Open access peer-reviewed chapter

Breakdown Characteristics of Varistor Ceramics

By Jianying Li, Kangning Wu and Yuwei Huang

Submitted: March 16th 2018Reviewed: June 22nd 2018Published: November 5th 2018

DOI: 10.5772/intechopen.79720

Downloaded: 634


Breakdown characteristics are of great importance for varistor ceramics, which largely depend on Schottky barriers at grain boundaries. In order to enhance breakdown performance for meeting the requirement of device miniaturization, different doping methods are introduced to not only restrict grain size from additional phase but also manipulate defect structure of Schottky barrier at grain boundaries from substitution. Distribution of barriers is another key point affecting breakdown characteristics in varistor ceramics. Dimensional effect, which is detected in not only ZnO ceramics but also CaCu3Ti4O12 ceramics, is practically and theoretically found to be closely correlated with uniformity of grains. As a result, breakdown characteristics of varistors are dominated by combination effect of single barrier performance and spatial barrier distribution. In this chapter, enhanced breakdown field in CaxSr1−xCu3Ti4O12 ceramics, in situ synthesized CaCu3Ti4O12-CuAl2O4 ceramics, and CaCu3Ti4O12-Y2/3Cu3Ti4O12 composite ceramics are investigated from the aspect of Schottky barriers at grain boundaries. In addition, dimensional effect is found in both ZnO and CaCu3Ti4O12 ceramics, which are investigated from grain size distribution through theoretical and experimental analysis.


  • breakdown characteristics
  • varistor ceramics
  • Schottky barrier
  • CaCu3Ti4O12 ceramics
  • ZnO ceramics

1. Introduction

Varistor ceramics exhibit excellent nonlinear current-voltage (I-V) characteristics that they are widely employed for overvoltage protection in power system and electronic circuits. Zinc oxide (ZnO) varistor ceramics is one typical varistor ceramics, which has been for decades widely employed in arrestors [1]. The breakdown field of commercial ZnO varistor ceramics is commonly 200–300 V/mm and the nonlinear coefficient is ∼50. Besides, perovskite CaCu3Ti4O12 (CCTO) ceramics exhibit giant permittivity and nonlinear characteristics that made them potential candidates for application in surge absorption [2, 3]. Varistor ceramics consist of grains and grain boundaries, and it is grain boundary which manipulates the breakdown field. Breakdown field is commonly suggested to be dominated by single grain boundary and the amount of grain boundaries along electric field direction. The single grain boundary electrical performance is determined by Schottky barriers which are primarily comprised of positively charged depletion layers and negatively charged interface states [4]. Meanwhile, the amount of grain boundaries is decided by grain size. With the progress of device miniaturization, the demand for varistor ceramics with high breakdown field and high-energy absorption capability needs to be fulfilled. In order to enhance breakdown characteristics, microstructure of varistor ceramics should be improved which can be summarized into decreasing grain sizes on one hand and enhancing single barrier performance on the other hand. Two major ways of achieving greater breakdown characteristics are (1) improving preparation method and (2) finding a better recipe which might contain additives [5, 6, 7, 8, 9, 10]. For improved preparation process, lots of methods like nano-sized particles and spark plasma sintering (SPS) techniques are induced to reduce the grain sizes [11, 12]. Doping is another typical topic in enhancing breakdown performance in varistor ceramics. As is known in ZnO varistor ceramics, nonlinear properties do not exist until Bi2O3 is added which forms an intergranular layer and manipulates defect structure to form better Schottky barriers at grain boundaries. Later on, Sb2O3, Co2O3, Mn2O3, etc. are added to further enhance breakdown field and improve nonlinear performance. As for CCTO varistor ceramics, several doping methods were introduced which have different effects on microstructure. Firstly, the doping ions are able to substitute ions in CCTO lattice (Ca2+, Cu2+) and form a relatively homogeneous structure [5]. This method dominantly manipulates Schottky barrier structure at grain boundaries. Secondly, another phase is formed besides CCTO phase resulting in heterogeneous structure, like SrTiO3, TiO2, CuAl2O4, etc. [6, 7, 8]. The additional phases mainly restrict the growth of grains and control the grain size to produce more grain boundaries. Thirdly, to form another CCTO-like phase with CCTO phase, like Y2/3Cu3Ti4O12 [9], is also suggested. This method not only introduces heterogeneous structure which restricts grain growth but also induces more defects at grain boundaries to enhance Schottky barriers. In summary, these three methods of doping result in diverse improvement of electrical characteristics due to various effects on microstructure of varistor ceramics. In the main text, these three kinds of doping methods are, respectively, introduced in detail.

