Chemical Vapor Synthesis and Physico-chemical Properties of V2O5 Nanoparticles
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Transcript of Chemical Vapor Synthesis and Physico-chemical Properties of V2O5 Nanoparticles
Communication
DOI: 10.1002/cvde.201104307
Chemical Vapor Synthesis and Physico-chemicalProperties of V2O5 Nanoparticles**
By Hoang Anh Le, Sungmin Chin, Eunseuk Park,
Gwinam Bae, and Jongsoo Jurng*
transition metal oxides are of great interest. In particular,
vanadium oxide-based materials, including vanadium pent-
oxide (V O ) and vanadium phosphates, are catalysts for the
In the field of heterogeneous catalysts, nanometer-size
2 5
mild oxidation of hydrocarbons and alcohols.[1] To date,
V2O5 has attracted increasing interest for its potential
applications as catalysts, sensors, and electrodes. V2O5
powders can be obtained by various physical and chemical
methods, such as CVD,[2–4] hydrothermal method,[1,3,5]
spray pyrolysis,[6] sol-gel,[7–9] co-precipitation,[10] and
microwave plasma-torch method,[11] etc. Chemical vapor
synthesis, also known as CVD or chemical vapor condensa-
tion (CVC),[12–14] is an alternative method for the direct
synthesis of nanoparticles. The principle advantages of the
reactions in the gas phase are, very short process times, and
nanometer-scale powders of high purity with a narrow
particle size distribution. The particle morphology, crystal-
line phase, and surface chemistry of thermally decomposed
particles can be controlled by regulating the precursor
composition, reaction temperature, pressure, solvent prop-
erty, and aging time.[15,16] In a typical CVC process, the
precursor solution is atomized into an aerosol reactor
(electric furnace) where droplets undergo solvent evapora-
tion and solute precipitation within the droplets, which are
then dried. In a typical thermal decomposition process, the
precursor solution was atomized into an aerosol reactor,
where droplets underwent solvent evaporation and solute
precipitation within the droplets, which were then dried,
followed by thermolysis of the precipitates at higher
temperatures, and finally sintering to form the final
particles.[15]
In the CVC process, the synthesis temperature is one of
the most important factors for determining the particle
[*] Dr. J.-S. Jurng, H. A. Le, Dr. S.-M. Chin, E.-S. Park, Dr. G.-N. BaeKorea Institute of Science and Technology (KIST)39-1 Hawolgok, Seongbuk, Seoul 136-791 (Republic of Korea)E-mail: [email protected]
H. A. LeUniversity of Science and Technology (UST)176 Gajung-dong, Yuseong-gu, Daejeon (Republic of Korea)
E.-S. ParkUniversity of Seoul, 90 Jeonnong-dongDongdaemun-gu, Seoul 130-743 (Republic of Korea)
[**] This work has been supported by theMinistry of Environment (192-091-001), the Ministry of Education, Science and Technology(2011K000750).
6 wileyonlinelibrary.com � 2012 WILEY-VCH Verlag Gmb
morphology, such as the crystal phase, size, specific surface
area, surface composition, and chemical state.[15,17] In this
study, V2O5 nanoparticles were obtained by the thermal
decomposition of a vanadium oxytriethoxide (VOTE)
solution. The detailed microstructural characteristics of
the thermally decomposed nanoparticles were examined as
a function of the synthesis temperatures (500–1300 8C).Figure 1a shows X-ray diffraction (XRD) patterns of the
V2O5 nanoparticles prepared at each synthesis temperature.
The XRD patterns of the V2O5 samples synthesized at 900,
1100, and 1300 8C showed similar patterns with different
peak intensities, and indicated a single-Shcherbinaite phase
with an orthorhombic structure (JCPDS Card No. 41-1426)
and lattice parameters of a¼ 1.1516 nm, b¼ 0.332 nm, and
c¼ 0.43727 nm.[8,10] In addition, the peak intensities of the
V2O5 samples increased with increasing synthesis tempera-
ture to 900 and 1300 8C, indicating enhanced crystallization.
