Abstract:
A nonreducing dielectric ceramic composition that includes BaTi0 3  as a main component, the BaTi0 3  containing alkali metal oxides in an amount more than 0.04 weight % as impurities. One or more of the following rare earth metal oxides (Re 2  O 3 ): Tb 2  O 3 , Dy 2  O 3 , Ho 2  O 3  and Er 2  O 3  ; and Co 2  O 3  in the following ratios: BaTiO 3  is 92.0-00.4 mol %; Re 2  O 3  is 0.3-4.0 mol %; and Co 2  O 3  is 0.3-4.0 mol %; the composition also includes the following subcomponents: 0.2-4.0 mol % BaO; 0.2-3.0 mol % of MnO; and 0.5-5.0 mol % of MgO. The composition may include 0.5-2.5 weight parts of oxide glass containing BaO-SrO-Li 2  O-SiO 2  incorporated with 100 weight parts for the above composition. The composition may also include 0.5-4.0 mol % CaTiO 3 , 0.5-3.5 mol % CaZrO 3  or one or both of NiO and Al 2  O 3  in an amount 0.3-3.0 mol %. Further, 0.5-2.5 weight parts of oxide glass containing BaO-SrO-Li 2  O-SiO 2  may be incorporated with 100 weight parts of the composition. SiO 2  in an amount of 0.2-3.0 mol % or one or both of NiO and Al 2  O 3  in an amount of 0.3-3.0 mol % may be incorporated in the composition. CaO or SrO may be substituted for BaO.

Description:
BACKGROUND OF THE INVENTION 
     1. Field of the Invention 
     The present invention relates to a nonreducing dielectric ceramic composition and, more particularly, to a composition used as a dielectric material for monolithic capacitors which include a base metal, such as nickel, as an internal electrode material. 
     2. Description of the Prior Art 
     Conventional dielectric ceramic materials are reduced to a semiconductive material when fired under neutral or reducing low partial pressure of oxygen. Therefore, a noble metal such as Pd or Pt should be used as an internal electrode material because they do not melt at sintering temperatures of the dielectric ceramic material and are not oxidized with the dielectric ceramic materials even if the sintering is carried out with a high partial pressure of oxygen. However, the use of such a noble metal is an obstacle to reduction of the manufacturing costs of monolithic ceramic capacitors. 
     Thus, in order to solve the above problem, it is desired to use a base metal such as Ni as an internal electrode material. However, when using such a base metal as the internal electrode material, it oxidizes and does not function as an electrode. Therefore, in order to use such a base metal as the internal electrode material, a dielectric ceramic material must be used which does not reduce to a semiconductive material even when fired in a neutral or reducing atmospheric gas having a low oxygen partial pressure but yet has a sufficient resistivity and a superior dielectric property. A dielectric ceramic material which meets these requirements is, for example, a BaTiO 3  -CaZrO 3  -MnO-MgO-based composition disclosed in Japanese patent Application Laid-Open No. 62-256422 (1987), or a BaTiO 3  -- (Mg, Zn, Sr, Ca)O-B 2  O 3  -SiO 2  -based composition disclosed in Japanese patent publication No. 61-14611 (1986). 
     However, in the nonreducing dielectric ceramic composition disclosed in Japanese Patent Application Laid Open No. 62-256422 (1987), CaZrO 3  or CaTiO 3  produced in the firing process is apt to provide a secondary phase with Mn or the like, and thus this would lead to danger of impairing reliability of the composition in a high temperature range. 
     Also, the composition disclosed in Japanese Patent Publication No. 61-14611 (1986) has dielectric constants of 1,000-2,800, and these values are inferior to the dielectric constants of 3,000-3,500 of the conventional ceramic composition using a noble metal such as Pd. Therefore, it is difficult to produce ceramic capacitors with a large capacitance without an increase in volume. 
     Still further, the temperature change rate of a dielectric constant of this composition falls within a change rate of ±10% between -25° C. and +85° C. with respect to a dielectric constant at 20° C., but in a change rate of high temperature exceeding +85° C., the change rate exceeds 10% and greatly shifts from the X7R characteristics specific by EIA. 
     SUMMARY OF THE INVENTION 
     Therefore, the principal object of the present invention is to provide a nonreducing dielectric ceramic composition which is fired without becoming semiconductive even in a low oxygen partial pressure atmosphere, and has a dielectric constant not less than 3,000 and high insulation resistance, and further satisfies a temperature change rate of dielectric constant within ±15% with respect to a dielectric constant at 25° C. between -55° C. and +125° C. 
     This invention is a nonreducing dielectric ceramic composition that includes 100 mol % of main components which include BaTiO 3  containing alkali metal oxides as impurities in an amount less than 0.04% by weight, at least one kind of rare earth metal oxides (Re 2  O 3 ) selected from Tb 2  O 3 , Dy 2  O 3 , Ho 2  O 3  and Er 2  O 3 , and Co 2  O 3  in the following ratios: BaTiO 3  92.0-99.4 mol %, Re 2  O 3  0.3-4.0 mol %, and Co 2  O 3  0.3-4.0 mol %, and subcomponents which include 0.2-4.0 mol % of BaO, 0.2-3.0 mol % of MnO, 0.5-5.0 mol % of MgO. 
     Furthermore, in the above nonreducing dielectric ceramic composition, 0.5-2.5 weight parts of oxide glass containing BaO-SrO-Li 2  O-SiO 2  may be incorporated based upon 100 weight parts for the above composition. 
     And, in the first nonreducing dielectric ceramic composition, 0.5-4.0 mol % CaTiO 3  may be incorporated therein as a subcomponent, and further, 0.5-2.5 weight parts of oxide glass containing BaO-SrO-Li 2  O-SiO 2  may be incorporated based upon 100 weight parts for the above composition. 
     In the first nonreducing dielectric ceramic composition, CaZrO 3  of 0.5-3.5 mol % may be incorporated therein as a subcomponent, and further, 0.5-2.5 weight parts of oxide glass containing BaO-SrO-Li 2  O-SiO 2  may be incorporated based upon 100 weight parts for the above composition. 
     Further, in the first nonreducing dielectric ceramic composition, 0.2-3.0 mol % SiO 2  as a subcomponent may be incorporated therein. 
     In the first nonreducing dielectric ceramic composition, one or both of NiO and Al 2  O 3  in an amount of 0.3-3.0 mol % as subcomponents may be incorporated therein. 
