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ISRN Nanomaterials
Volume 2012 (2012), Article ID 687641, 7 pages
http://dx.doi.org/10.5402/2012/687641
Research Article

Structure and Composition of Ba-W-Ti-O Ceramics Interface Regions Formed at Ultrasonic Vibration

1Physical-Technical Institute UB RAS, 132 Kirov Straße, Izhevsk 426000, Russia
2Kotelnikov Institute of Radio Engineering and Electronics, RAS, 11 Mokhovaya Straße, Korp. 7, Moscow 125009, Russia
3Scientific-Educational Nano-Center, Tomsk Polytechnic University, 30 Lenin Avenue, Tomsk 634050, Russia

Received 2 April 2012; Accepted 29 April 2012

Academic Editors: C. Angeles-Chavez, G. Speranza, and V. Yamakov

Copyright © 2012 O. Karban 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.

Abstract

The study of Ba-W-Ti-O ceramics has shown that the structure and composition of their interface regions differ from those in the grain bulk owing to the diffusion of tungsten atoms to the grain surface during sintering. They are determined by the conditions of compacting of dry nanopowders (compaction pressure and power of ultrasonic action) and vary in a nonmonotonic way. Increasing the pressure during dry static compacting and exposure to ultrasound result in the formation of a complex structure of fragments and boundaries between them, increasing the acoustic density and decreasing the intergranular boundary thickness. This affects the travel time of the phonon pulse through the sample, which allows one to determine the density and thickness of the grain boundaries by the method of phonon spectroscopy.

1. Introduction

The functional characteristics of the segnetoelectrical ceramics based on BaTiO3-WTiO3 depend on the structure which in turn depends on the conditions of manufacture. The physical characteristics of barium-titanate ceramics were shown to be size dependent [14], and the Ba/Ti ratio was found to determine the grain growth mechanism [5, 6]. At the same time, as was shown in [79], the relation between the elements in the ceramic interface regions may substantially differ from that in the bulk, which can result in both phase transformation and new phase formation. There may form, for example, a cubic-phase layer in the interface regions of polycrystalline tetragonal ceramics BaTiO3 [10], a BaCO3 phase as a result of interaction with atmospheric CO2 on heating [11], and a glass phase in the interface areas of segnetoelectrical ceramics [12]. The changes in structure and phase composition occurring during sintering depend on both rheological heredity and compacting parameters.

The most used technologies are based on various powder consolidation techniques: uniaxial static pressing [12], dynamical pressing, and hydrostatic pressing which, as a rule, lead to large density gradients in compacts of complex shape. This may cause deformation or crack initiation during sintering, and it is impossible to reduce mechanical stresses in the compacted object and minimize the inhomogeneous deformation during subsequent sintering of such ceramic compacts without plasticizers. However, the use of plasticizers and binding agents is not always possible as it may cause the material contamination and the increase of residual porosity. The density and stress distribution in the bulk of compacts depend on the conditions of wall friction on compacting.

As known, the exposure to ultrasound (US) during dry uniaxial compacting reduces the interparticle friction and favors uniform close particle packing in compacts [13]. In this work we have studied the effect of the ultrasound power applied during powder compacting on physical properties of ceramic compacts.

2. Experimental

The nanosized powders of BaTiO3-WTiO3 composition with an average particle size of 50 nm obtained by the sol-gel method were compacted by uniaxial dry pressing under US action (the amplitude of 5÷10𝜇m, the frequency of 20–22 kHz). The scheme and characteristics of the equipment for obtaining samples are described in [13]. The compacting parameters (compacting pressure and US power) are listed in Table 1. The ceramics were sintered at a temperature of 1623 K for 3 hours. The sintered specimens had the shape of a parallelepiped 2×14×8 mm in size having 8 holes of diameter 0.6 mm with a positioning precision of ±5 microns (Figure 1). The same tolerance value was required for the specimen dimensions.

tab1
Table 1: Compacting parameters (compacting pressure P, US power W), density 𝜌, and phase composition according to X-ray diffraction analysis of the studied specimens of BaTiO3-WTiO3 ceramics.
687641.fig.001
Figure 1: Ceramic cases of microwave amalgamators from BaTiO3-WTiO3 nanopowders.

