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Journal of Materials
Volume 2013 (2013), Article ID 726314, 5 pages
Research Article

Preparation of Ultrahigh Potential Gradient of ZnO Varistors by Rare-Earth Doping and Low-Temperature Sintering

1Department of Mathematics and Physics, Shanghai Dianji University, Shanghai 201306, China
2World Premier International Research Center for Materials Nanoarchitectonics, National Institute for Materials Science, Ibaraki 305-0044, Japan
3State Key Laboratory of Precision Spectroscopy, East China Normal University, Shanghai 200241, China

Received 9 December 2012; Accepted 4 January 2013

Academic Editor: Pawan K. Kahol

Copyright © 2013 Lei Ke 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.


The effects of rare-earth doping and low-temperature sintering on electrical properties of ZnO varistors were investigated. The potential gradient of the ZnO varistors increased significantly to 2247.2 V/mm after doping 0.08 mol% of Y2O3 and sintering at 800°C for 2 h. The notable decrease of the grain size with the given experimental conditions was the origin for the increase in . During the process of high-temperature sintering, both the oxygen at the grain boundary interface and the neutralisation of the ions on the depletion layer were directly reduced, which caused the weight loss and the internal derangement of double Schottky barriers.

1. Introduction

ZnO-based varistors are ceramic resistor devices, which have been widely used in voltage stabilization, transient surge protection in electronic circuits and electrical power systems. They exhibit excellent nonlinear current-voltage (I-V) characteristics described by the relation , where is the electrical current density, is the potential gradient, is the nonlinear coefficient, and is a constant that depends on the microstructure [1, 2].

Numerous researchers have studied the effects of processing and microstructure on electrical conduction in ZnO varistors [35]. The nonlinear current-voltage characteristic results from the formation of double Schottky type electrostatic barriers at the grain boundaries with characteristic voltage drops of 2-3 V per grain boundary [6]. The increase in conductivity has been attributed to the mechanism of depletion layer breakdown or electron tunneling, which is due to the lowering of the electrostatic barriers [7].

Most previous work on fabrication of ZnO varistors has based on traditional raw materials, which contain zinc oxide mixed with small amounts of other oxides. The samples are sintered at a high temperature about 1200°C [8, 9]. For the fabrication of high potential gradient varistors, one main method is to decrease the grain size [10]. However, the elevated temperature sintering process accelerates the growth of grain size. In order to reduce grain growth and maintain the high-field properties, rare-earth doping and low-temperature sintering are adopted. A lower temperature reduces the cost and is easier to be realized. The objective of this paper is to investigate the electrical properties of samples produced by this process, especially the potential gradient.

2. Experimental

Reagent-grade raw materials were used in proportions of mol%    mol%   mol%   mol%   mol%   mol%   mol%   with equal to 0 or 0.08. Instead of grinding for more hours with a conventional ball milling, raw materials were mixed by high-energy ball milling with stainless steel balls and ethanol in a nylon bottle for 5 h at 500 rpm. The mixture was dried at 120°C for 2 h and pulverized using an agate mortar/pestle. The powder samples were mixed with few drops of a binder addition of 2 wt% polyvinyl alcohol (PVA) and uniaxially pressed into discs of 10 mm in diameter and 1 mm in thickness under 150 Mpa pressure. The green pellets were, respectively, sintered at 800°C and 1200°C for 2 h. The densities of the pellets were measured by Archimedes method. Silver paste was coated on both faces of the pellets and the ohmic contact of electrodes was formed by heating at 600°C for 15 minutes. All samples were divided into four groups for investigation, as shown in Table 1.

Table 1: Relative density of samples with different doping concentrations and sintering temperatures.