     And, in the first nonreducing dielectric ceramic composition, one or both of NiO and Al 2  O 3  in an amount of 0.3-3.0 mol % may be incorporated therein as a subcomponent and 0.5-2.5 weight parts of oxide glass containing BaO-SrO-Li 2  O-SiO 2  may be incorporated therein based upon 100 weight parts for the above composition. 
     In the second nonreducing dielectric ceramic composition, 0.2-4.0 mol % SrO may be included instead of BaO in the amount of 0.2-4.0 mol %. 
     Further, in the second nonreducing dielectric ceramic composition, 0.2-4.0 mol % SrO may be included instead of BaO in the amount of 0.2-4.0 mol %. 
     When the nonreducing dielectric ceramic composition according to the invention is fired in a neutral or reducing atmosphere, the dielectric ceramic is not reduced to a semiconductive state. Moreover, this nonreducing dielectric ceramic composition has a high insulation resistance value and a high dielectric constant which is not less than 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     Therefore, when using the nonreducing dielectric ceramic composition of the invention as a dielectric material for monolithic ceramic capacitors, a base metal such as Ni can be used for the internal electrode material. Thus, it is possible to reduce the manufacturing cost of monolithic ceramic capacitors without impairing their characteristics as compared with that of the conventional capacitors using a noble metal such as Pd as the internal electrode. 
     The above and further objects, features, aspects and advantages of the invention will more fully be apparent from the following detailed description of the embodiments. 
    
    
     BRIEF DESCRIPTION OF THE DRAWINGS 
     FIG. 1 is a graph showing a change rate of capacitance of Embodiment 3 when an applied d.c. electric field intensity is varied. 
    
    
     DESCRIPTION OF THE PREFERRED EMBODIMENTS 
     Embodiment 1 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, BaCO 3  for mol ratio correction of Ba to Ti, rare earth metal oxides, Co 2  O 3 , MnO, and MgO were prepared. These materials were weighed to prepare a mixture for the composition shown in Table 1. Further, for Samples No. 1-23, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for example, for Sample No. 24, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 25, BaTiO3 having 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, a powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it for 3 hours at 400° C. in air, and thereafter the disk was fired at the temperature shown in Table 2 for 2 hours in reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. Dielectric constant (E), dielectric loss (tan δ), insulation resistance value (log IR), and temperature change rate of capacitance (TCC) were measured at room temperature. The results are shown in Table 2. 
     In addition, the dielectric constant (E), dielectric loss (tan δ) were measured at a temperature of 25° C., frequency of 1 kHz and an A.C. voltage of 1 V. The insulation resistance value was measured at 25° C., applying a D.C. voltage of 500 V for two minutes, and the results are shown in logarithmic values (log IR). Concerning the temperature change rate of capacitance (TCC), change rates at -55° C. and 125° C. were determined based on the capacitance value at 25° C. as a reference (Δ C -55  /C 25 ,Δ C +125  /C 25 ), and also an absolute value of the maximum value of the temperature change rate of capacitance between -55° C. and +125° C. was determined based on the capacitance at 25° C. as a reference (|ΔC/C 25  | max ). 
     As can be seen from Table 2, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,300°-1,360° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition has a high insulation resistance value, over 11.0 in log IR, and a high dielectric constant above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined in the present invention as mentioned above is as follows. 
     First, the reason that the ranges of the main components are as defined above will be explained. 
     If the main component BaTiO 3  is less than 92.0 mol % as in Sample No. 4, the insulation resistance value and dielectric constant are lowered. If the BaTiO 3  exceeds 99.4 mol % as in Sample No. 3, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxides content in BaTiO 3  exceeds 0.04 weight % as in Samples No. 24 and No. 25, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are as defined above will be explained. 
     If the BaO content is less than 0.2 mol % as in Sample No. 9, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mol % as Sample No. 12, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 17, there is no improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO exceeds 3.0 mol % as in Sample No. 15, the insulation resistance value is decreased. 
     If the MgO content is less than 0.5 mol % as in Sample No 18, there is no flattening of the temperature change rate of capacitance, causing a tendency to shift the rate toward a (-) side especially in a low temperature range, and also there is no improvement of the insulation resistance value. If the MgO exceeds 5.0 mol % as in Sample No. 23, the dielectric constant and insulation resistance value are lowered. 
     In addition, the characteristic data shown in Table 2 is obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     Embodiment 2 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, BaCO 3  for mol ratio correction of Ba to Ti, rare earth metal oxides, Co 2  O 3 , MnO, MgO, and oxide glass were prepared. These materials were weighed to prepare a mixture for the composition shown in Table 3. Further for samples 101-127, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for Sample No. 128, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No 129, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, a powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it for 3 hours at 400° C. in air, and thereafter the disk was fired at the temperature shown in Table 4 for 2 hours, in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. Dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of Embodiment 1. The results are shown in Table 4. 
     As can be seen from Table 4, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduce even when fired at a temperature within a range of 1,260°-1,300° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition has a high insulation resistance value, over 12.0 in log IR, and a high dielectric constant, above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristic specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention is as follows. 
     First, the reason that the ranges of the main components are defined as discussed will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mol % as in Sample No. 104, the insulation resistance value and dielectric constant are lowered. If the BaTiO 3  content exceeds 99.4 mol % as in Sample No. 103, the effect of adding the rare earth metal oxide and Co 2  O 3  in lost, and the temperature change range of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxide content of the BaTiO 3  exceeds 0.04 weight % as in Samples No. 128 and No. 129, the dielectric constant is lowered. 
     Next, the reason that ranges of subcomponents are defined as discussed above will be explained. 
     If the BaO content is less than 0.2 mol % as in Sample No. 109, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mole % as in Sample No. 112, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 117, the improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO content exceeds 3.0 mol % as in Sample No. 115, the insulation resistance value is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 122 and No. 123, there is no flattening of the temperature change rate of capacitance, causing a tendency to shift the rate toward a (-) side, especially in a low temperature range, and there is no improvement of the insulation resistance value. If the MgO content exceeds 5.0 mol % as in Sample No. 127, the dielectric constant and insulation resistance value are lowered. 