The X-ray studies were performed with a DRON-3 diffractometer in CuK𝛼 monochromatic radiation. The images of the specimen surface chips were obtained with a scanning electron microscope (SEM) Philips XL30 and a scanning probe microscope Solver P47. The chemical composition was analyzed by the X-ray photoelectron spectroscopy (XPS) using modified ES-2401 spectrometer. The spectra were excited by the MgKα radiation. The vacuum in the analyzer chamber was 5·10−6 Pa. The spectra were calibrated against the C1s-line (𝐸𝑏=285.0 eV) of the adsorbed hydrocarbon layer [14]. The mathematical treatment of the spectra was carried out by a technique based on the Fourier analysis with an improved convergence procedure [15]. The specimens for XPS analysis were prepared as chips.

The structure of the ceramics interface regions and their specimen-average characteristics were investigated by the heat pulse method [16]. This approach is based on the analysis of the weakly nonequilibrium phonon (NP) transport in the specimen studied at helium temperatures when the NP wavelength 𝜆 is less than the mean grain size R but comparable to the intergranular interface thickness. The method and the model used as well as the peculiarities of the data processing are detailed in [17, 18]. In this work we analyzed the propagation of the flow of weakly nonequilibrium thermal phonons generated by pulse heating of a metal (gold) film deposited on a face of the specimen under study. The phonon nonequilibrium pulse transmitted through the imperfect specimen was registered on the opposite side by a broadband detector (bolometer) based on a superconducting thin film. The measurements were performed at helium temperatures at which inelastic phonon-phonon processes are unlikely. The thermostat temperature 𝑇0 could be modified by means of He vapor evacuation in the 1.5–3.8 K interval. The bolometer operating point was shifted in temperature by the field of a superconducting magnet situated in the immediate vicinity of the bolometer. The power generated in the NP-injector film (Au) amounted to 102÷101 W/mm2 (the pulse duration was 100 ns), the film being heated to a temperature 𝑇 such that 𝑇=𝑇𝑇0𝑇0. This allowed us to assume the Planck distribution of NP phonons to have the thermostat temperature. The measurements performed at different 𝑇0 permitted to obtain the temperature characteristics of subterahertz NP scattering.

3. Results and Discussion

The density of the sintered specimens was 4.43–4.52 g/cm3 (Table 1). With increasing compacting pressure, the specimen density grows reaching its maximum at 𝑃=874.4 MPa and 𝑊=1.5 KW. With further increase in compacting pressure, the sintered-specimen density decreases in contrast to the compacts whose density increases monotonically with pressure [19].

The diffractograms of sintered Ba-W-Ti-O ceramics are presented in Figure 2. The specimens contain the BaTi4O9, Ba2Ti9O20, and BaWO4 phases (Table 1). According to the phase diagram of refractory oxides BaO-TiO, the specimens annealed at temperatures above 1623 K are characterized by a combination of BaTi4O9 and Ba2Ti9O20 compounds [20]. In all the specimens, except 3, one can observe a segnetoelectrical phase WO3 whose lattice parameter (𝑎=0.3837nm) is typical of a film structure. At the maximum values of compacting parameters (specimen 5), there appears a metastable phase BaTi2O5.

687641.fig.002
Figure 2: Specimen diffractograms.

XRD is used to obtain the phase information in the bulk, while XPS mainly probes the grain interface [21].

3.1. X-Ray Photoelectron Spectroscopy

According to the scanning electron microscopy (SEM) and atomic-force microscopy (AFM) data, the fracture in the specimens occurs at the grain boundaries; therefore, an analysis of the XPS spectra of the chip surface made it possible to define the composition of the ceramics interface regions. In the 𝑊4𝑓7/2 spectra (Table 2) one line corresponding to W6+ is observed: tungsten may be present in the form of either WO3 or (WO4)2 [22] which cannot be distinguished. In the 𝑇𝑖2𝑝3/2 spectra the line of energy 458.6÷458.8 eV corresponding to Ti4+ [23] is dominant practically in all specimens. Ti3+ is present only in specimen 5 obtained at 𝑃=1050.4 MPa and 𝑊 = 3 kW.

tab2
Table 2: Binding energy and relative content of Ti, Ba, and W in XPS spectra.

