Services on Demand
- Cited by SciELO
- Access statistics
Print version ISSN 1516-1439On-line version ISSN 1980-5373
Mat. Res. vol.9 no.3 São Carlos July/Sept. 2006
Instituto de Química, Departamento de Físico-Química, Universidade Estadual Paulista, P. O. Box 355, 14801-907 Araraquara, São Paulo, Brazil
The present paper aims to verify the inuence of rare earth oxide such as lanthanum (La2O3) and neodymium (Nd2O3) doping SnO2 + 0.25%CoO + 0.75%MnO2 + 0.05%Ta2O5 system. The analysis focus on microstructural inuence on electrical properties. Microstructural analysis were made by using Transmission Electron Microscopy (TEM) at different regions of the samples. From such analysis it was found that La2O3 and Nd2O3 oxides cause heterogeneous segregation and precipitation at grain boundary concerning cobalt and manganese, decreasing the nonohmic electrical properties, as discussed, likely due to the increasing of grain boundary non-active potential barriers.
Keywords: ceramic, varistor, tin dioxide, rare earth oxides
Tin dioxide is an n-type semiconductor with rutile structure that present low densication after sintering1. However, SnO2 can be densied by its doping with specic oxides such as CoO and MnO224. The effects of CoO and MnO2 doping on the sintering of SnO2 were studied by Cerri et al.2. It was also reported that manganese and cobalt oxides are sensitive to temperature and oxygen partial pressure, changing its valence state with temperature. For instance, at higher temperatures (temperatures higher than 950 °C for cobalt and 1100 °C for manganese) both oxides present +2 valences. The densication of SnO2 ceramics has been attributed to the effect of cobalt and manganese in the surface of the SnO2 grains by replacing of Sn+4 by Co+2 and/or Mn+2 leading to the formation of oxygen vacancies. It is believed that such a picture increases oxygen diffusion at grain boundary, promoting densication.
Although the CoO and MnO2 are extremely active in the promotion of the SnO2 densication, these binary ceramic compounds are highly electronically resistive. Therefore, other additives are needed to improve electrical conduction. Pianaro et al.3 added 0.05 mol% of Nb2O5 to SnO2 + 1.0%CoO system obtaining a varistor behavior with nonlinear coeffient (a) about 8 and electric breakdown eld (Eb) of 1800 V.cm-1. In a later study, Antunes et al.4 substituted the Nb2O5 by Ta2O5 also obtaining varistor behavior with a about 13 and Eb about 2940 V.cm-1. Therefore, dopants of valence (+5), such as Nb+5 or Ta+5, when added in small amounts to SnO2-based ceramics are capable of leading to an increasing of electronic conductivity which assists the nonohmic behavior performance.
The non-ohmic behavior is dependent of the dopants added to SnO2 and the sintering conditions as temperature and atmosphere. During the sintering and cooling processes the diffusion of molecular oxygen throughout grain boundary may occur, promoting reactions responsible for potential barrier voltage formation5. The effect of partial substitution of CoO by MnO2 in the (98.95)%SnO2 + x%CoO + (1-x)%MnO2 + 0.05%Ta2O5 system was studied6,7 using x = 0.25 and 0.50 mol%. However, for x = 0.25 better nonlinear characteristics were found: a ~ 54 and Eb ~ 8500 V.cm-1 7.
The main goal of the present paper is to evaluate the inuence of small addition of La2O3 and Nd2O3 (both in 0.05 mol%) to SnO2 + 0.25%CoO + 0.75%MnO2 + 0.05%Ta2O5 system8 concerning microstructural characteristics and electrical properties.
2. Experimental Procedure
The oxides used to prepare the ceramic systems were SnO2 (Aldrich), CoO (Sigma), MnO2 (Sigma), Ta2O5 (Sigma), La2O3 (Sigma) and Nd2O3 (Sigma). The powder were prepared by mechanical mixing in isopropyl alcohol, using polypropylene jars with yttrium stabilized zirconium balls to aid the mixing process. After drying, the powders were pressed into pellets (11.0 mm x 1.0 mm) by uniaxial pressing, followed by isostatic pressing. The pellets were then sintered at 1300 °C (heating rate of 10 °C / min) for 1 hour and cooled (cooling rate of 5 °C / min) to room temperature. The grain size was determined by SEM (Scanning Electron Microscopy) micrographic analysis (obtained with a TOPCON SM 300) (ASTM-112 norm). The relative densities of the samples were measured using the Archimedes method. The presence of a solid solution phase was determined by X ray diffraction patterns (obtained with a SIEMENS diffractometer, model D-5000, CuKa radiation). In order to take the electrical measurements, silver contacts were painted on the samples' surfaces, after which the pellets were treated at 400 °C for 30 min. Current-voltage plots were obtained by measurements using High Voltage Unit Source (KEITHLEY Model 237). The microstructural analyses were also obtained by Transmission Electron Microscope (TEM) PHILIPS CM 200 equipped with an X ray Energy Dispersive (EDS) unit. To better description of the samples we adopt the following nomenclature: SnO2 + 0.25%CoO + 0.75%MnO2 + 0.05%Ta2O5 were named as S2C7MT and the same composition doped with La2O5 and Nd2O5 were named respectively as S2C7MTL and S2C7MTN.