     If the oxide glass content which contains BaO-SrO-Li 2  O-SiO 2  is less than 0.5 weight % as in Sample No. 121, the effects of lowering the sintering temperature and improving the anti-reduction are lost. If the oxide glass content which contains BaO-SrO-Li 2  O-SiO 2  is less than 5 weight % as in Sample No. 119, a decreased dielectric constant will result. 
     In addition, the characteristic data shown in Table 4 was obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are of the same composition. 
     Embodiment 3 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, BaCO 3  for mol ratio correction of Ba to Ti, rare earth metal oxides, Co 2  O 3 , MnO, MgO, CaTiO 3 , and oxide glass were prepared. These materials were weighed to prepare a mixture for a composition shown in Table 5. Further, for Samples No. 201-232, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for Sample No. 233, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 234, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet balanced by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, the powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it at 400° C. for 3 hours in air, and thereafter the disk was fired at the temperature shown in Table 6 for 2 hours, in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. A dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and a temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of Embodiment 1. Further, a D.C. bias characteristic is expressed by a change rate of an electrostatic capacitance value when a D.C. voltage is applied so as to form an electric field intensity of 2.0 (KV/mm) versus an electrostatic capacitance value when no voltage is applied. 
     And FIG. 1 is a graph showing a change rate of capacitance of the embodiments and examples for comparison when applied D.C. electric field intensity was varied. 
     As can be seen from Table 6 and FIG. 1, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,260°-1,300° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition shows a high insulation resistance value, over 12.0 in log IR, and a high dielectric constant, above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA, and the composition also has superior D.C. bias characteristics. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention as is follows. 
     First, the reason that the ranges of the main components are as defined above will be explained. 
     If the main component BaTiO 3  component is less than 92.0 mol % as in Sample No. 204, the insulation resistance value and dielectric constant is low. If the content of BaTiO 3  exceeds 99.4 mol %, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxides content in the BaTiO 3  exceeds 0.04 weight % as in Samples No. 233 and No. 234, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are defined above will be explained. 
     If the BaO content is less than 0.2 mol % as in Sample No. 209, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mol % as in Sample No. 212, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 217, there is no improvement in anti-reduction of composition and insulation resistance value is lowered. If the MnO content exceeds 3.0 mol % as in Sample No. 215, the insulation resistance value is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 222 and No. 223, a curve of the temperature change rate of capacitance tends to go single-peaked and to shift to a (-) side in a low temperature range and to a (+) side in a high temperature range (near Curie point), and improvement of insulation resistance is low. If the MgO content exceeds 5.0 mol % as in Sample No. 227, the dielectric constant and insulation resistance value is lowered. 
     If the CaTiO 3  content is less than 0.5 mol % as in Sample No. 232, improvement of the D.C. bias characteristic is lost and dependence on applied voltage of electrostatic capacitance is increased. If the CaTiO 3  content exceeds 4.0 mol % as in Sample No. 230, the temperature change rate of capacitance in a high temperature range tends to shift to a (-) side and the dielectric constant becomes lower. 
     If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  is less than 0.5 weight % as in Sample No. 221, the effects of lowered sintering temperature and improved anti-reduction are lost. If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  exceeds 2.5 weight % as in Sample No. 219, the dielectric constant is decreased. 
     In addition, the characteristic data shown in Table 6 is obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors having the same composition. 
     Embodiment 4 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, rare earth metal oxides, BaCO 3  , MnO, MgO, CaZrO 3 , and oxide glass were prepared. These materials were weighed to prepared a mixture for a composition shown in Table 7. Further, for Samples No. 301-332, BaTiO 3  containing 0.03 weight % was used, for Sample No. 333, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 334, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     The weighed materials thus obtained were mixed with a dispersion medium by a ball mill using PSZ balls to make a slurry. Then, an organic binder and plasticizer were added to the slurry and these were sufficiently agitated and then formed in to a sheet by the doctor blade method to obtain a ceramic green sheet. 
     Then, on one face of the ceramic green sheet thus obtained, conductive paste for forming internal electrodes was printed and dried, and then a plurality of the green sheets were laminated and pressed in the direction of the thickness to obtain a stacked body. The binder of the stacked body was removed by holding it at 320° C. for 5 hours in air and thereafter the stacked body was fired at the temperature shown in Table 8 for 2 hours in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic body. 
     The resultant sintered ceramic body was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. A dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR) and a temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of the Embodiment 1. Further, a mean time to failure (MTTF) of the capacitor was measured. The results are shown in Table 8. 
     In addition, the MTTF was calculated in such a way that taking a number of samples n=18, and applying an electric field intensity of 10.0 KV/mm to the samples at an ambient temperature of 150° C. and counting time to dielectric breakdown. 
     As can be seen from Table 8, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,260°-1,300° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition has a value, 4,000 or more, of a product of an insulation resistance value and an electrostatic capacitance value (RC product) and a high dielectric constant, more than 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA, and the MTTF is 500 hours or more when an electric field intensity of 10.0 KV/mm is applied with super acceleration at an ambient temperature of 150° C. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention is as follows. 
     First, the reason that the ranges of the main component are as defined above will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mol % as in Sample No. 304, the insulation resistance value and dielectric constant is lowered. If the BaTiO 3  content exceeds 99.4 mol % as in Sample No. 303, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxide content in the BaTi 3  exceeds 0.04 weight % as in Samples No. 333 and No. 334, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are as defined above will be explained. 
     If the BaO content is less than 0.2 mol % as in Sample No. 309, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mol % as in Sample No. 312, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 317, there is no improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO content exceeds 3.0 mol % as in Sample No. 315, the insulation resistance value is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 322 and No. 323, a curve of the temperature change rate of capacitance tends to show a single peak and to shift to a (-) side in a low temperature range and to a (+) side in a high temperature range (near Curie point), and improvement of insulation resistance is lost. If the MgO content exceeds 5.0 mol % as in Sample No. 326, the dielectric constant and insulation resistance value is lowered. 
     If the CaZrO 3  content is less than 0.5 mol % as in Samples No. 331 and No. 332, there is no improvement of MTTF. The CaZrO 3  content exceeds 3.5 mol % as in Sample No. 329, the temperature change rate of capacitance in a high temperature range (near Curie point) tends to shift to a (-) side and the dielectric constant is lowered. 
     If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  ia less than 0.5 weight % as in Sample No. 321, the effects of lowering the sintering temperature and improving anti-reduction are lost. If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  exceeds 2.5 weight % as in Sample No. 319, the dielectric constant is decreased. 