In the 𝐵𝑎3𝑑5/2 spectra of the studied specimens three peaks corresponding to barium atoms in different chemical environments were detected: 𝐸𝑏Ba(I)=779.4±0.1 eV; 𝐸𝑏Ba(II)=780.5±0.1 eV; 𝐸𝑏Ba(III)=781.5±0.1 eV.

In an XPS study of polycrystalline barium titanate (BaTiO3) [24] the peak Ba(I) was attributed to barium atoms in perovskite-like structures. In the same paper much attention was given to interpretation of the Ba(I) peak which may be ascribed to barium in the Ba(OH)2 and BaCO3 compounds. Such an interpretation, however, takes no account of the analysis of the C1s and O1s spectra. In the case of the BaCO3 formation in the C1s spectrum a component with binding energy (289.4÷290.8) eV should be observed [22]. The Ba(II) peak is also attributed [23] to Ba atoms in perovskite structures.

It is known that changes in the element-oxygen interatomic distance result in a shift of the element and oxygen XPS spectral lines. So, it was shown [25] that different structural constituents of vitreous silicium dioxide differ in the position of O1 s and Si2p peaks: a 0.004 nm change in the Si-O distance results in the shift of the O1s peak by 0.3 eV and Si2p by 0.3–0.9 eV. An analogous situation is apparently observed for the Ba(I) and Ba(II) structures. Both structures are perovskite-like but distorted and differ in the Ba-O interatomic distance.

The available data for the 𝐸𝑏 value of Ba3d in the BaTi3 perovskite structure substantially differ in magnitude: 778.5, 780 eV [23], 789 eV [12], 780.0 eV [26], and 778.8 eV [22]. This difference may be caused by distortions in the perovskite structure, all the structures being perovskite-like.

The position of the Ba3d peak (line) of (in) BaCO3 corresponds to 𝐸𝑏 of 779.8 [22] –780.0 эB [26] Пoлoжeниe Ba3d линии BaCO3соответствyет   𝐸𝑏 779.8 [22] –780.0 [26] эB.

The position of the O1s oxygen peak of barium hydroxide (531.2 eV) coincides with the position of the peak of O atoms included in oxygen-containing organic functional groups (C–O) which are present in the adsorbed hydrocarbon layer on the chip surface. Therefore, an analysis of the Ba3d and O1s XPS spectra cannot provide an unambiguous answer to the question of the barium hydroxide presence on the surface of the ceramic chips under study.

According to the X-ray phase analysis, the ceramics investigated include some compounds of perovskite-like structure: BaTi4O9 and Ba2Ti9O20 (Table 3). In order to determine to what exactly barium compound correspond the Ba(I) and Ba(II) peaks, one should study the standard specimens of barium titanates.

tab3
Table 3: The Ti: Ba: W ratio (at.%) in the bulk (XRD data) and interface regions (XPS) of the ceramics investigated.

The Ba3d peak with binding energy 781.5 eV, lacking in the XPS spectra of the samples investigated in [22], may be attributed to Ba atoms included in a structure other than perovskite. So, two perovskite-like structures (I and II) that probably differ in composition are present on the chip surface. The structure I is observed only in specimens 1 and 5, while the structure II appears with increasing compacting pressure to 525 MPa in specimen 2, decreases with pressure in specimen 3, and disappears in specimens 4 and 6. The structure III is a compound other than perovskite. In specimens 1→ 3→4, 6 its content increases from ~60% to ~100%.

The Ba : Ti : W ratio (at.%) in the bulk, obtained from the X-ray phase analysis, is presented in Table 3 in comparison with that in the interface regions (XPS data). The difference in elemental composition between the bulk and the interface regions is due, in particular, to an increase in the content of tungsten which diffuses during sintering into the grain-surface areas by the action of temperature.