3. Results and Discussion
The Figure 1 illustrates the microstructure obtained by SEM for (a) S2C7MT, (b) S2C7MTL and (c) S2C7MTN systems. From this gure it cannot be observed any segregation or precipitation. However, the addition of rare earth oxides promote a decrease in the average grain size, according to the results presented in Table 1. The relative density values are not inuenced substantially. The rare earth oxides led a similar behavior to that cause by the addition of the Cr2O3 in SnO2-based varistor systems3,4,9. Besides, segregated at grain boundary are causing changes on potential barrier height so that modifying the electrical properties. As shall be showed latter herein by means of TEM analysis, the observed behavior are being caused by precipitation and segregation at grain boundary region.
A large decrease of breakdown voltage (Eb) and nonlinear coeffcient a occurs due to the addition of rare earth oxides. The observed effect can be explained by the fact that the addition of the rare earth oxides cause a decrease on the amount of Co and Mn atoms segregation at grain boundary during sintering, leading to formation of higher amount of non-active potential barrier since the mean grain size are also decreasing. Accordingly, in addition, there are also grain boundary heterogeneities as will be better discussed further when TEM micrographs of the systems were introduced. From electrical point of view, these microstructural feature is reected on the amount of effective potential barrier throughout microstructure10,11. The phenomenology discussed in these two papers10,11 also applies here and the discussion on results validates the phenomenology that relates excess of precipitates to higher amount of non-active potential barriers.
Indeed, Figure 3 illustrates the microstructure obtained by TEM and EDS spectra for S2C7MT system. Table 2 presents the results from EDS analysis. The microstructure indicates that cobalt and manganese are found segregated and eventually precipitated at grains boundary region. In average, concerning bulk region it was found that SnO2 and Ta2O5 are homogeneously distributed as expected5 albeit sometimes Ta2O5 are found in higher concentration in the precipitates. The manganese and cobalt elements are also found to be homogeneously distributed in bulk regions. The Figure 3 also shows that near precipitates these elements are absent (below sensitivity detection of the equipment) which is in agreement to what was proposed in reference 11. These results are also in agreement with those reported in literature concerning the presence of a secondary phase of Co2SnO4 composition precipitated at SnO2.CoO-based system grain boundaries12. In addition, it was already showed that grain boundaries are rich in cobalt and/or manganese and that these elements are important in modelling the nonohmic properties5. However, an excess of precipitate can deteriorate the grain boundary electrical properties due to heterogeneous precipitation and/or segregation at grain boundaries as discussed in reference 11 which appear to be the specic role of rare earth doping SnO2.(Co1/4,Mn3/4)O-based varistor system concerning its inuence on microstructural and electrical properties.
Figure 4 illustrates the microstructure obtained by TEM and EDS spectra for S2C7MTN system. As can be seen from this illustrative TEM image of the system, the microstructure is more heterogeneous compared to that of S2C7MT system. In average, similarly to S2C7MT bulk region, the S2C7MTN bulk region contains SnO2 and Ta2O5 homogeneously distributed. There are also regions where cobalt and manganese were found precipitated, specially at triple grain junctions. Such regions are more abundant in S2C7MTN than in S2C7MT system. Besides, cobalt and manganese elements at grain boundaries were, in average, detected in lower amounts compared to S2C7MT system. The higher heterogeneity of S2C7MTN compared to S2C7MT is indicated by the analysis of larger precipitates containing cobalt and manganese in higher amount, where neodymium was found absent. Otherwise, in precipitates containing neodymium, cobalt is absent and manganese are found in higher amounts.
Figure 5 illustrates the microstructure obtained by TEM and EDS spectra for S2C7MTL system. The S2C7MTL system, in average, showed highly homogeneity of grains concerning amounts of tin, tantalum, cobalt and manganese elements, similarly to what was observed to S2C7MT and S2C7MTN systems. It was found higher amount of precipitates at triple points compared to S2C7MT. At grains boundaries double junctions these elements were found to be lower than those found in the S2C7MT and comparable to those found S2C7MTN systems. This behavior occurs in S2C7MTL and S2C7MTN likely because precipitates richer in Co and Mn at triple grain boundaries when are been formed consume the amount of Co and Mn elements adjacent to these regions11. Besides, it was observed from microstructure analysis that lanthanum presents an irregular distribution in the sample. In the precipitate points were lanthanum was found, cobalt was absent or in lower quantities compared to the points were lanthanum was not found. Similar features were found in neodymium containing systems.