     In addition, the characteristic data shown in Table 8 is obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     Embodiment 5 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, BaCO 3  for mol ratio correction of Ba to Ti, rare earth metal oxides, Co 2  O 3 , MnO, SiO 2  , MgO were prepared. These materials were weighed to prepare a mixture for a composition shown in Tale 9. Further, for samples No. 401-429, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for Sample No. 430, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 431, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, the powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it for 3 hours at 400° C. in air, and thereafter the disk was fired at the temperature shown in Table 10 for 2 hours in a reducing atmospheric gas flown with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. Dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and temperature change rate of capacitance (TCC) were measured at room temperature. The results are shown in Table 10. 
     As can be seen from Table 10, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,260°-1,300° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition has a high insulation resistance value, over 11.0 in log IR, and a high dielectric constant, above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention is as follows. 
     First, the reason that the ranges of the main components are defined as discussed above will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mol % as in Sample No. 404, the insulation resistance value and dielectric constant are lowered. If the content of BaTiO 3  exceeds 99.4 mol % as in Sample No. 403, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxides in the BaTiO 3  exceeds 0.04 mol % as in Samples No. 430 and No. 431, the dielectric constant is lowered. 
     Next, the reason that the ranges of the subcomponents are as defined above will be explained. 
     If the BaO content is less than 0.2 mol % as in Sample No. 409, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mol % as in Sample No. 412, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 417, there is no improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO exceeds 3.0 mol % as in Sample No. 415, the insulation resistance value is decreased. 
     In the SiO 2  content is less than 0.2 mol % as in Sample No. 423, the sintering temperature is not lowered. If the SiO 2  content exceeds 5.0 mol % as in Sample No. 420, the dielectric constant is lowered. 
     If the MgO content is less than 0.5 mol % as in Sample No. 424, there is no flattening of the temperature change rate of capacitance, causing a tendency to shift the rate toward a (-) side, especially, in a low temperature range, and also there is no improvement of the insulation resistance value. If the MgO content exceeds 5.0 mol % as in Sample No. 429, the dielectric constant and insulation resistance value are lowered. 
     In addition, the characteristic data shown in Table 10 is obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     Embodiment 6 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, rare earth metal oxides, Co 2  O 3 , MnO, NiO, Al 2  O 3 , and MgO were prepared. These materials were weighed to prepare a mixture of the composition shown in Table 11. Further, for Samples No. 501-529, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for Sample No. 530, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 531, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, a powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it at 400° C. for 3 hours in air, and thereafter the disk was fired at the temperature shown in Table 12 for 2 hours in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. A dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and a temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of Embodiment 1. The results are shown in Table 12. 
     As can be seen from Table 12, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,300°-1,360° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric composition has a high insulation resistance value, over 11.0 in log IR at room temperature and a small decline of it at a high temperature, and a high dielectric constant, above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention is as follows. 
     First, the reasons that the ranges of the main component are as defined above will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mole % as in Sample No. 504, the insulation resistance value and dielectric constant become lower. If the BaTiO 3  content exceeds 99.4 mol % as in Sample No. 503, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxides content is the BaTiO 3  exceeds 0.04% as in Samples No. 530 and No. 531, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are as defined above will be explained. 
     In the BaO content is less than 0.2 mol % as in Sample No. 509, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mol % as in Sample No. 512, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 517, there is no improvement in anti-reduction of the composition and the insulation resistance value is lowered. If the MnO exceeds 2.0 mol % as in Sample No. 515, the insulation resistance value, especially one in a high temperature range is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 524 and No. 525, there is no effect on flattening a curve of the temperature change rate of capacitance, causing a tendency to shift the curve to a (-) side especially in a low temperature range, and improvement of insulation resistance value is lost. If the MgO content exceeds 5.0 mol % as in Sample No. 529, the dielectric constant and insulation resistance value are lowered. 
     If the NiO or Al 2  O 3  content is less than 0.3 mol % as in Sample No. 518, there is no improvement of anti-reduction of the composition and lowering insulation resistance value and there is no improvement of IR value at high temperature. If the NiO content exceeds 3.0 mol % as in Sample No. 521, insulation resistance value is decreased. If the Al 2  O 3  content exceeds 3.0 mol % as in Sample No. 522, sinterability and dielectric constant are reduced, and dielectric loss is increased. 
     In addition, the characteristic data shown in Table 12 are ones obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     Embodiment 7 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, rare earth metal oxides, Co 2  O 3 , MnO, NiO, Al 2  O 3 , MgO and oxide glass were prepared. These materials were weighed to prepare a mixture for the composition shown in Table 13. Further, for Samples No. 601-632, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for Sample No. 633, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 634, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, a powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it at 400° C. for 3 hours in air, and thereafter the disk was fired at the temperature shown in Table 14 for 2 hours in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. Dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and a temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of Embodiment 1. The results are shown in Table 14. 
     As can be seen from Table 14, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,230°-1,280° C. in a neutral or reducing atmospheric gas. Still furthermore, the ceramic obtained from this nonreducing dielectric ceramic composition has a high insulation resistance value, over 12.0 in log IR at room temperature and a small decline of it at a high temperature, and a high dielectric constant, above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention as follows. 
     First, the reason that the ranges of the main components are as defined above will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mol % as in Sample No. 604, the insulation resistance value and dielectric constant become lower. If the BaTiO 3  content exceeds 99.4 mol % as in Sample No. 603, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxides content in the BaTiO 3  exceeds 0.04 weight % as in Samples No. 633 and No. 634, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are as defined above will be explained. 
     If the BaO content is less than 0.2 mol % as in Sample No. 609, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the BaO content exceeds 4.0 mol % as in Sample No. 612, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 617, there is no improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO content exceeds 2.0 mol % as in Sample No. 615, the insulation resistance value, especially one in a high temperature range, is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 627 and No. 628, there is no effect on flattening a curve of the temperature change rate of capacitance, causing a tendency to shift the curve to a (-) side, especially in a low temperature range, and improvement of the insulation resistance value is lost. If the MgO content exceeds 5.0 mol % as in Sample No. 632, insulation resistance value is lowered. 
