Journal of Solid State Physics

Volume 2014 (2014), Article ID 585701, 4 pages

http://dx.doi.org/10.1155/2014/585701

Research Article

Preparation and Electrical Properties of Ba₂TiOSi2− xGexO₇ ( and ) Ferroelectric Ceramics

S. K. Barbar¹ and M. Roy²

¹Materials Science Laboratory, Department of Physics, J.N. Vyas University, Jodhpur, Rajasthan 342001, India

²Materials Science Laboratory, Department of Physics, M.L. Sukhadia University, Udaipur, Rajasthan 313002, India

Received 11 April 2014; Revised 23 June 2014; Accepted 24 June 2014; Published 14 July 2014

Academic Editor: Ya Cheng

Copyright © 2014 S. K. Barbar and M. Roy. 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.

Polycrystalline ceramic samples of pure and germanium (Ge⁴⁺) doped fresnoite of general formula Ba₂TiOSi2−xGexO₇ ( and 0.2) have been prepared by solid state reaction technique. The formation of the single phase compound was confirmed by X-ray diffraction and the structural parameters were refined by the Rietveld refinement technique. The dc conductivity of both the materials has been measured as a function of temperature from room temperature to 753 K and activation energy was calculated using the relation . The activation energy 4.74 eV obtained for the pure compound is very high in comparison with 1.47 eV of Ge⁴⁺-substituted compound. The frequency and temperature dependent dielectric behavior of both the compounds have been studied. The real and imaginary parts of the dielectric constant increase with the increase of temperature.

1. Introduction

Fresnoite, a rare barium titanium silicate mineral, Ba₂TiOSi₂O₇, was discovered during the geological investigation of the sanbornite deposits at Fresno County, California [1]. The mineral shows a noncentrosymmetric tetragonal crystal structure with space group P4bm [2]. Due to its noncentrosymmetricity, the material shows good ferroelectric, piezoelectric, pyroelectric, optical, and other physical properties useful for different practical devices [3–8]. The single crystal data of fresnoite shows a broad peak in dielectric permittivity at ~433 K but the same peak is absent in dielectric loss curve. It is surprising that the ceramic samples fail to reveal the dielectric anomaly shown in case of single crystal at 433 K [3]. Not only that, but a small reproducible dielectric anomaly has also been reported in the frequency range 0.1–100 kHz at 805 K. However, the single crystal X-ray data taken at 297 K and 573 K revealed no change in symmetry except small changes in atomic position, the largest of which were less than 0.02 Å [8]. Recent studies on oriented crystallization using thermal gradient, crystallization kinetics, and electrical properties through impedance spectroscopy were also carried out on fresnoite and fresnoite like glassy materials [9–11]. The ceramic sample also showed good hysteresis loop at room temperature but the shape of the loop remained unchanged when temperature increased to 875 K. It is surprising that the high temperature X-ray, DTA, and specific heat measurements gave no indication of phase transition.

The present paper reports on the synthesis, X-ray diffraction, dc conductivity, and dielectric properties of pure and 10% Ge-doped fresnoite compounds.

2. Materials and Method

The Polycrystalline ceramic samples of pure and Ge-substituted fresnoite compounds of general formula Ba₂TiOSi2−xGexO₇ ( and 0.2) were prepared by conventional solid state reaction technique using high purity (99.9%) carbonates and oxides (BaCO₃, TiO₂, GeO₂ and SiO₂). Stoichiometric mixture of these oxides and carbonates was thoroughly mixed and grinded for several hours and then calcined at 800–900°C in silica crucible in air atmosphere. The process of mixing and calcination was repeated until a fine homogeneous powder of the material was obtained. The resulting mixture was compressed into pellet form and sintered at desired temperature. The complete synthesis process of both the compounds was reported in our earlier paper [12]. The formation of the single phase compound was checked by X-ray diffraction pattern using the Rigaku X-ray diffractometer with CuKα radiation and nickel filter in a wide range of from 10 to 70° with a scanning rate of 2° per minute. The dc electrical conductivity as a function of temperature was measured by laboratory made setup. The dielectric constant and dissipation factor as a function of frequencies (100 Hz to 2 MHz) and temperature (300 K–673 K) were measured by Hioki 3532-50 LCR HiTester. The dc conductivity and dielectric measurements were performed on the circular dish-shaped samples with silver paint coated on two sides as the electrodes.

3. Results and Discussion

The room temperature (RT) X-ray diffraction patterns of the samples Ba₂TiOSi2−xGexO₇ ( and 0.2) are shown in Figure 1. From the X-ray diffraction pattern it is observed that there is a small shift in some of the peaks positions and intensities for the substituted compound with respect to the pure compound. The detailed Rietveld refinement of X-ray diffraction data for both the compounds was reported in our earlier paper [12]. The lattice parameters and some other structural parameters are summarized in Table 1.