In the specic case of SnO2.(Co1/4,Mn3/4)O-based varistor composition in which there are two dopants used to improve densication, CoO and MnO, the addition of rare earth dopants can cause deleterious precipitation leading to lower nonohmic properties. In the case of SnO2.MnO, according to what was discussed in the literature10,13, the nonohmic properties are controlled by the distribution of different junctions which is formed depending on the dopant and thermal treatment features. It was already showed that the SnO2.MnO system consists of two phases, SnO2 grains and Mn2SnO4, precipitated along multiple grain junctions10 and two types of SnO2-SnO2 grain boundaries were identied one rich in Mn and other poor in Mn element. It was concluded from reference 10 that the changes in the concentration of Mn along the grain boundary are associated not only to grain misorientation but also to Mn diffusity along the grain boundary, which controls the junctions' heterogeneities. Therefore, in other words, SnO2-based systems doped with MnO tending to cause a more heterogeneous microstructure which does not favor the nonohmic electrical properties since SnO2.CoO-based system when appropriated doped with La2O3 presents a homogeneous microstructure accompanied by high electrical nonohmic properties14. From this aspect, it is important to note that the deleterious effect of neodymium and lanthanum oxides observed in this work is an armful indirect effect which explain just the properties when MnO is present.
The addition of rare earth oxides in SnO2.(Co1/4,Mn3/4)O-based result in a deleterious effect over nonohmic electrical properties due to heterogeneous precipitation of metal elements at grain double and triple junctions. This effect on the microstructure results in a heterogeneous active junctions distribution throughout device, resulting in the decreasing of the nonohmic electrical properties.
The nancial support of this research project by the São Paulo state research funding institution, FAPESP and CNPq is gratefully acknowledged.
1. Jarzebski ZM, Sekowski K. Micro-Calorimetric Measurements in Fe-C and Fe-C-Si-Mn Alloys. Archiv Fur Das Eisenhuttenwesen. 1979; 50(5):225-7. [ Links ]
2. Cerri JA, Leite ER, Gouvea D, Longo E, Varela JA. Effect of Cobalt(II) oxide and Manganese(IV) oxide on sintering of Tin(IV) oxide. Journal of the American Ceramic Society. 1996 Mar; 79(3):799-804. [ Links ]
3. Pianaro SA, Bueno PR, Longo E, Varela JA. A New SnO2-Based Varistor System. Journal of Materials Science Letters. 1995 May; 14(10):6924. [ Links ]
4. Antunes AC, Antunes SRM, Pianaro SA, Rocha MR, Longo E, Varela JA. Nonlinear electrical behaviour of the SnO2 center dot CoO center dot Ta2O5 system. Journal of Materials Science Letters. 1998 Apr; 17(7):5779. [ Links ]
5. Bueno PR, Leite ER, Oliveira MM, Orlandi MO, Longo E. Role of oxygen at the grain boundary of metal oxide varistors: A potential barrier formation mechanism. Applied Physics Letters. 2001 Jul; 79(1):48-50. [ Links ]
6. Dibb A, Tebcherani SM, Lacerda W, Santos MRC, Cilense M, Varela JA, et al. Influence of simultaneous addition of MnO2 and CoO on properties of SnO2-based ceramics. Materials Letters. 2000 Oct; 46(1):39-43. [ Links ]
7. Dibb A, Tebcherani SM, Santos M, Cilense M, Varela JA, Longo E. MnO2 influence on the electrical properties of SnO2-based ceramic systems. Advanced Powder Technology Ii. 2001; 189-191: 161-5. [ Links ]
8. Dibb A, Tebcherani SM, Lacerda W, Cilense M, Varela JA, Longo E. Influence of the rare-earths oxides doped on the SnO2CoOMnO2Ta2O5 varistor system. Journal of Materials Science-Materials in Electronics. 2002 Sep; 13(9):567-70. [ Links ]
9. Bueno PR, Pianaro SA, Pereira EC, Bulhoes LOS, Longo E, Varela JA. Investigation of the electrical properties of SnO2 varistor system using impedance spectroscopy. Journal of Applied Physics. 1998 Oct; 84(7):3700-5. [ Links ]
10. Bueno PR, Orlandi MO, Simoes LGP, Leite ER, Longo E, Cerri JA. Nonohmic behavior of SnO2-MnO polycrystalline ceramics. I. Correlations between microstructural morphology and nonohmic features. Journal of Applied Physics. 2004 Sep; 96(5):2693-700. [ Links ]
11. Simoes LGP, Bueno PR, Orlandi MO, Leite ER, Longo E. The influence of excess precipitate on the non-ohmic properties of SnO2-based varistors. Journal of Electroceramics. 2003 Mar; 10(1):63-8. [ Links ]
12. Varela JA, Cerri JA, Leite ER, Longo E, Shamsuzzoha M, Bradt RC. Microstructural evolution during sintering of CoO doped SnO2 ceramics. Ceramics International. 1999; 25(3):253-6. [ Links ]
13. Orlandi MO, Bomio MRD, Longo E, Bueno PR. Nonohmic behavior of SnO2-MnO polycrystalline ceramics. II. Analysis of admittance and dielectric spectroscopy. Journal of Applied Physics. 2004 Oct; 96(7):38117. [ Links ]
14. Oliveira MM, Bueno PR, Cassia-Santos MR, Longo E, Varela JA. Sensitivity of SnO2 non-ohmic behavior to the sintering process and to the addition of La2O3. Journal of the European Ceramic Society. 2001 Sep; 21(9):1179-85. [ Links ]
Received: April 19, 2006; Revised: July 31, 2006