Besides methods of enhancing breakdown characteristics, a non-negligible phenomenon that electrical performance is not uniform in the bulk of the ceramics should be taken into consideration for design and practical application. The inhomogeneous electrical properties at the cross section have been widely reported. About 5–11% of cross-section region in varistor ceramics was found to exhibit lower breakdown voltage than the rest of the regions [13]. This further results in current localization, which causes electrical puncture, thermal cracking, or even thermal runaway [14]. In addition, dimensional effect, which exhibits as the thickness dependence of breakdown field, is found in not only ZnO ceramics but also CCTO ceramics [15, 16, 17]. It is found that breakdown field and nonlinear coefficient are significantly decreased below a critical thickness, which brings much trouble in designing. The spatial electrical nonuniformity was widely attributed to inhomogeneous grain size distribution and grain boundary characteristics. Electrical measurements using microcontact on single grain boundary suggested that 50% grain boundaries can be defined as “good,” 30% are “bad,” and the rest are ineffective [18]. At the same time, reports from luminescence created by electrical breakdown also provide support for uneven grain boundaries [19]. In this work, the structural origin of dimensional effect in varistor ceramics is investigated through experiment and simulation, which suggested that wide grain size distribution should be responsible. After careful processing of controlling grain sizes into narrower distribution, dimensional effect is diminished, which, to some extent, proves the responsibility of grain size distribution.


2. Enhancement of electrical breakdown field in varistor ceramics

2.1. Enhanced breakdown field in Ca1−xSrxCu3Ti4O12 ceramics via tailoring donor density

2.1.1. Phase composition and surface morphology

X-ray diffraction (XRD) patterns of Ca1−xSrxCu3Ti4O12 ceramics are presented in Figure 1. Main perovskite phase of CCTO is detected with small amount of impurity phase of CuO and SrTiO3 in Figure 1(a). In the enlarged view of (220) peak in Figure 1(b), the peak gradually moves to a lower angle with the increase of Sr/Ca ratio, indicating increased lattice constant as a result of Ca2+ (0.99 Å) with smaller radius being substituted by Sr2+ (1.26 Å).

Figure 1.

XRD patterns of Ca1−xSrxCu3Ti4O12 varistor ceramics.

SEM images and corresponding grain size distribution are shown in Figure 2. Grain size of the samples is smaller than that in CCTO ceramics (>8 μm), while it changes little on the ratio of Sr/Ca (2.4–2.8 μm). Energy dispersive X-ray spectroscopy (EDS) is further measured at the marked regions in Figure 2 with the results listed in Table 1. No pure CaCu3Ti4O12 or SrCu3Ti4O12 is detected, indicating solid solution systems. Major discrepancy for those large grains (A1, B2, C2, D1) and small grains (A2, B3, C3, D2) is found to be Sr/Ca ratio. The higher Sr/Ca ratio in larger grains indicates Sr2+ might have benefit for grain growth in relatively low temperatures.

Figure 2.

Backscattering SEM pictures of Ca1−xSrxCu3Ti4O12 ceramic samples. (a) Sr0.2-Ca0.8, (b) Sr0.4-Ca0.6, (c) Sr0.6-Ca0.4 and (d) Sr0.8-Ca0.2. (usage permitted by Elsevier).

Atom (%)Sr0.2-Ca0.8Sr0.4-Ca0.6Sr0.6-Ca0.4Sr0.8-Ca0.2
O K66.6870.3162.3168.9972.7559.2065.9363.4567.6773.60
Ti K17.1415.490.8616.2014.226.7017.1118.6516.6613.73
Cu K11.9410.6436.8210.749.4432.8712.7013.8011.519.50
Sr L0.850.281.691.140.883.333.153.262.40
Ca K3.393.270.710.463.543.313.663.08

Table 1.