Table 1: Structural and electrical parameters of Ba₂(TiO) ( and 0.2).

Composition
()
()
()
Tetragonality (/)
(eV)

8.542
5.220
381.083
0.61
4.74

8.551
5.222
383.437
0.61
1.47

(a)

(b)

Figure 1: RT X-ray diffraction patterns of Ba₂TiOSi2−xGexO₇ ( & 0.2).

The temperature dependence of dc electrical conductivity () for both the compositions has been evaluated by taking the steady-state values of current and results are plotted for elevated temperature range from 643 to 753 K shown in Figure 2. The resistivities of these samples are so high that they are almost temperature independent from RT to 643 K and hence the results are plotted for an elevated temperature range from 643 to 753 K. The high resistivity of the samples reveals the insulating property of ferroelectrics. Not only this, when an electric field is applied to the samples, there is the known reorientation of the dipoles, but also the displacement of the charge carriers. Therefore, the electrical conductivity behavior should be considered for ferroelectricity. After 643 K, the conductivity of both the samples increases up to the measured temperature range. The increase in conductivity may be explained by the fact that it is a consequence of thermally activated processes, which can be described by the Arrhenius relation:

where is the preexponential factor, is the activation energy, and is the Boltzmann constant having the value  eV/K. The Arrhenius equation is an accurate formula for the temperature dependence of reaction rates. In the natural logarithm form, the Arrhenius equation has the same form as an equation for a straight line; hence, we fit the data as a straight line and calculate the activation energy by measuring the slope of this straight line. The activation energies of both the samples ( and 0.2) were calculated from versus 1000/ curve and tabulated in Table 1. It is well known that oxide materials need high temperature for their processing; at temperature above 1000°C, the oxygen present in the compound is expected to escape from the sample lattice and create oxygen vacancies in the lattice. During the cooling process, oxygen again enters in the lattice but these oxygen ions cannot totally compensate the loss of oxygen. This is the case with titanates and other layered structure compounds including present compounds [13, 14]. The high value of activation energy of the pure fresnoite compound and the decrease in of Ge-substituted compound can be explained on the basis of energy band gap of silicon (Si) and germanium (Ge). The energy band gap for Ge (0.67 eV) is smaller than energy band gap for Si (1.11 eV); hence, with the substitution of Ge on Si site the activation energy decreases and conductivity increases. This increase in conductivity can also be explained on the basis of dissociation bond energy of Si–O bond and Si–Ge bond. When the Ge-ion is substituted in Si-site, the Si–O bond of high bond energy 452 kJ/mol breaks and makes a new bond Si–Ge of low bond energy 297 kJ/mol hence bond strength reduce and increases the conductivity of substituted compound. The detailed description of the high activation energy value of the pure fresnoite compound has been given on the basis of energy band model in our earlier paper [15]. Although there is a difference in conductivity of both samples, their small but finite conductivities have been taken into account to explain the ferroelectricity in the samples.

Figure 2: versus 1000/ curves of Ba₂TiOSi2−xGexO₇ ( & 0.2).

Figure 3 shows the variation of dielectric constant () as a function of frequencies (100 Hz to 2 MHz) at RT. From the figure, it is clear that dielectric constant decreases with the increase of frequency. At lower frequencies, the dielectric constant decreases rapidly but it remains almost constant (relaxation behavior) or frequency independent at higher frequencies. This variation of dielectric constant and dissipation factor at lower frequencies is attributed not to the electronic and ionic contribution of polarization, but to the space charge contribution. While with the increase of frequency, the ionic and electronic contribution become dominant and space charge contribution diminishes gradually and hence dielectric constant decreases with the increase of frequency.

Figure 3: Dielectric constant versus curves of Ba₂TiOSi2−xGexO₇ ( & 0.2) at room temperature.

The temperature variation of dielectric constant of Ba₂TiOSi2−xGexO₇ ( and 0.2) at a frequency of 100 kHz is shown in Figure 4. From the figure it is observed that dielectric constant of pure compound is almost temperature independent up to 600 K and then increases up to the measured temperature range. When the Ge⁴⁺ ions are substituted on Si⁴⁺ ions site, dielectric constant increases rapidly and continuously after a temperature of 400 K. The plot reveals that at lower temperature the magnitude of dielectric constant of the compound is lower than the dielectric constant of pure () compound. But, at higher temperature the dielectric constant increases with respect to the dielectric constant of the compound. This increase in dielectric constant for substituted compound implies that this substitution produces more and more dipole moments in the lattice at higher temperature and hence increases the dielectric constant. But, no dielectric anomaly occurs up to the measured temperature range in both the compounds. Figure 5 shows the variation of dissipation factor () of both the compounds as a function of temperature at a frequency of 100 kHz. The dissipation factor shows almost similar behavior as the dielectric constant. The decrease in magnitude of dissipation factor for the compound at higher temperature supports the nature of dielectric constant as shown in Figure 4. Not only this, but no dielectric anomalies have also been observed in any case up to the measured temperature range.

