber 2000 1000 0 (cm−1 ) Series1 Figure 12: FTIR spectrum of MW1–3(S950). 500◦ C. However, there is another factor that may play an important role in the thermal treatment of bimetallic nanoparticles: the duration of the calcination process. To understand the importance of this factor, the influence of three different calcination times, four, eight, and twelve hours, on the characteristics of the final product were investigated. The bimetallic oxide samples that underwent the different calcination times are labeled MW1–3(8) and MW1–3(12), referring to calcination for eight and twelve hours, respectively. In addition, the MW1–3 sample was tested, which was calcined for four hours at 500◦ C. The X-ray diffraction patterns of the nanoparticles produced after different thermal treatment times (Figure 15) showed that increased calcination time did not significantly change the crystallinity of the produced nanobimetallic oxides. This assertion was supported by the unchanging intensities of the reflections in the oxides. The reflection that belonged to the monometallic phases monoclinic MoO3 (JCPD: 80–0347) and cubic WO3 (JCPD: 41–0905), which could easily be identified in the XRD pattern of MW1–3 (Figure 15(a)), weakened and became indistinct after eight hours of calcination at 500◦ C (Figure 15(b)). Such reflections disappeared in the X-ray pattern of MW1–3(12), indicating that the produced nanoparticles of molybdenum-tungsten were a pure bimetallic Mo0.5 W0.5 O3 phase (JCPD: 28–0667, Figure 15(c)). The TEM image of the nanoparticles of MW1–3(8) did not show a distinct difference in average particle size (Figure 16(b)) when compared with the TEM image of the nanoparticles of MW1–3 (Figure 16(a)). Both samples had average particle sizes from 3 to 10 nm. This observation eliminated the possibility of sintering during the long calcination time. On the contrary, increased calcination time was advantageous, as it gave the monoclinic MoO3 and cubic WO3 phases enough time to transform into the desired bimetallic Mo0.5 W0.5 O3 phase. Upon initial inspection, the TEM image of the nanoparticles of the bimetallic Mo0.5 W0.5 O3 phase in MW1–3(12) indicated large agglomerates with average particle sizes from 41 to 160 nm (Figure 16(c)). By zooming on these agglomerates, however, the TEM image revealed nanoparticles with average particle sizes from 2 to 9 nm, which appeared as black spots, in addition to nonmeasurable ultrafine nanoparticles with diameters smaller than 2 nm (dark gray patches Figure 16(d)). 4. Conclusions The Pechini method can be successfully applied for the preparation of Mo0.5 W0.5 O3 , and the ratios of the reactants strongly affected the purity of the final products. (i) The molar ratios CA : TM = 2 and EG : CA = 1.5 were the most favorable for the preparation of Mo0.5 W0.5 O3 nanoparticles having average particle ISRN Nanomaterials 11 (a) (b) (c) (d) (e) Figure 14: Transmission electron micrographs of nanocrystalline particles of (a) MW1–3, (b) MW1–3(650), (c) MW1–3(750), (d) MW1– 3(850), (e) MW1–3(950), and (e) MW1–3(950). 120 120 (MW1–3) (MW1–3(4)) Relative intensity 100 80 60 40 80 60 40 20 20 0 0 20 30 40 50 60 70 80 20 30 40 50 2θ 2θ (a) (b) 120 (MW1–3(8)) 100 Relative intensity Relative intensity 100 80 60 40 20 0 20 30 40 50 60 70 80 2θ (c) Figure 15: XRD patterns of (a) MW1–3, (b) MW1–3(4), and (c) MW1–3(8). 60 70 80 12 ISRN Nanomaterials (a) (b) (c) (d) Figure 16: Transmission electron micrographs of nanocrystalline particles of (a) MW1–3, (b) MW1–3(8), (c) MW1–3(12), and (d) MW1– 3(12). sizes from 2 to 9 nm. Meanwhile, the molar ratios CA : TM = 4 and EG : CA = 0.19 were optimal for the preparation of Mo0.5 W0.5 O3 nanoparticles having average particle sizes from 11 to 29 nm. (ii) The sequence of the preparation steps affects nanoparticle dispersion, whereas the polyesterification reaction, as a starting step, also strongly influenced the dispersion of the nanoparticles. (iii) Increased calcination time (eight hours) at a suitable temperature (500◦ C) was advantageous, as it gave the monometallic phases enough time to transform into the desired bimetallic W0.5 Mo0.5 O3 phase. [6] [7] [8] [9] References [1] Y.-C. Nah, A. Ghicov, D. Kim, and P. Schmuki, “Enhanced electrochromic properties of self-organized nanoporous WO3 ,” Electrochemistry Communications, vol. 10, no. 11, pp. 1777–1780, 2008. [2] O. Marin-Flores, T. Turba, J. Breit, M. Norton, and S. 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