EDS results for marked points in Figure 2 (usage permitted by Elsevier).

2.1.2. Enhanced breakdown field and complex impedance spectra

Figure 3 is current density-electric field (J-E) curves of Ca1−xSrxCu3Ti4O12 ceramics. The breakdown field E1mA and nonlinear coefficient αare calculated:


where U1mA and U0.1mA are the voltage under current density of 1 and 0.1 mA/cm2, respectively, and dis the sample thickness. The corresponding αand E1mA are listed in Table 2. Enhanced E1mA are observed in Ca1−xSrxCu3Ti4O12 especially for samples with Sr/Ca ratio of 0.4/0.6. It increased remarkably to 24.52 kV/cm, which is as twice as that of CCTO. Elevated E1mA can be partially ascribed to decreased grain size. However, greatly varied E1mA are found in samples with similar grain size of ∼2.5 μm in Figure 2, indicating grain size is not decisive. Series connected RCunits are widely employed for characterizing properties of grains and grain boundaries based on the fact that CCTO ceramics consist semiconducting grains and insulating grain boundaries [2, 20]. The complex impedance Z* can be expressed as:


where Rgb and Cgb are resistance and capacitance of grain boundaries while Rg and Cg are resistance and capacitance of grains. Rg and Rgb can be thus obtained as intercepts in complex impedance spectra in Figure 4. In addition, resistance activation energies of grain (Eg) and grain boundary (Egb) are calculated via the Arrhenius equation. As shown in Table 2, Rg and Eg remain constant to ∼225 Ω and ∼0.13 eV, while Rgb and Egb vary significantly. Highest Rgb and Egb of 9900 MΩ and 1.03 eV are obtained for samples with Sr/Ca ratio of 0.4/4.6, which is in accordance with breakdown field in Figure 3(a). Consequently, it is reasonable to deduce that modified grain boundary characteristics that are crucial for the improved breakdown field.

Figure 3.

Current-voltage (J-E) characteristics (a) and impedance spectra (b) of Ca1−xSrxCu3Ti4O12 ceramics at room temperature.

E1mA (kV/cm)15.8824.527.286.15
Rg (Ω)221221234233
Rgb (MΩ)640990027012
Eg (eV)
Egb (eV)

Table 2.

Parameters for electrical nonlinearity and inhomogeneity of grain and grain boundary of Ca1−xSrxCu3Ti4O12 varistor ceramics.

Figure 4.

C-Vcharacteristics of Ca1−xSrxCu3Ti4O12 varistor ceramics.

2.1.3. Tailoring of donor density

Back-to-back Schottky barrier at grain boundary is crucial for the nonlinearity of varistors. Generally, the barrier height ϕ0 depends on the depletion layer width xd, interface state density Ns, and donor concentration Nd:


For single grain boundary, the grain boundary capacitance of unit area C0 under zero biased voltage is C0 = [rNd/(8ϕ0)]1/2, while the capacitance Cunder a bias voltage Uis as follows [21]:


Dependence of (C−1 − 1/2C0−1) on Uis plotted in Figure 4, showing good nonlinearity. Barrier parameter is calculated and listed in Table 3. Nd for all the samples is almost constant, while Ns varies remarkably from 3.3 × 1013 cm−3 for Sr0.4-Ca0.6 to 15.6 × 1013 cm−3 for Sr0.8-Ca0.2. Consequently, the highest barrier height is obtained in Sr0.4-Ca0.6 and lowest in Sr0.8-Ca0.2, which matches the results of Egb from impedance spectra.

ϕ0 (eV)
xd (nm)630880460240
Ns (109 cm−2)7.735.909.207.53
Nd (1013 cm−3)6.113.349.9915.67

Table 3.

Parameters of Schottky barrier of Ca1−xSrxCu3Ti4O12 varistor ceramics (usage permitted by Elsevier).