Figure 4: Dielectric constant versus temperature curves of Ba₂TiOSi2−xGexO₇ ( & 0.2) at 100 kHz.

Figure 5: Dissipation factor versus temperature curves of Ba₂TiOSi2−xGexO₇ ( & 0.2) at 100 kHz.

4. Conclusion

Analyzing the X-ray results, it is concluded that the Rietveld refinement with a structural model of Pseudo-Voigt function using noncentrosymmetric space group P4bm confirmed the tetragonal structure of both the compounds. The dependence of dielectric constant and dielectric loss on temperature could be discussed with the effect of Ge⁴⁺ concentration on both conductivity and dielectric behaviour. The high resistivity and moderate dielectric constant of both the samples tends to ferroelectricity and responsible for good dielectric and ferroelectric behavior useful for different practical devices. Because of low dielectric constant, both the materials are useful for low frequency resonator.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

References

J. T. Alfors, M. C. Stinson, R. A. Matthews, and A. Pabst, “Seven new barium minerals from eastern Fresno County, California,” The American Mineralogist, vol. 50, pp. 314–340, 1965.

P. B. Moore and S. J. Louisnathan, “The crystal structure of fresnoite, Ba₂(TiO)Si₂O₇,” Zeitschrift für Kristallographie, vol. 130, no. 1–6, pp. 438–448, 1969.

A. Halliyal, A. S. Bhalla, S. A. Markgraf, L. E. Cross, and R. E. Newnham, “Unusual pyroelectric and piezoelectric properties of fresnoite (Ba₂TiSi₂O₈) single crystal and polar glass-ceramics,” Ferroelectrics, vol. 62, pp. 27–38, 1985.

M. Kimura, Y. Fujino, and T. Kawamura, “New piezoelectric crystal: synthetic fresnoite (Ba₂Si₂TiO₈),” Applied Physics Letters, vol. 29, no. 4, p. 227, 1976.

M. Kimura, “Elastic and piezoelectric properties of Ba₂Si₂TiO₈,” Journal of Applied Physics, vol. 48, p. 2850, 1977.

S. Haussühl, J. Eckstein, K. Recker, and F. Wallrafen, “Growth and physical properties of fresnoite Ba₂TiSi₂O₈,” Journal of Crystal Growth, vol. 40, no. 2, pp. 200–204, 1977.

S. A. Markgraf, A. Halliyal, A. S. Bhalla, R. E. Newnham, and C. T. Prewitt, “X-ray structure refinement and pyroelectric investigation of fresnoite, Ba₂TiSi₂O₈,” Ferroelectrics, vol. 62, no. 1, p. 17, 1985.

M. C. Foster, D. J. Arbogast, R. M. Nielson, P. Photinos, and S. C. Abrahams, “Fresnoite: a new ferroelectric mineral,” Journal of Applied Physics, vol. 85, no. 4, pp. 2299–2303, 1999.

T. Hoche, M. Grodzicki, F. Heyroth, and P. A. van Aken, “Convergence of the Møller-Plesset perturbation series for the fcc lattices of neon and argon,” Physical Review B, vol. 82, no. 20, Article ID 205111, 2005.

Y. Takahashi, M. Osada, H. Masai, and T. Fujiwara, “Softer region at boundary of supercooled liquid-crystal in glassy fresnoite,” Applied Physics Letters, vol. 94, Article ID 241909, 2009.

B. Rangarajan, T. Shrout, and M. Lanagan, “Crystallization kinetics and dielectric properties of fresnoite BaO-TiO₂-SiO₂ glass-ceramics,” Journal of the American Ceramic Society, vol. 92, no. 11, pp. 2642–2647, 2009.

S. K. Barbar and M. Roy, “Synthesis of Ba₂TiOSi₂O₇ and Ba₂TiOSi1.8Ge0.2O₇ ferroelectric ceramics and the structure determination by Rietveld analysis,” Ceramics International, vol. 37, no. 7, pp. 2695–2700, 2011.

R. E. Newnham, R. W. Wolfe, and J. F. Dorrian, “Structural basis of ferroelectricity in the bismuth titanate family,” Materials Research Bulletin, vol. 6, no. 10, pp. 1029–1039, 1971.

P. S. Rama Sastry, G. S. Kumar, T. Bhimashankaram, and G. Prasad, “Pyroelectricity in calcium substituted sodium bismuth titanate layer structured ferroelectric ceramics,” Bulletin of Materials Science, vol. 22, pp. 59–64, 1999.

M. Roy, S. K. Barbar, P. Dave, S. Jangid, and I. Bala, “X-ray, scanning electron microscopy and electrical properties of synthetic fresnoite (Ba₂TiSi₂O₈) ceramics,” Applied Physics A, vol. 100, no. 4, pp. 1191–1196, 2010.