     If the NiO or Al 2  O 3  content is less than 0.3 mol % as in Sample No. 618, there is no improvement of anti-reduction of the composition, the insulation resistance value is decreased and there is no improvement of IR value at high temperature. If the NiO content exceeds 3.0 mol % as in Sample No. 621, insulation resistance value is decreased. If the Al 2  O 3  content exceeds 3.0 mol % as in Sample No. 622, sinterability and dielectric constant are decreased and dielectric loss is increased. 
     If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  is less than 0.5 weight % as in Sample No. 626, the lowering of sintering temperature and improvement of anti-reduction are lost. If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  exceeds 2.5 weight % as in Sample No. 624, the dielectric constant is decreased. 
     In addition, the characteristic data shown in Table 14 is obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     Embodiment 8 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, CaCO 3  for mol ratio correction of Ba to Ti, rare earth metal oxides, Co 2  O 3 , MnO, MgO and oxide glass were prepared. These materials were weighed to prepare a mixture for the composition shown in Table 15. Further, for Samples No. 701-727, BaTiO 3  containing 0.03 weight % of alkali metal oxides was used, for Sample No. 728, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 727, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, a powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a press of 2 ton/cm 2 . 
     Then the binder of the disk thus obtained was removed by holding it at 400° C. for 3 hours in air, and thereafter the disk was fired at the temperature shown in Table 16 for 2 hours in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. Dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of Embodiment 1. The results are shown in Table 16. 
     As can be seen from Table 16, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,260°-1,300° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition has a high insulation resistance value over 12.0 in log IR, and a high dielectric constant above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention is as follows. 
     First, the reason that the ranges of the main components are as defined above will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mol % as in Sample No. 704, the insulation resistance value and dielectric constant are lowered. If the BaTiO 3  content exceeds 99.4 mol % as in Sample No. 703, the effect of adding rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance in a high temperature range (near Curie point) is greatly shifted towards a (+) side. 
     If the alkali metal oxides content in the BaTiO 3  exceeds 0.04 weight % as in Samples No. 728 and No. 729, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are as defined above will be explained. 
     If the CaO content is less than 0.2 mol % as in Sample No. 729, the composition is reduced during firing in a neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the CaO content exceeds 4.0 mol % as Sample No. 712, sinterability is lowered. 
     If the MnO is less than 0.2 mol % as in Sample No. 717, there is no improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO content exceeds 3.0 mol % as in Sample No. 715, the insulation resistance value is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 722 and No. 723, there is no effect on flattening a curve of the temperature change rate of capacitance, causing a tendency to shift the curve to a (-) side, especially in a low temperature range, and improvement of insulation resistance value is lost. If the MgO content exceeds 5.0 mol % as in Sample No. 727, the dielectric constant and the insulation resistance value are lowered. 
     If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  is less than 0.5 weight % as in Sample No. 721, the effect of lowering the sintering temperature and improving anti-reduction are lost. If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  exceeds 2.5 weight % as in Sample No. 719, the dielectric constant is decreased. 
     In addition, the characteristic data shown in Table 16 is obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     Embodiment 9 
     As starting materials, BaTiO 3  having different contents of alkali metal oxides as impurities, SrCO 3  for mol ratio correction of Ba to Ti, rare earth metal oxides, Co 2  O 3 , MnO, MgO and oxide glass were prepared. These materials were weighed to prepare a mixture for the composition shown in Table 17. Further, for Samples No. 801-827, BaTiO 3  containing 0.03 weight % of alkali metal oxides were used, for Sample No. 828, BaTiO 3  containing 0.05 weight % of alkali metal oxides was used, and for Sample No. 829, BaTiO 3  containing 0.07 weight % of alkali metal oxides was used. 
     Vinyl acetate binder in an amount of 5 weight % was added to the weighed mixed material, and then it was sufficiently wet-blended by a ball mill using PSZ balls. After evaporating the dispersion medium and drying the mixture, a powder of the mixture was obtained by a grading process. The powder thus obtained was compacted into a disk having a 10 mm diameter and a 1 mm thickness under a pressure of 2 ton/cm 2 . 
     Then, the binder of the disk thus obtained was removed by holding it at 400° C. for 3 hours in the air, and thereafter the disk was fired at the temperature shown in Table 18 for 2 hours in a reducing atmospheric gas flow with a H 2  /N 2  volume ratio of 3/100 to obtain a sintered ceramic disk. 
     The resultant sintered ceramic disk was coated with a silver paste on opposite sides and baked to obtain a ceramic capacitor. A dielectric constant (ε), dielectric loss (tan δ), insulation resistance value (log IR), and a temperature change rate of capacitance (TCC) were measured at room temperature in the same condition as that of Embodiment 1. The results are shown in Table 18. 
     As can be seen from Table 18, a nonreducing dielectric ceramic composition according to the invention has high resistance to reduction even when fired at a temperature within a range of 1,260°-1,300° C. in a neutral or reducing atmospheric gas. Still further, the ceramic obtained from this nonreducing dielectric ceramic composition has a high insulation resistance value, over 12.0 in log IR, and a high dielectric constant, above 3,000, and its temperature change rate of capacitance satisfies the X7R characteristics specified by EIA. 
     The reason why the ranges of main components and subcomponents are defined as mentioned above in the present invention is as follows. 
     First, the reason that the ranges of the main components are as defined above will be explained. 
     If the main component BaTiO 3  content is less than 92.0 mol % as in Sample No. 804, the insulation resistance value and dielectric constant are lowered. If the BaTiO 3  content exceeds 99.4 mol % as in Sample No. 803, the effect of adding the rare earth metal oxide and Co 2  O 3  is lost, and the temperature change rate of capacitance is a high temperature range (near Curie point) is greatly shifted toward a (+) side. 
     If the alkali metal oxides content in the BaTiO 3  exceeds 0.04 weight % as in Samples No. 828 and No. 829, the dielectric constant is lowered. 
     Next, the reason that the ranges of subcomponents are as defined above will be explained. 
     If the SrO content is less than 0.2 Mol % as in Sample No. 809, the composition is reduced during firing in the neutral or reducing atmospheric gas, and the insulation resistance value is lowered. If the SrO exceeds 4.0 mol % as in Sample No. 812, sinterability is lowered. 
     If the MnO content is less than 0.2 mol % as in Sample No. 817, there is no improvement of anti-reduction of the composition and the insulation resistance value is lowered. If the MnO content exceeds 3.0 mol % as in Sample No. 815, the insulation resistance value is decreased. 