The peaks (001) intensity became higher and the peak shape
narrower, indicating an increase in V2O5 crystallite or grain
size, which was calculated from the line broadening of (001)
diffraction peak using the Debye-Scherrer formula
(r¼ 3.4 g cm�3) as listed in Table 1. No peaks of other
phases were observed in the XRD pattern, suggesting that
theV2O5 nanoparticles prepared byCVC contained a single,
highly crystalline phase without impurities. On the other
hand, no detectable peaks were observed at synthesis
temperatures of 500 and 700 8C, indicating the presence of
an amorphous structure.
N2 adsorption/desorption isothermal tests were carried
out using the Brunauer-Emmett-Teller (BET) and Barrett-
Joyner-Halenda (BJH) methods to estimate the pore size
distribution and adsorption properties of the prepared
samples, the isotherm curves of which are presented in
Figure 1b. The isotherm of the prepared samples showed
typical Type IV (BDDT classification) curves, and their
narrow hysteresis loops exhibited a typical Type H3
pattern,[8] indicating the presence of mesopores (2–50 nm).
In thermal decomposition synthesis of the precursor
solution, the particle morphology depends strongly on the
synthesis conditions, such as the synthesis temperature,
precursor concentration, and precursor aerosol residence
time in the heating zone. In particular, the synthesis
temperature is an important factor determining the resulting
particle size, crystallinity, and phase.[15] Figures 2 a to e
present transmission electron microscopy (TEM) images of
the V2O5 samples produced by CVC at various synthesis
temperatures. Figures 2a and b indicate that the samples
prepared at 500 and 700 8C have an amorphous structure.
Meanwhile, the particle structure was nanorods,[18] ribbon-
like shape,[9] or strip-like shape[19] at higher temperatures
(900–1300 8C). The particle size, dBET in Table 1, gradually
increased with increasing synthesis temperature from 900 to
H & Co. KGaA, Weinheim Chem. Vap. Deposition 2012, 18, 6–9
Communication
Fig. 1. a) XRD patterns, and b) hysteresis loop, of V2O5 nanoparticles synthesized at various synthesis temperatures.
Table 1. Physico-chemical properties of the prepared samples at various temperatures. The values in parentheses are the area ratio (%).
Synthesis
temperature
[8C]
SBET[m2 g�1]
dBET[a]
[nm]
dXRD[b]
[nm]
Vp
[cm3 g�1]
dpore[nm]
V 2p3/2 O 1s
V1 V2 O1 O2
500 37.1 � � 0.116 12.6 517 (70.9) 516.2 (29.1) 529.9 (70.1) 530.7 (29.9)
700 48.5 � � 0.341 28.1 517 (76.6) 515.8 (23.4) 529.9 (74.6) 530.7 (25.4)
900 46.8 37.7 25.1 0.269 29.6 517 (82.4) 516 (17.6) 529.9 (100) �1100 39.3 44.9 23.7 0.179 18.2 517 (89.4) 516 (10.6) 529.9 (100) �1300 36.3 48.6 33.8 0.223 19.1 517 (83.1) 516.3 (16.9) 529.9 (100) �[a]Particle size by equation using BET surface area.[b]Crystallite size calculated using Debye-Scherrer formula after analysis of XRD patterns using the PowderX program.
1300 8C. In addition, the resulting particles had various
colors according to the synthesis temperature, as shown in
the second row of Figure 2. Black powders at the 500 and
700 8C samples could be assigned toV4þ, while dark-green at
900 8C and completely bright yellow-orange at 1100 and
Fig. 2. PSD (top), TEM images (middle) and photographs (bottom) of the prepare
Chem. Vap. Deposition 2012, 18, 6–9 � 2012 WILEY-VCH Verlag Gm
1300 8C (which is the color of pure V2O5,[6,20,21]) correspond
to V5þ. Figure 2 (top row) also shows the particle size
distribution (PSD) of the samples synthesized at 900, 1100,
and 1300 8C with modal sizes at 15, 60, and 30 nm,
respectively. There are significant gaps in the particles sizes
d samples at various synthesis temperatures.
bH & Co. KGaA, Weinheim www.cvd-journal.de 7
Communication
that were calculated, based on the XRD and BET results, at
synthesis temperatures of 900 to 1300 8C, showing differ-
ences (dXRD/dBET) of a factor of 0.53 to 0.7. The possible
reason for this difference is polydispersity since dBET is a
surface-weighted particle property, whereas crystallite size
(dXRD) is a mass-weighted particle property. The TEM
images in Figure 2 show that the morphology of the samples
is not uniform, which means that it is difficult to estimate the
diameter of this material by one value.