The titanium and barium content diminishes, the decrease in the number of Ti atoms being greater, as seen from the Ba : Ti ratio.

With increasing compacting pressure the tungsten content grows on the chip surface of sintered specimens. The structure III is likely to correspond to scheelite BaWO4 whose amount in the interface region may increase as the Ba and W fractions grow. The line 781.5 eV corresponds to a metastable modification of barium titanate arising only in interface regions. Since the layer analyzed by the XPS method is several nanometers thick, this metastable modification may exist as a film phase. Moreover, such a considerable difference in W concentration between the grain surface and the bulk confirms the assumption that WO3 forms only in the interface regions. As the content of the perovskite-like structure in the interface regions decreases and then completely disappears with increasing pressure, one can suppose that the acoustic transmission of the boundaries must grow as a consequence of the decrease in structure imperfection of the interface regions.

3.2. Phonon Spectroscopy

The experimental technique and the analysis of propagation of nonequilibrium phonons in ceramic materials were reported in [17]. In this study, the samples were plane-parallel polished plates with a thickness (L) 0.1–1.0 mm and an area of about 0.5 cm2. The phonon injector (gold) and detector (tin) films were formed on the opposite faces of the samples by thermal deposition in vacuum. Experiments were performed in liquid helium in the temperature range 1.5–3.8 K. The thermostat temperature was varied by pumping off helium vapor. The temperature measurement accuracy was no worse than 103 K. The operating point of the bolometer was shifted by applying a weak magnetic field. The experimentally measured value was the time 𝑡𝑚 of arrival of the maximum diffusion signal of nonequilibrium phonons at the detector (bolometer). Phonons were injected from the metal film located on the opposite face of the sample and heated by a short (107 s) current pulse to a temperature 𝑇;𝑇=𝑇𝑇0𝑇0 (𝑇0 is the thermostat temperature). This approach made it possible, providing 𝑇𝑇0 and changing the thermostat temperature, to obtain the temperature dependence 𝑡𝑚(𝑇).

The diffusion mode was controlled by the corresponding dependence of 𝑡𝑚 on the specimen thickness: 𝑡𝑚(𝐿)𝐿2.

The experimentally measured time of the phonon nonequilibrium diffusion signal maximum, 𝑡𝑚(𝑇), is definitely related to the effective diffusion coefficient 𝐷e(𝑇) by the transport mean free path 𝑙tr of nonequilibrium phonons of frequency 𝜔2,8kT/h [17] 𝐷e𝐿(𝑇)=22𝑡m=1(𝑇)3𝑙tr,(𝑇)𝑣(1) where L is the specimen size in the NP flow direction; v is the average sound velocity (in the ceramics under study 𝑣=4.54105 cm/s); T is the NP temperature. A comparison between the experimental temperature dependences of the NP scattering and theory was performed by the relation [27] 𝑙tr=𝑙0𝑓𝜔1𝑓𝜔,(2) where 𝑓𝜔 is the probability of the nonequilibrium phonon passage through the grain boundary [18]; 𝑙00,6𝑅 is the mean ballistic path of NP in a single grain of size 𝑅.

Figure 3 presents a set of theoretical curves of 𝑓𝜔/(1𝑓𝜔) as a function of q2𝑙gb calculated for different ratios between the acoustic impedances of the grain material,𝜌1𝑣1, and intergranular layer, 𝜌2𝑣2; 𝑙gb is the layer thickness, and 𝑞1,2 are the wave vectors of a phonon of frequency 𝜔 in the grain material and intergranular layer, respectively: 𝑞1=2.8𝑘𝑇𝑣1,𝑞2=𝑞1𝜌2𝑣2/𝜌1𝑣1.(3) For each specimen the experimental values of temperature dependences 𝑙tr(𝑇)/0,6R were fitted to a theoretical curve. In the case of a good fit of the experimental dependence to the theoretical curve (corresponding to a particular value of 𝜌2𝑣2/𝜌1𝑣1) the thickness 𝑙gb was determined. The 𝑙gb value for each specimen and the corresponding parameters 𝜌2𝑣2/𝜌1𝑣1 are presented in Table 4.