Oxygen vacancy is considered as origin of electron formation due to weak cation▬O bonds. Space of Asite in CCTO is rather rigid as the observed Ca▬O distance is 2.61 Å, while the expected value is 2.72 Å [22]. Radius of Sr is much larger than that of Ca so that Sr▬O bonds are extremely over bonded. In increasing the ratio of Sr/Ca, larger Sr stretches the Ti▬O bonds, leading to enhanced polarizability of the tilted TiO6 octahedra and possible breaking of the balance of Cu▬O plane. Therefore, oxygen vacancy is much easier to be produced as well as segregated Cu-rich secondary phase, shown in Figure 1 [23].

On the contrary, oxygen vacancy may be inhibited due to solid solution effect between SCTO and CCTO. Taking Sr2+ in CCTO as an example, besides SrCa, Sr exists as SrCu and Sri∙∙ as Cu2+ is easily loss in CCTO. Sr-Cu distortion is likely formed due to the same valence of Sr, Ca, and Cu ions. Increased Asite ions can coordinate with the O2− in TiO6 octahedron. Moreover, Sri∙∙ can compensate the electrons generated by oxygen vacancies. As a result, declined donor density is thus formed, which can result from Ca in SCTO as well. Maximum integrated action of strong solid solution effect and weak Sr stretching effect is achieved when Sr/Ca ratio is 40/60, which leads to greatly elevated potential barrier height more than 1.0 eV and enhanced breakdown field consequently.

2.2. In situ synthesized CCTO-xCuAl2O4 varistor ceramics

2.2.1. Preparation and characterization of in situ synthesized CCTO-xCuAl2O4 samples

CCTO powders are prepared via traditional solid-state reaction method and suspended in Al(NO3)3 aqueous solution. Subsequently, the suspension was quantitatively titrated with NH4OH to make Al(OH)3 precipitate on the surface of CCTO particles. After drying, the powders are calcined at 950°C for 4 h to dehydrate Al(OH)3 into Al2O3. Finally, they were pressed into pellets and sintered in air at 1100°C for 4 h.

XRD patterns are presented in Figure 5(a). Only single phase of CCTO can be detected when x = 0. With increased precipitation of Al3+, another spinel phase CuAl2O4 is found. Backscattering SEM picture of CCTO-0.4CuAl2O4 sample is further taken as shown in Figure 5(b), in which three typical regions, A, B, and C, can be observed. According to EDS results presented in Table 4, element distribution of the gray grains (A, 15–20 μm in size) is similar to CCTO with a little Al. The black grains (B1, B2, and B3, 1–4 μm in size) are found to be the secondary phase, while the bright region of C is Cu-rich intergranular phase. It is proposed that Cu2O and CuO are easily precipitated over 1000°C as Cu-rich phase, which is the main source for CuAl2O4. The involved chemical reactions can be expressed as:


Figure 5.

XRD patterns (a) and SEM picture (b) of in situ synthesized CCTO-xCuAl2O4 ceramics (usage permitted by IOP Publishing).

Atom (%)AB1B2B3C
O K41.9739.644.6450.3737.81
Al K1.4241.5528.3819.700.79
Ca K6.560.612.263.121.10
Ti K28.812.609.3512.445.17
Cu K21.2515.6315.3714.3755.13

Table 4.

EDS results of in situ synthesized CCTO-0.4CuAl2O4 sample in Figure 5(b) (usage permitted by IOP Publishing).

Surface morphology of the samples is characterized by SEM as shown in Figure 6. For CCTO ceramics, little secondary phase is found, and the average grain size is 19.1 μm as shown in Figure 6(a). As to samples with x = 0.4 found in Figure 6(b), numbers of small particles appear in interior and intergranular region of CCTO grains, and the average grain size is 18.8 μm. When xincreases to 0.5 and 0.65, average grain sizes decrease notably to about 1.6 μm. It is proposed that reduction of grain size may arise from the depleted Cu-rich phases, which assists grain growth in forming CuAl2O4 according to Eq. (4). Pinning effect of CuAl2O4 phase could further inhibit the grain growth, which generally obeys the Zener model:


where Gis the limit size of the matrix grain and rand fare particle diameter and volume fraction of the secondary phase, respectively. The grain size of the secondary phase decreases, and the volume fraction of the secondary phase increases; the matrix grain size apparently declines. Therefore, the best pining effect is achieved in the sample with x = 0.5 for relatively small grain size and high volume fraction of the spinel phase.