The crystalline phases were identified by an X-ray diffractometry (XRD, D/max 2550V) using a CuKα radiation. The surface microstructure was examined by a scanning electron microscope (SEM, JSM-5610LV). The average grain size was determined by the measurement on the micrographs with the linear intercept method using the following expression [11, 12]: where is the random line length on the micrograph, is the magnification of the micrograph, and is the number of the grain boundaries intercepted by lines. The electrical properties of varistors were measured using a DC parameter instrument (CJ1001). The breakdown voltage () was measured at the current density of 1.0 mA/cm2 and the potential gradient () was obtained by , where is the thickness of sample. The leakage current () was measured at the electrical field of 0.75  and the nonlinear coefficient () was determined in the range of 1.0 mA/cm2 to 10 mA/cm2 in current density, according to the expression of . It also contained a built-in 1400 kV DC power supply so as to describe the I-V property.

3. Discussion of Results

Figure 1 shows the phase composition of four samples. It is observed that ZnO is the main phase and Zn7Sb2O12 is the secondary phase in all the systems. However, one can also observe the presence of bismuth-rich phase for Sample 3 and Sample 4, and Y2O3 phase for Sample 4 only. This indicates that the additive Y2O3 after sintering at 1200°C is forming a solid solution with ZnO according to the following equation: As indicated in (2), the formation of solid solution in the ZnO lattices should increase the zinc vacancy concentration. These defects restrain the diffusion of electron through the lattices, decreasing of the ceramic in a certain extent. The disappearance of bismuth-rich phase indicates that the Bi2O3 phase is bounded into other phases or volatilized badly at the sintering temperature of 1200°C, which is unfavorable to the nonlinearity. The decrease of relative density results also from the volatilization of Bi2O3 (see Table 1).

Figure 1: XRD data of the four samples.

Microstructural observations show a significant influence of Y2O3 doping and sintering temperatures on the morphology of the ZnO grains and the distribution of the grain size. The ZnO grain size has an obvious decrease from 1.602 μm to 1.145 μm with Y2O3 doping (see Figures 2(c) and 2(d)) and from 3.377 μm to 1.145 μm with low-temperature sintering (see Figures 2(b) and 2(d)). Comparing with the conventional ZnO varistors [2, 8], the grain size of Sample 4 has been reduced by at least 50%. The temperature at which the liquid phase occurs is about 740°C. Much higher above this temperature, such as 1200°C, exaggerated grain growth occurs. Exaggerated grain growth results in a bimodal grain size distribution, with the small grains among the huge ones. Due to the exaggerated grain growth and the volatilization of Bi2O3, Y2O3 doping nearly makes no difference on the microstructure of ZnO varistors during the high sinter temperature (see Figures 2(a) and 2(b)). The micrographs in Figure 2 also witness that the obtained Sample 4 is nanograined and contains the very developed free surfaces as well as grain boundaries. It has been demonstrated recently that the physical properties of nanograined ZnO, especially doped one, strongly depend on the presence of defects like grain boundaries and on the presence of amorphous surficial and intergranular layers [13, 14]. The crystalline ZnO grains of Sample 4 do not directly contact each other and are completely surrounded by a thin layer of material such as amorphous intergranular phase. It forms a kind of continuous foam-like network, where the amorphous intergranular phase amount could be increased by the decrease in grain size.

Figure 2: SEM images for (a) Sample 1, (b) Sample 2, (c) Sample 3, and (d) Sample 4.

The electrical characterization of these samples normalized in potential gradient (V/mm) as a function of current density (μA/mm2) is shown in Figure 3. The values of , , and are presented in Table 2. Comparing with the other three samples, Sample 4 has the highest (2247.2 V/mm) and (23.0). The value of most of the existing commercial ZnO varistors is below 2000 V/mm [3]. The potential gradient of Sample 4 has been increased at least 12%. Increasing the sintering temperature causes the grains to grow, and the electrical active grain boundaries decrease with the volatilization of Bi2O3. A sharp rise in , after sintering at 1200°C, is attributed to the lowering of the grain boundary barrier height with the disappear of bismuth-rich phase.

Table 2: , , and for the four samples.
Figure 3: Partial I-V characteristics for the four samples.