tab4
Table 4: Characteristics of the nanoceramics under study*.
687641.fig.003
Figure 3: The probability 𝑓𝜔/(1𝑓𝜔) of the NP flow passing through the plane intergranular boundary of thickness 𝑙gb as a function of 𝑞2𝑙gb. (1) 𝜌2𝑣2/𝜌1𝑣1 = 0.6; (2) 0.7; (3) 0.75; (4) 0.8; (5) 0.85. The experimental points for specimens: 1 (); 2 (□); 3 (△); 4 (*); 5 (○); 6 (×), and a specimen prepared with a different procedure ().

In the ceramics studied different boundary types are observed: boundaries between agglomerates, between grains in the agglomerates, and boundaries between areas of coherent scattering. However, a satisfactory agreement between the theoretical calculations and the experimental temperature dependences of NP scattering is observed only in the case when R is the size of grains (particles) forming the agglomerates. Indirect evidence on the efficiency of NP scattering at different boundaries in ceramics may be provided by the value of the 𝑙tr/R ratio. So, for specimen 4 at T = 3.8 K this ratio is 1.4 for agglomerates, 8 for grains, 15–30 for CSA, and it increases as the NP temperature (energy) decreases. It may appear that the main contribution to the NP scattering should come from the agglomerate boundaries, but then, because of the large boundary thickness, the experimental NP scattering dependences would lie on the wings of the theoretical curves and exhibit a weaker dependence of 𝑙gb(T)/d on 𝑞2𝑙gb (temperature). This is not the case because the intergranular boundaries greatly exceed the boundaries between agglomerates in number, and it may be concluded that the temperature dependence of the NP scattering is determined by the scattering at boundaries between the grains forming the agglomerates.

Consider now the results presented in Figure 3. The experimental points obtained for specimens 1 and 5 lie on the same curve (i.e., are characterized by the same impedance), which corroborates the XPS evidence for the existence, in interface regions, of the structure Ba(I) being characteristic of these specimens only. The difference between them in temperature dependence 𝐷(𝑇) suggests that in specimen 5 the thickness of the interface region diminishes and its hardness (i.e., impedance) grows as a result of an increase in the content of cubic phase WO3. The difference in the interface region structure revealed by XPS in specimens 4 and 5 compacted at a pressure 𝑃=1040.5 MPa and different power of ultrasonic activation is also confirmed by the phonon spectroscopy data. Specimens 1 and 2 compacted at low pressures without US action are distinguished by a large boundary thickness. The optimum boundary structure is found in specimens compacted at a pressure of about 700–800 MPa which allows the formation of an interface region with prevailing content of isotropic structure.

4. Conclusion

In the studied segnetoelectrical Ba-W-Ti-O ceramics, compacted under different conditions of pressure and ultrasound action with subsequent sintering at 1623 K, the ceramic phase composition, as well as the structure and composition of the interface regions, varies in a nonmonotonic way. It is shown that the interface region composition substantially differs from that of the grain bulk owing to the diffusion of tungsten atoms to the grain surface during sintering. Increasing the compacting pressure is favorable to the retention of the BaWO4 phase in the bulk of a specimen. Increasing the pressure during dry static compacting and exposure to ultrasound result in the formation of a complex structure of fragments and boundaries between them, increase the acoustic density, and lead to a decrease in the intergranular boundary thickness to the values that are sometimes comparable to the lattice constant of the boundary material. The boundary structure becomes optimum at a pressure of about 700–800 MPa, which is due to a decrease in the perovskite structure content in the interface regions.

Acknowledgments

This work was supported by the RFBR Grant no. 11-02-00704, Russian Ministry of Science and Education (contract no. 13.G25.31.0021; state assignment “Science”).O. Khasanov is thankful to Dr. S. A. Fomin for useful discussions.

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