Figure 6.

SEM images of CCTO-xCuAl2O4 ceramic samples: (a)x = 0, (b)x = 0.4, (c)x = 0.5, and (d)x = 0.65 (usage permitted by Elsevier).

2.2.2. Enhanced breakdown field in CCTO-xCuAl2O4 ceramic samples

J-Echaracteristics of in situ synthesized CCTO-xCuAl2O4 ceramics are plotted in Figure 7, and the corresponding E1mA and αare plotted in the inset. It is clear that E1mA of samples with x = 0.5 increased sharply to about 21 kV/cm with reduced grain size. On this basis, it is proposed that aggregation of CuAl2O4 and the inhibiting of grain growth should take responsibility for the greatly enhanced E1mA. Although E1mA = 4.3 kV/cm is found in x = 0.65 samples with similar grain size of ∼1.6 μm, it can be ascribed to abnormally large grains as presented in Figure 6(d).

Figure 7.

J-Echaracteristics of in situ synthesized (a) and directly induced (b) CCTO-xCuAl2O4 samples.

For comparison, CuAl2O4 is directly introduced into CCTO by solid-state reaction method following the same sintering condition. Dependence of αand E1mA on addition of the secondary phase is plotted in Figure 7(b). Similar to the in situ synthesized samples, the highest E1mA is achieved when x = 0.5. However, its highest E1mA is only about 15 kV/cm. This suggests that enhanced E1mA in directly induced samples mainly arise from pinning effect while additional depletion of Cu-rich phase should be also considered for in situ synthesized samples.

2.2.3. Complex impedance analysis for CCTO-xCuAl2O4 samples

Figure 8(a) is complex impedance spectra of CCTO-xCuAl2O4 samples at 393 K. Rgb increases greatly from 0.37 to 13.55 MΩ with increased Al. Based on the dominant effect of Rgb to the overall resistance, DC conductivity can approximate to conductivity of grain boundary. Activation energy of DC conductivity can be thus calculated via the Arrhenius equation, as shown in Figure 8(b). Highest energy of 0.81 eV is found for samples with x = 0.5, indicating inhibited hopping conduction process in them. Thus, it is suggested that the new formation of insulating phase CuAl2O4 may modify the electronic structure of grain boundaries and improve the electrical properties of CCTO ceramics. The enhanced Rgb can be attributed to higher activation energy required for hopping conduction at grain boundary.

Figure 8.

Impedance spectra (a) and temperature dependence of DC conductivity (b) of CCTO-xCuAl2O4.

2.3. CCTO-YCTO composite ceramics with enhanced nonlinearity

2.3.1. Phase composition and surface morphology

(1 − x)CaCu3T4O12-xY2/3Cu3T4O12 [(1 − x)CCTO-xYCTO] ceramics were prepared via solid-state reaction method. They were sintered in air at 1100°C for 10 h. XRD patterns are shown in Figure 9(a), in which the main phase of perovskite phase and small amount of CuO, TiO2, and Y2Ti2O7 are detected. With increased Y3+, (200) peak moves to lower angle. However, it is hard to identify CCTO with YCTO phase due to similar lattice structure. Therefore, EDS is conducted (Figure 9(b) and Table 5). Element distribution of the large gains (4–6 μm) is close to YCTO, while small grains (1–2 μm) are close to CCTO although solid solution is found.

Figure 9.

XRD patterns (a) and SEM picture (b) of 0.2CCTO-0.8YCTO ceramics (usage permitted by Elsevier).

Atom (%)A1A2A3B1B2
Y K4.004.64.560.890.85
Ca K0.870.610.944.904.76
Cu K9.088.297.989.1510.34
Ti K20.4919.4119.8920.7721.77
O K64.8666.0965.6264.2961.89

Table 5.

EDS results of 0.2CCTO-0.8YCTO sample in Figure 9(b) (usage permitted by Elsevier).