Figure 3 shows the X-ray photoelectron spectroscopy
(XPS) spectra of theO 1s and V 2p3/2 regions. Generally, the
photoelectron peaks of O 1s could be resolved into two
components. The dominant peak at about 529.9 eV was
characteristic of metallic oxides, which was in agreement
with O 1s electron binding energy (BE) arising from
vanadium.[22] The O 1s excitation spectrum of the vanadyl
oxygen is characterized by a large peak centered at 530.7 eV
which could be assigned to V-O(2)-V bridging oxygen.[23]
Values for the V 2p3/2 BE for the various oxidation states of
Fig. 3. XPS spectra of theO 1s andV 2p3/2 regions for the prepared samples at
various synthesis temperatures.
8 www.cvd-journal.de � 2012 WILEY-VCH Verlag GmbH
vanadium are presented in Table 1. The main peak position,
517.0 eV, is lower than the literature datum (517.2 eV),[3]
corresponding to V2O5 stoichiometry (V5þ), however all
samples also have a ‘‘shoulder’’ peak in the V 2p3/2 at 515.8–
516.3 eV which could also be assigned to V4þ ions.[24] It can
be concluded that the oxidation of the vanadium on the
surface of nanorods is between þ4 and þ5. The mixed
valence, V4þ/5þ, was said to be crucial to the higher electric
conductivity.[25] Thus, the XPS results are in good agree-
ment with the XRD results.
V2O5 nanoparticles were successfully synthesized using
VOTE aerosol as the vanadium precursor, by thermal
decomposition in an electric furnace without additional
calcination. At lower temperatures (500–700 8C), the
obtained product had an amorphous structure. At higher
temperatures (900–1300 8C), single, highly crystalline V2O5
nanoparticles, without impurities, were synthesized. The
particle size and crystallinity increased with increasing
synthesis temperature. In addition, the colors of the
resulting particles differed according to the synthesis
temperatures (black, dark-green, and bright yellow-orange).
Experimental
Synthesis of Vanadium: In this study, the V2O5 powders were preparedby CVC. Detailed CVC process and preparation of V2O5 nanoparticles byCVC are described elsewhere [1,17]. The VOTE (VO(OC2H5)3, Aldrich,>97%) solution was used as the V2O5 precursor and was stored in a bubblerthat was placed in an oil bath at 95 -C. The bubbler was wrapped with heatingtape (90 -C) to prevent any loss due to condensation. The argon (the precursorcarrier gas) and air (the diluent gas) flow rates were fixed at 0.7 and7.0 Lmin�1, respectively. An alumina tube (0.8m in length and 0.01m indiameter) was placed in an electric furnace controlled by a temperaturecontroller. The precursor aerosol residence time in the heating zone wasapproximately 0.47 s. The VOTE vapor concentration was calculated as6.74T 10�5mol L�1 by assuming that the carrier gas through the bubbler wascompletely saturated. The synthesis temperature was varied from 500 to1300 -C at 200 -C intervals.
Characterization: The crystal phases of the prepared samples wereexamined by XRD (Rigaku D/Max 2500) using Cu Ka radiation. The XRDpattern and data were also analyzed using the PowderX program. TEManalysis was carried out using a CM-30 microscope (Philips; operated at300 kV, image resolution <0.23 nm). The TEM images were analyzed usingflexible plugin architecture of the public domain image processing programImageJ to determine precisely the primary particle size (dTEM) and PSD. Thepowder specific surface area (SSA, m2 g�1) was determined by nitrogenadsorption (>99.999%) at 77K on a Micromeritics Tristar 3000 apparatususing the BET method. The pore volume distribution was determined fromthe desorption isotherms (Micromeritics ASAP 2010 Multigas system) usingthe BJH method. Assuming monodispersity and spherical primary particles,the BET-equivalent particle diameter (dBET) was calculated using theformula, dBET¼ 6/(rT SSA), where r is the particle density. XPS (VGscientific ESCA Lab II) with a resolution of 0.1 eV was performed with MgKa (1253.6 eV) radiation as the excitation source. All BEs were referenced tothe C 1s peak at 285.0 eV for adventitious carbon. After subtracting theShirley-type background, the core-level spectra were decomposed into theircomponents with mixed Gaussian-Lorentzian lines using a non-linear, leastsquares, curve-fitting procedure on the public software package XPSPEAKv.4.1.