Some early researches about ZnO-based varistors report that the best nonlinear behavior is achieved between 1200°C and 1300°C. However, in the specific case of our varistors, the change in with the sintering temperature, as shown in Figure 4, is related to the microstructural modifications associated with the reactions that occur during the liquid phase sintering. Higher sintering temperature makes the reactions more adequately, except the largely evaporation process of Bi2O3. In the present varistor systems where no bismuth-rich phase is observed in Sample 1 and Sample 2, this dependence would be related to the high-energy ball milling in the early period of experiment and the pinning effect of Y2O3 during the sintering process. High-energy ball milling induces the grain refinement, and the deliquescent Y2O3 particles between ZnO grains restrain the grain growth. Both of these realize the wetting of smaller grains at a relative lower temperature.

Figure 4: Evolution of the nonlinear coefficient as a function of sintering temperature.

On the other hand, the ionic radius of (0.89) is larger than the ionic radius of (0.74 ). It is difficult for ions to solid dissolve into the grains at a lower temperature (800°C). ions dissolve at the grain boundaries and exist in the forms of Y2O3 and/or other two crystal phases of Bi3YO6 and Bi19YO3 [15]. The equilibrium reactions occurred at the grain boundaries can be written (not observed in our experiment) as

The dissolved ions have no effect on the lattice structure of ZnO. They form small particles at the edge of the grains and as a result pin the grains to restrict their growth. The decrease of the grain size directly induces the increase in the amount of grain boundaries, subsequently in and . At a higher temperature (1200°C), with the volatilization of Bi2O3, the above-mentioned reaction processes do not occur, however, being substituted by the solid solution reaction according to (2). High sinter temperature makes the solid solution reaction occur easily. ions act as acceptor ions, which make the resistance of grains rise, with the given experimental conditions of high-energy ball milling and low-temperature sintering. Additional vacancies () are created with ions solid dissolved into the ZnO grains. The volatilization of Bi2O3 causes the resistance of grain boundaries to decrease. The reduction of differences in resistance between the grain boundaries and the grains accelerates the degeneration in nonlinear of the varistors (see Table 2).

With (2) proceed during the sintering process, more and oxygen appear. The oxygen migrates away along the grain boundaries, which causes a significant rightward progress of (2). The shortage of oxygen makes the reaction occur during the cooling process as follows: where Oad is the adsorbed oxygen at the grain boundaries.

According to the model proposed by Gupta and Carlson [16], , , , and are the primary defects on the depletion layer. The donor levels of and are at 0.5 and 2 eV below the conduction band edge of ZnO, it is too large for to enter into the lattices of varistors to form . Instead, a charge transfer occurs between the positively charged oxygen vacancy and the negatively charged adsorbed oxygen at the interface:

The reactions described above only contain the doubly charged ions, and a similar analogy can be written for the singly charged ions as well. With the loss of oxygen, the neutralisation of the ions on the depletion layer reduces the barrier height of double Schottky barrier and finally decreases the potential gradient of the varistors.

4. Conclusions

The ZnO varistors with ultrahigh potential gradient are prepared by rare-earth doping and low-temperature sintering. The origin for this is the great decrease of grain size. The experimental results indicate that the deliquescent Y2O3 particles between ZnO grains during the low-temperature sintering process restrain the grain growth and promote the electrical nonlinear. At a higher temperature, the decrease of potential gradient can be explained by the solid solution of ions and the volatilization of Bi2O3. The adsorbed ions at the grain boundaries induce the neutralisation of ions on the depletion layer and cause the barrier lowering, which also have an effect on the electrical properties of the varistors.


The authors gratefully acknowledge the financial support of the National Natural Science Foundation of China (Grants no. 50471045 and no. 10804071), Shanghai Municipal Education Commission Project (Grants no. 12AZ16 and no. 12YZ185), and Shanghai Dianji University Project (Grants no. 11C409).