SEM pictures were taken, as shown in Figure 9. Large grains are formed in pure CCTO and YCTO ceramics with Cu-rich phase segregated in the intergranular region marked by red circles as shown in Figure 10(a) and (d). Discontinuous distribution of grain size is finally formed in CCTO samples. Stripy grains in pure YCTO ceramics suggest that sintering temperature is so high that grains could not hold the hexagonal shape. Meanwhile, two kinds of grains, with grain sizes of 4–6 μm and 1–2 μm, respectively, were found uniformly distributed in composite ceramics. Average grain size is reduced, which indicates that grain growth of CCTO and YCTO was suppressed by each other in the form of pinning effect.

Figure 10.

Surface morphology of (1 −x)CCTO-xYCTO ceramics: (a)x = 0, (b)x = 0.5, (c)x = 0.8, and (d)x = 1.0.

2.3.2. Enhanced electrical nonlinearity

J-Echaracteristics at room temperature are presented in Figure 11. E1mA of 0.5CCTO-0.5YCTO and 0.2CCTO-0.8YCTO are enhanced to 10.17 and 11.24 kV/cm, respectively, which are approximately 10 times of that 1.24 kV/cm of CCTO sample. αis improved to 9.57 and 9.88, respectively, as well. Although extremely high αis reported in some reports, they are hard to be repeated. αlargely depends on the current range used for calculation in Eq. (2) and the measuring method. As shown in Figure 11(b), some reports of high αare actually ∼5 in the current range 0.1–1 mA/cm in lnJ–lnEplots [24, 25, 26]. The reported high αmight also originate from positive feedback of heat generated from thermal emission process at grain boundary.

Figure 11.

J-Echaracteristics of (1 − x)CCTO-xYCTO ceramics (a) and some reported CCTO ceramics with high nonlinear coefficient (b).

Complex impendence spectroscopy at room temperature is plotted in Figure 12. Rg is close to 20–40 Ω, and Rgb varies significantly up to 1200 MΩ in samples with x = 0.8, while it is 55.5 MΩ in pure CCTO. To further explore the carriers’ migration across barrier, Eg and Egb are calculated in Table 6. Similar to other reports, Eg is constant while Egb differs significantly, inferring crucial role of grain boundary on carrier transport. Egb gradually increases with increased x, suggesting gradually developed Schottky barrier with the addition of YCTO. The barrier height of sample with x = 0.8 reaches a maximum of 1.50 eV, which is twice higher than 0.69 eV of CCTO. The high barrier height leads to high nonlinear coefficient, which is consistent with results of J-Eperformance shown in Figure 11(a).

Figure 12.

Complex impedance spectra of (1 − x)CCTO-xYCTO ceramics.

Eg (eV)
Egb (eV)0.691.111.50031

Table 6.

Activation energies of grain and grain boundary resistance of (1 − x)CCTO-xYCTO samples.

Grain boundary resistance dominates the conduction process. So the hopping conduction is deduced, inhibiting improved grain boundary resistance and activation energy in composite ceramics. This inhibition may arise from increased number of grain boundaries or enhanced blocking effect of single barrier. There are three types of grain boundaries: CCTO/YCTO, CCTO/CCTO, and YCTO/YCTO. Egb of 0.2CCTO-0.8YCTO samples (1.43 eV) is higher than that 1.11 eV of 0.5CCTO-0.5YCTO samples, indicating effect of grain boundary type is more important. Assuming both CCTO and YCTO grains are cubic, its surface area ratio can be simply written as:


where Ais surface area of grains, ris grain size, Vol is single grain volume, and Vol% is volume fraction. Densities of CCTO and YCTO are 5.05 and 5.20 g/cm3, respectively. The average grain sizes for CCTO and YCTO are 1.24 and 4.57 μm according to results found in Figure 10(b and c). On this basis, it can be obtained that ACCTO/AYCTO for 0.5CCTO-0.5YCTO is 0.38, while it is 0.95 for 0.2CCTO-0.8YCTO. In other words, the number of CCTO/YCTO interfaces reaches maximum in 0.2CCTO-0.8YCTO sample. On one hand, solid solution between Y3+ and Ca2+ could inhibit generation of donors, leading to thicker depletion layers. On the other hand, more interface states are produced at the YCTO/CCTO heterojunction. As a result, barrier height is improved so that more energy is needed for carriers to migrate across barriers.