     If the MgO content is less than 0.5 mol % as in Samples No. 822 and No. 823, there is no effect on flattening a curve of the temperature change rate of capacitance causing a tendency to shift to a (-) side, especially in a low temperature range, and improvement of insulation resistance value is lost. If the MgO content exceeds 5.0 mol % as in Sample No. 827, the dielectric constant and the insulation resistance value are lowered. 
     In the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  is less than 0.5 weight % as in Sample No. 821, the effects of lowering a sintering temperature and improving anti-reduction are lost. If the oxide glass content that contains BaO-SrO-Li 2  O-SiO 2  exceeds 2.5 weight % as in Sample No. 819, the dielectric constant is reduced. 
     In addition, the characteristic data shown in Table 16 in obtained using disk type capacitors, but approximately the same data can be obtained using monolithic capacitors which are made by the same composition. 
     
                                           TABLE 1__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   BaO  MnO  MgONo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)__________________________________________________________________________ 1    97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0 2    99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0 3*   99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0 4*   90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0 5    93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0 6    97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  1.0  2.0 7    96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0 8    96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0 9*   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.010    96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.011    96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0 12*  96.5 Ho.sub.2 O.sub.3          1.5 20   5.0  1.5  2.013    97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  3.014    97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.0  3.0 15*  97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.5  3.016    97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.3  3.0 17*  97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.1  3.0 18*  96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.419    96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.620    96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  3.021    96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  4.022    96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  5.0 23*  96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  6.0 24*  96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  1.0 25*  96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  1.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 2__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRIC            INSULATIONSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       RESISTANCENo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         log IR__________________________________________________________________________ 1    1340      3110    1.6     -9.7 +2.5 9.7 11.8 2    1340      3360    1.7     -9.1 -0.3 9.1 11.7 3*   1360      3320    1.6     -14.8                                +18.6                                     35.7                                         11.6 4*   1300      2910    1.7     -8.2 -1.7 8.2 10.4 5    1300      3280    1.9     -9.2 +3.6 9.2 11.6 6    1340      3330    1.7     -9.2 -0.8 9.2 11.5 7    1360      3190    1.8     -10.9                                +2.4 10.9                                         11.6 8    1340      3220    1.8     -9.8 +2.8 9.8 11.7 9*   unmeasurable as being semiconductive10    1340      3280    1.9     -10.7                                -3.2 10.7                                         11.611    1360      3060    1.8     -11.1                                -3.9 11.1                                         11.5 12*  unmeasurable as not sintered enough at 1360° C.13    1340      3180    1.8     -5.7 +7.9 9.8 11.714    1340      3210    1.7     -7.4 +8.1 9.1 11.6 15*  1320      3030    1.6     -3.4 +8.6 8.6 9.716    1340      3160    1.7     -7.3 +0.3 7.3 11.7 17*  1340      2940    9.6     -9.7 -3.6 9.7 8.1 18*  1340      3130    1.7     -15.8                                -3.6 15.8                                         10.419    1340      3220    1.7     -9.1 -4.8 9.1 11.620    1360      3190    1.9     -4.5 -9.7 9.7 11.521    1340      3080    1.7     -6.8 +4.8 6.8 11.422    1320      3010    1.6     -7.6 +1.8 7.6 11.2 23*  1300      2820    1.6     -7.2 +3.6 7.2 10.3 24*  1340      2620    1.6     -7.8 +3.3 7.8 11.5 25*  1340      2460    1.5     -8.2 +3.7 10.8                                         11.4__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 3__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   BaO  MnO  MgO  OXIDE GLASSNo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                  (wt parts)__________________________________________________________________________101   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0  1.0102   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0  1.0 103* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0  1.0 104* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0  1.0105   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0  1.0106   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  1.0  2.0  1.0107   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0  1.0108   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0  1.0 109* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.0  1.0110   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.0  1.0111   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0  1.0 112* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  1.5  2.0  1.0113   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  3.0  1.0114   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.0  3.0  1.0 115* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.5  3.0  1.0116   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.3  3.0  1.0 117* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.1  3.0  1.0118   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.0 119* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  3.0120   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  0.5 121* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  0.3 122* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.2  1.0 123* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.4  1.0124   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  3.0  1.0125   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  4.0  1.0126   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  5.0  1.0 127* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  6.0  1.0 128* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  1.0  1.0 129* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  1.0  1.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 4__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRIC            INSULATIONSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       RESISTANCENo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         log IR__________________________________________________________________________101   1280      3150    1.7     -9.2 +2.1 9.2 12.7102   1280      3420    1.9     -8.6 -0.3 8.6 12.6 103* 1300      3380    1.6     -13.6                                +18.6                                     38.6                                         12.6 104* 1300      2820    1.7     -8.8 -0.6 8.8 11.7105   1260      3230    1.8     -9.4 +2.4 9.4 12.7106   1260      3290    1.6     -9.8 -0.3 9.8 12.7107   1260      3160    1.7     -11.8                                +1.8 11.8                                         12.5108   1280      3170    1.8     -10.6                                +2.8 10.6                                         12.6 198* unmeasurable as being semiconductive110   1300      3230    1.8     -11.8                                +3.6 11.8                                         12.5111   1300      3080    1.9     -11.4                                -4.8 11.4                                         12.4 112* unmeasurable as not sintered enough at 1360° C.113   1280      3160    1.7     -6.8 +8.2 9.4 12.6114   1260      3230    1.7     -7.3 +8.4 8.4 12.5 115* 1260      3040    1.7     -3.4 +9.2 9.2 10.5116   1280      3170    1.6     -7.6 +0.3 7.6 12.6 117* 1280      2970    8.7     -20.6                                -3.6 20.6                                         9.2118   1260      3090    1.6     -9.1 +2.3 9.1 12.6 119* 1260      2880    1.8     -7.8 +3.8 7.8 12.4120   1280      3140    1.7     -9.8 -6.8 9.8 12.5 121* 1360      3170    1.7     -8.6 +7.7 8.6 11.6 122* 1280      3130    1.6     -16.8                                -3.6 16.8                                         11.5 123* 1280      3190    1.6     -14.8                                -8.6 14.8                                         11.7124   1300      3220    1.8     -3.8 -9.2 9.2 12.5125   1280      3100    1.7     -7.4 +4.8 7.4 12.3126   1280      3010    1.6     -8.6 +2.8 8.6 12.2 127* 1280      2860    1.7     -8.2 +3.6 8.2 11.4 128* 1280      2610    1.5     -7.2 +3.3 9.8 12.5 129* 1280      2420    1.6     -7.0 +3.7 10.8                                         12.4__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 5__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   BaO  MnO  MgO  CaTiO.sub.3                                       OXIDE GLASSNo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                  (mol %)                                       (wt parts)__________________________________________________________________________201   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0  1.0  1.0202   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0  1.0  1.0 203* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0  1.0  1.0 204* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0  1.0  1.0205   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0  1.0  1.0206   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  1.0  2.0  1.0  1.0207   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0  1.0  1.0208   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0  1.0  1.0 209* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.0  1.0  1.0210   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.0  1.0  1.0211   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0  1.0  1.0 212* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  1.5  2.0  1.0  1.0213   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  3.0  2.0  1.0214   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.0  3.0  2.0  1.0 215* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.5  3.0  2.0  1.0216   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.3  3.0  2.0  1.0 217* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.1  3.0  2.0  1.0218   96.5 Tb.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.0  2.0 219* 96.5 Tb.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.0  3.0220   96.5 Tb.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.0  0.5 221* 96.5 Tb.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.0  0.3 222* 96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.2  3.0  1.5 223* 96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.4  3.0  1.5224   96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  3.0  3.0  1.5225   96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  4.0  3.0  1.5226   96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  5.0  3.0  1.5 227* 96.0 Er.sub.2 O.sub.3          1.5 2.5  1.5  1.0  6.0  3.0  1.5228   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  3.0  1.5229   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  4.0  1.5 230* 97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  5.0  1.5231   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  0.5  1.5 232* 97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  0.3  1.5 233* 97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  1.0  1.5 234* 97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.5  1.0  1.5__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 6__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRIC             INSULATION                                                  BIASSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)        RESISTANCE                                                  characteristicNo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                          log IR  ΔC__________________________________________________________________________                                                  (%)201   1280      3210    1.7     -9.6 +1.5 9.6  12.6    -11.0202   1280      3360    1.8     -7.9 -1.1 7.9  12.5    -11.8 203* 1300      3310    1.7     -12.6                                +26.5                                     42.8 12.5    -12.3 204* 1300      2780    1.8     -8.6 -1.3 8.6  11.4    -12.1205   1260      3290    1.7     -9.1 +1.9 9.1  12.7    -11.6206   1260      3270    1.6     -9.6 -0.3 9.6  12.6    -11.4207   1260      3230    1.8     -10.9                                +1.4 10.9 12.5    -12.2208   1280      3290    1.7     -10.3                                +2.8 10.3 12.5    -12.5 209  unmeasurable as being semiconductive210   1300      3270    1.9     -10.9                                +3.8 10.9 12.3    -12.6211   1300      3160    2.1     -11.2                                -4.1 11.2 12.1    -11.9 212* unmeasurable as not sintered enough at 1360° C.213   1260      3100    1.8     -6.3 +4.4 9.1  12.5    -9.6214   1260      3150    1l8     -6.1 +4.1 8.8  12.2    -10.1 215* 1260      3060    1.9     -4.2 +5.2 9.2  10.6    -9.8216   1280      3120    1.7     -9.1 +0.3 9.1  12.6    -10.2 217* 1280      3010    6.9     -18.4                                +1.2 18.4 9.8     -9.9218   1260      3110    1.8     -9.4 +1.3 9.4  12.5    -10.4 219* 1260      2830    1.9     -7.6 -0.3 7.6  12.2    -10.3220   1280      3170    1.7     -9.7 -6.5 10.3 12.4    -10.0 221* 1350      3040    2.0     -8.6 -7.2 8.6  11.3    -9.8 228* 1280      3010    1.6     -17.3                                +6.9 26.8 11.6    -7.8 223* 1280      3090    1.7     -15.4                                +4.8 29.3 11.7    -8.1224   1300      3110    1.6     -4.2 -9.4 9.4  12.6    -7.9225   1280      3130    1.7     -6.8 +3.6 7.9  12.4    -8.3226   1280      3030    1.8     -7.1 + 2.8                                     8.3  12.3    -7.7 227* 1300      2820    1.9     -8.8 +3.1 8.8  11.6    -8.0228   1280      3080    1.8     -7.2 +2.1 7.2  12.6    -7.2229   1280      3010    1.7     -6.1 -3.3 8.1  12.6    -6.3 230* 1280      2710    1.8     -5.0 -10.3                                     16.2 12.4    -6.0231   1280      3220    1.6     -9.2 +2.4 9.2  12.3    -13.0 232* 1280      3200    1.7     -10.1                                +1.2 10.1 12.5    -23.9 233* 1280      2730    1.6     -8.2 +2.3 9.6  12.4    -12.2 234* 1280      2540    1.7     -8.0 +2.7 10.2 12.3    -12.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 7__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   BaO  MnO  MgO  CaZrO.sub.3                                       OXIDE GLASSNo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                  (mol %)                                       (wt parts)__________________________________________________________________________301   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0  2.0  1.5302   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0  2.0  1.5 303* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0  2.0  1.5 304* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0  2.0  1.5305   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0  2.0  1.5306   96.5 Ho.sub.2 O.sub.3          1.5 2.0  2.0  1.0  2.0  2.0  1.5307   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0  2.0  1.5308   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0  2.0  1.5 309* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.0  2.0  1.5310   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.0  2.0  1.5311   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0  2.0  1.5 312* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  1.5  2.0  2.0  1.5313   97.5 Er.sub.2 O.sub.3          1.0 1.5  1.5  2.5  3.0  2.5  1.5314   97.5 Er.sub.2 O.sub.3          1.0 1.5  1.5  3.0  3.0  2.5  1.5 315* 97.5 Er.sub.2 O.sub.3          1.0 1.5  1.5  3.5  3.0  2.5  1.5316   97.5 Er.sub.2 O.sub.3          1.0 1.5  1.5  0.3  3.0  2.5  1.5 317* 97.5 Er.sub.2 O.sub.3          1.0 1.5  1.5  0.1  3.0  2.5  1.5318   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.5  2.0 319* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.5  3.0320   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.5  0.5 321* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  2.5  0.3 322* 97.5 Tb.sub.2 O.sub.3          1.5 1.0  1.5  1.0  0.2  3.0  1.0 323* 97.5 Tb.sub.2 O.sub.3          1.5 1.0  1.5  1.0  0.4  3.0  1.0324   97.5 Tb.sub.2 O.sub.3          1.5 1.0  1.5  1.0  3.0  3.0  1.0325   97.5 Tb.sub.2 O.sub.3          1.5 1.0  1.5  1.0  5.0  3.0  1.0 326* 97.5 Tb.sub.2 O.sub.3          1.5 1.0  1.5  1.0  6.0  3.0  1.0327   98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  3.0  1.0328   98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  3.5  1.0 329* 98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  4.0  1.0330   98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  0.5  1.0 331* 98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  0.4  1.0 322* 98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  0.3  1.0 333* 98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  1.5  1.0 334* 98.0 Dy.sub.2 O.sub.3          1.0 1.0  1.5  1.0  1.5  1.5  1.