  1. M. A. Ashrafa, A. H. Bhuiyanb, M. A. Hakimc et al., “Microstructure and electrical properties of Ho2O3 doped Bi2O3-based ZnO varistor ceramics,” Physica B, vol. 405, no. 17, pp. 3770–3774, 2010. View at Publisher · View at Google Scholar
  2. T. K. Gupta, “Application of zinc oxide varistors,” Journal of the American Ceramic Society, vol. 73, no. 7, pp. 1817–1840, 1990. View at Google Scholar · View at Scopus
  3. S. Shichimiya, M. Yamaguchi, N. Furuse, M. Kobayashi, and S. Ishibe, “Development of advanced arresters for GIS with new zinc-oxide elements,” IEEE Transactions on Power Delivery, vol. 13, no. 2, pp. 465–471, 1998. View at Google Scholar · View at Scopus
  4. M. M. Shahrakia, S. A. Shojaeec, M. A. F. Sania et al., “Two-step sintering of ZnO varistors,” Solid State Ionics, vol. 190, no. 1, pp. 99–105, 2011. View at Publisher · View at Google Scholar
  5. E. Savarya, S. Marinela, F. Gascoina et al., “Peculiar effects of microwave sintering on ZnO based varistors properties,” Journal of Alloys and Compounds, vol. 509, no. 21, pp. 6163–6169, 2011. View at Publisher · View at Google Scholar
  6. G. D. Mahan, L. M. Levinson, and H. R. Philipp, “Theory of conduction in ZnO varistors,” Journal of Applied Physics, vol. 50, no. 4, pp. 2799–2812, 1979. View at Publisher · View at Google Scholar · View at Scopus
  7. K. Eda, “Conduction mechanism of non-Ohmic zinc oxide ceramics,” Journal of Applied Physics, vol. 49, no. 5, pp. 2964–2972, 1978. View at Publisher · View at Google Scholar · View at Scopus
  8. M. Peiteado, J. F. Fernández, and A. C. Caballero, “Processing strategies to control grain growth in ZnO based varistors,” Journal of the European Ceramic Society, vol. 25, no. 12, pp. 2999–3003, 2005. View at Publisher · View at Google Scholar · View at Scopus
  9. S. T. Kuo and W. H. Tuan, “Grain growth behaviour of ZnO-based multilayer varistors,” Journal of the European Ceramic Society, vol. 30, no. 2, pp. 525–530, 2010. View at Publisher · View at Google Scholar
  10. J. He, J. Liu, J. Hu, R. Zeng, and W. Long, “Non-uniform ageing behavior of individual grain boundaries in ZnO varistor ceramics,” Journal of the European Ceramic Society, vol. 31, no. 8, pp. 1451–1456, 2011. View at Publisher · View at Google Scholar · View at Scopus
  11. American Society for Metals, Metals Handbook, Volume 8: Metallography, Structures and Phase Diagrams, American Society for Metals, Warrendale, Pa, USA, 8th edition, 1973.
  12. H. O. Toplan and Y. Karakas, “Grain growth in TiO2-added ZnO-Bi2O3-CoO-MnO ceramics prepared by chemical processing,” Ceramics International, vol. 28, no. 8, pp. 911–915, 2002. View at Publisher · View at Google Scholar · View at Scopus
  13. B. B. Straumal, A. A. Mazilkin, S. G. Protasova et al., “Amorphous grain boundary layers in the ferromagnetic nanograined ZnO films,” Thin Solid Films, vol. 520, pp. 1192–1194, 2011. View at Publisher · View at Google Scholar
  14. B. B. Straumal, S. G. Protasova, A. A. Mazilkin et al., “Amorphous interlayers between crystalline grains in ferromagnetic ZnO films,” Materials Letters, vol. 71, pp. 21–24, 2012. View at Publisher · View at Google Scholar
  15. Y. Shimizu, F. C. Lin, Y. Takao, and M. Egashira, “Zinc oxide varistor gas sensors: II, effect of chromium(III) oxide and yttrium oxide additives on the hydrogen-sensing properties,” Journal of the American Ceramic Society, vol. 81, no. 6, pp. 1633–1643, 1998. View at Google Scholar · View at Scopus
  16. T. K. Gupta and W. G. Carlson, “A grain-boundary defect model for instability/stability of a ZnO varistor,” Journal of Materials Science, vol. 20, no. 10, pp. 3487–3500, 1985. View at Publisher · View at Google Scholar · View at Scopus