3. Dimensional effect of varistor ceramics

3.1. Phenomenon of dimensional effect

Thickness dependence of E1mA and αof ZnO ceramics with low, medium, and high potential gradients is plotted in Figure 13(a). Similar phenomenon is also found in CCTO ceramics in Figure 13(b). Every curve exhibits a turning point corresponding to sample thickness d. Critical thickness dc, critical breakdown field Ec, and critical nonlinear coefficient αc are determined by each curve. Such behavior can be empirically represented as:


where the exponent brepresents the transitional behavior for the entire curve. Let this exponent in d < dc domain be denoted as b1 while it is denoted as b2 in the d > dc domain, i.e.:


Figure 13.

Thickness dependence ofE1mA andαof (a) ZnO ceramics and (b) CCTO ceramics.

The summary of the parameters b1, b2, dc, and Ec in Figure 13 is listed in Table 7. dc significantly decreases with increased E1mA and Ec, which indicate that those who exhibit higher E1mA exhibit less severe dimensional effect. At the same time, b2 slightly decreases with increased E1mA, suggesting more stable E1mA with variation of thickness. However, no matter what varistors are used in high-voltage or low-voltage situations, dimensional effect undoubtedly exists, which brings much trouble for practical application and design. Therefore, further investigation of dimensional effect is needed for stable electrical performance.

Samplesb1b2dc (mm)Ec (V/mm)
ZnO ceramicsHigh9.40.210.19185
CaCu3Ti4O12 ceramics0.2780.0870.9053

Table 7.

The exponents b1 and b2, critical thickness dc, and the transitional breakdown field Ec of ZnO ceramics and CCTO ceramics in Figure 12.

3.2. Simulation of dimensional effect

Breakdown voltage of single grain boundary is acknowledged to be nearly constant (∼3 V), indicating other factors should be responsible for dimensional effect. To understand the structural origin of dimensional effect, a model based on the network of grains and grain boundaries is proposed. Grain sizes in varistor ceramics fit the normal distribution, in which the probability density f(l) can be expressed as:


where lis the average grain size, σis the standard deviation, and μis the mathematical expectation. For ceramics with diameter of Dand thickness of d, it is assumed that all grains are cubic with length of m; the number of grains on the cross-section Nis thus calculated as:


It is assumed that these Ngrains on the cross section lead to Ngrain chains along thickness direction. Since lalso fits normal distribution, the average grain number should be d/m, and the variance of the average grain size should be σ2/(d/m); therefore:


The amount of chains with grain sizes from l¯to l¯ + Δl¯fits:


Another assumption is that the current that went through one grain chain is independent on other chains. On this basis, the relationship between the voltage and the current in one grain chain can be expressed as:


where VB is the breakdown voltage of single grain boundary and ρg is the electrical resistivity of grain. Consequently, the total current in this piece of ceramics should be the sum of current flowing in Ngrain chains:


Based on the model above, J-Echaracteristic under a fixed thickness can be acquired with increased applied voltage V, and the E1mA is able to be calculated. With variance of din Eq. (12), a series of J-Ecurves are acquired, and E1mA corresponding to different thicknesses are therefore known. According to grain size distribution of the measured ZnO varistor samples with high and medium E1mA found in Figure 13(a), average grain size mand variance σ2 are calculated and taken into the model. Hence, the thickness dependences of E1mA are plotted in Figure 14. The dc of high-voltage varistors is ∼0.2 mm, whereas it is ∼0.3 mm for medium-voltage varistors. Both dc and Ec from simulation fit the experimental results in Figure 13(a) well, proving the effectiveness of the proposed model.

Figure 14.

The thickness dependence of breakdown field via simulation (usage permitted by Elsevier).

In addition, if the average grain size is fixed, sample thickness dis reversely proportional to the variance of the average grain size. The maximum of the probability density f(μ) fits:


With increased d, f(m) increases, indicating a narrower grain size distribution. Therefore, dimensional effect of varistor ceramics originated from the thickness dependence of grain size variance.