Received: August 1, 2011
Revised: October 26, 2011
[1] G. T. Chandrappa, N. Steunou, S. Cassaignon, C. Bauvais, J. Livage,Catal. Today 2003, 78, 85.
& Co. KGaA, Weinheim Chem. Vap. Deposition 2012, 18, 6–9
Communication
[2] M. N. Field, I. P. Parkin, J. Mater. Chem. 2000, 10, 1863.
[3] J. Musschoot, D. Deduytsche, H. Poelman, J. Haemers, R. L. VanMeirhaeghe, S. Van den Berghe, C. Detavernier, J. Electrochem. Soc.2009, 156, P122.
[4] C. Piccirillo, R. Binions, I. P. Parkin, Chem. Vap. Deposition 2007, 13,145.
[5] F. Sediri, N. Gharbi, J. Phys. Chem. Solids 2007, 68, 1821.
[6] A. Bouzidi, N. Benramdane, A. Nakrela, C. Mathieu, B. Khelifa, R.Desfeux, A. Da Costa, Mater. Sci. Eng, B 2002, 95, 141.
[7] M. Gotic, Mater. Lett. 2003, 57, 3186.
[8] T. Puangpetch, S. Chavadej, T. Sreethawong, Powder Technol. 2011,208, 37.
[9] M. A. Zoubi, H. K. Farag, F. Endres, J. Mater. Sci. 2008, 44, 1363.
[10] Z. J. Lao, K. Konstantinov, Y. Tournaire, S. H. Ng, G. X. Wang, H. K.Liu, J. Power Sources 2006, 162, 1451.
[11] D. Shin, C. Bang, Y. Hong, H. Uhm, Mater. Chem. Phys. 2006, 99, 269.
[12] W. Chang, G. Skandan, H. Hahn, S. Danforth, B. Kear, Nanostruct.Mater. 1994, 4, 345.
[13] M. T. Swihart, Curr. Opin. Colloid Interface Sci. 2003, 8, 127.
Chem. Vap. Deposition 2012, 18, 6–9 � 2012 WILEY-VCH Verlag Gm
[14] M.Wintere,Nanocrystalline Ceramics: Synthesis and Structure, Springer,Germany 2002.
[15] S. Chin, E. Park, M. Kim, J. Jurng, Powder Technol. 2010, 201, 171.
[16] E. Park, S. Chin, J. Kim, G.-N. Bae, J. Jurng, Powder Technol. 2011, 208,740.
[17] H. A. Le, S. Chin, E. Park, L. T. Linh, G. N. Bae, J. Jurng, Chem. Vap.Deposition 2011, 17, 228.
[18] N. Asim, S. Radiman, M. A. Yarmo, M. S. Banaye Golriz, MicroporousMesoporous Mater. 2009, 120, 397.
[19] C. Zheng, J. Solid State Chem. 2001, 159, 181.
[20] W. Chen, Mater. Lett. 2004, 58, 2275.
[21] K. Melghit, S. Pillai, D. V. Kumar, J. Mater. Sci. Lett. 1999, 18, 661.
[22] L. Li, C.-Y. Liu, Y. Liu, Mater. Chem. Phys. 2009, 113, 551.
[23] M. Cavalleri, K. Hermann, A. Knop-Gericke, M. Havecker, R. Herbert,C. Hess, A. Oestereich, J. Dobler, R. Schlogl, J. Catal. 2009, 262, 215.
[24] Y. Ishige, T. Sudayama, Y. Wakisaka, T. Mizokawa, H. Wadati, G.Sawatzky, T. Regier, M. Isobe, Y. Ueda, Phys. Rev. B: Condens. MatterMater. Phys. 2011, 83, 125112.
[25] C. Tsang, A. Manthiram, J. Electrochem. Soc. 1997, 144, 520.
bH & Co. KGaA, Weinheim www.cvd-journal.de 9