As for CCTO ceramics which also exhibits dimensional effect shown in Figure 13(b), SEM images and grain size distribution on longitudinal section morphologies are investigated, as shown in Figure 15. Grains are smaller near the surface, whereas they are larger and denser in the interior. Quantitative analysis shows that grain sizes are more uniform near the surface while the size distribution is wider in the interior. The average grain size increased from 20.23 μm near the surface to 23.94 μm in the interior, while the porosity decreased from 4.95% near the surface to 0.33% in the interior. Although the grains with size below 30 μm are dominant in number, they contribute less to the section area. It can be seen in Figure 15(b), (d), and (f) that although grains with size below 15 μm contribute to more than 50% of grains, the sum of their occupied area is less than 10%. Despite small increase of average grain size from the surface to interior part, the major grain size that contributed to section areas is significantly different. On the surface, amount of the grains between 20 and 40 μm is most, while grains between 40 and 60 μm dominate the section area. Especially, the grain size range extends to 50–90 μm in the interior. From this point, it can be deduced that nonuniform distribution of grain size indeed contributed to dimensional effect in varistor ceramics, which is in accordance with simulation discussed above.

Figure 15.

SEM of cross-section morphologies, grain area, and grain size distribution at the surface (a and b), near the surface (c and d), and in the interior (e and f) of CCTO ceramics (usage permitted by Elsevier).

3.3. Elimination of dimensional effect

In not only ZnO varistor ceramics but also CCTO ceramics, dimensional effect exists because of nonuniform grain size distribution, which restricts its practical application. Therefore, in order to diminish or to attenuate dimensional effect, it is important to make grain size distribution more uniform. Despite the traditional processed ZnO varistor ceramics (Tr), another amine processed (Am) samples are prepared. At first, ZnO is dissolved in NH4(OH) and NH4(HCO3) solution with other additives in solutions, which is consequently heated to 110°C. After careful monitoring and controlling the pH of this mixed solution to 8–9, the precipitations are separated from the solution by filtration and washed with diethylamine solution to remove all chloride ions. When the solution is dried, the remained powders are calcined at 500°C, and then traditional processes are followed.

SEM photos of traditional processed (Tr) and amine processed (Am) ZnO samples are shown in Figure 16(a) and (b), respectively. Lots of small grains are scattered between compactly aligned big grains in Tr samples, as shown in Figure 16(a). However, no such small grains are seen in Am samples. The grains in Am samples are more uniform than those in Tr samples. Lots of grains with size below 3 μm exist in Tr samples, while the grains are compact with almost no grains with size below 3 μm.

Figure 16.

SEM pictures for (a) traditional processed and (b) amine processed ZnO varistors (usage permitted by Elsevier).

Thickness dependence of E1mA of Tr and Am samples are depicted in Figure 17. Tr samples exhibit distinct dimensional effect with dc of 0.28 mm. Notably, the Am samples show lower E1mA but exhibit no distinct dimensional effect. The decreased E1mA might be attributed to larger average grain size in Am samples than that in Tr samples. What is evident is that uniform grain sizes are obtained, which could effectively eliminate dimensional effect.

Figure 17.

Thickness dependence ofE1mA for traditional processed (Tr) ZnO varistors and amine processed (Am) ZnO varistors with identical recipe and processing variables (usage permitted by Elsevier).

4. Conclusion

Breakdown characteristics in varistor ceramics are investigated from grain boundary characteristics based on single barrier performance and barrier distribution. On one hand, different methods of doping including substitution and additional phase result in not only restriction on grain sizes but also manipulation of defects in Schottky barriers of varistor ceramics to enhance breakdown field to meet the requirement of device miniaturization. In addition, restriction on further decreased thickness of varistor ceramics is found as dimensional effect in not only ZnO ceramics but also CaCu3Ti4O12 ceramics. From theoretical analysis and experimental results, the dimensional effect is found closely related with the uniformity of grain sizes, which influence the distribution of grain boundaries quite well. Consequently, the breakdown characteristics in varistor ceramics are understood from the aspect of single barrier performance and spatial distribution of barriers.

© 2018 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution 3.0 License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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Jianying Li, Kangning Wu and Yuwei Huang (November 5th 2018). Breakdown Characteristics of Varistor Ceramics, Electrical and Electronic Properties of Materials, Md. Kawsar Alam, IntechOpen, DOI: 10.5772/intechopen.79720. Available from:

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