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 8__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRICSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)        RC PRODUCT                                                  MTTFNo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                          (Ω ·                                                  (hour)__________________________________________________________________________301   1280      3390    1.8     -0.7 -11.7                                     11.7 6670    780302   1280      3360    1.8     -0.9 -11.1                                     11.1 7430    810 303* 1300      3310    1.7     -15.3                                +29.5                                     52.8 3980    not measured 304* 1300      2820    1.8     -0.6 -11.3                                     11.3 2420    830305   1280      3190    1.7     -0.1 -11.9                                     11.9 4100    790306   1260      3370    1.6     -0.6 -10.3                                     10.3 5800    910307   1260      3230    1.8     -0.9 -11.4                                     11.4 4830    870308   1260      3290    1.7     -0.3 -12.8                                     12.8 4420    800 309* unmeasurable as being semiconductive310   1300      3370    1.9     -0.9 -10.8                                     10.8 4890    740311   1300      3260    1.7     -1.2 -10.1                                     10.1 5210    850 312* unmeasurable as not sintered enough at 1360° C.313   1260      3200    1.8     -0.3 -11.2                                     11.2 4830    840314   1260      3150    1.8     -0.1 -10.8                                     10.8 2500    870 315* 1260      3060    1.9     +0.2 -10.7                                     10.7 2810    820316   1280      3320    1.7     -0.1 -10.3                                     10.3 6720    950 317* 1300      3010    6.9     -4.2 -11.2                                     11.2  860     27318   1260      3410    1.8     -0.4 -10.3                                     10.3 6810    860 319* 1260      2730    2.0     -0.6 -14.9                                     14.9 4040    800320   1280      3270    1.8     -0.7 -10.6                                     10.6 6090    &gt;1000 321* 1350      3140    2.8     -0.6 -9.8 9.8  1390    160 322* 1280      3110    1.6     -18.3                                +24.1                                     28.1 3480    930 323* 1280      3190    1.7     -17.4                                +26.6                                     31.6 3710    960324   1300      3340    1.8     -0.2 -9.4 9.4  6920    &gt;1000325   1280      3290    1.7     -0.1 -8.8 8.8  7020    &gt;1000 326* 1300      2820    1.9     -0.8 -9.1 9.1  3080    &gt;1000327   1280      3280    1.8     -0.2 -11.4                                     11.4 6890    980328   1280      3410    1.7     -0.1 -12.1                                     12.1 6510    &gt;1000 329* 1260      2810    1.8     +0.4 -17.3                                     17.3 4210    &gt;1000330   1280      3220    1.6     +0.2 -10.1                                     10.1 5980    620 331* 1280      3310    1.7     ±0.0                                -9.8 9.8  5380    340 332* 1280      3200    1.8     -0.6 -11.2                                     11.2 5870    270 333* 1280      2840    1.6     -0.2 -10.8                                     10.8 4930    710 334* 1280      2620    1.7     ±0.0                                -10.4                                     10.4 4520    690__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 9__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   BaO  MnO  MgO  SiO.sub.2No.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                  (mol %)__________________________________________________________________________401   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0  2.0402   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0  2.0 403* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0  2.0 404* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0  2.0405   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0  2.0406   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  1.0  2.0  2.0407   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0  2.0408   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0  2.0 409* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.0  2.0410   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.0  2.0411   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0  2.0 412* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  1.5  2.0  2.0413   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  3.0  3.0414   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.0  3.0  3.0 415* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  3.5  3.0  3.0416   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.3  3.0  3.0 417* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.1  3.0  3.0418   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  3.0419   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  5.0 420* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  6.0421   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  0.5422   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  0.3 423* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.5  2.0  0.1 424* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.4  1.0425   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  0.6  1.0426   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  3.0  1.0427   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  4.0  1.0428   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  5.0  1.0 429* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  6.0  1.0 430* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  1.0  1.0 431* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  1.0  1.0  1.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 10__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRIC            INSULATIONSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       RESISTANCENo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         log IR__________________________________________________________________________401   1280      3180    1.8     -10.8                                +1.9 10.8                                         11.8402   1280      3390    1.7     -8.9 -1.8 8.9 11.7 403* 1300      3430    1.8     -14.6                                +20.7                                     32.4                                         11.6 404* 1260      2940    1.6     -7.8 -1.3 7.8 10.5405   1260      3260    1.7     -8.9 +3.5 8.9 11.8406   1260      3260    1.5     -9.6 -0.8 9.6 11.6407   1260      3130    1.6     -10.7                                +3.2 10.7                                         11.6408   1280      3190    1.7     -9.9 +3.4 9.9 11.7 409* unmeasurable as being semiconductive410   1300      3280    1.8     -10.9                                +2.7 10.9                                         11.6411   1300      3090    1.8     -10.9                                -5.2 10.9                                         11.3 412* unmeasurble as not sintered enough at 1360° C.413   1280      3190    1.8     -7.2 +9.1 9.6 11.6414   1260      3210    1.7     -6.9 +7.6 8.4 11.5 415* 1260      3010    1.8     -3.4 +8.8 9.2 9.5416   1280      3110    1.7     -9.7 +0.3 9.7 11.6 417* 1280      2940    8.9     -11.2                                -3.8 11.2                                         8.1418   1260      3120    1.6     -8.9 +2.8 8.9 11.7419   1260      3050    1.7     -8.6 +2.9 8.6 11.3 420* 1280      2680    1.6     -9.6 -6.8 10.2                                         11.1421   1280      3230    1.7     -8.4 +4.1 8.4 11.4422   1300      3290    1.6     -11.2                                +1.8 11.2                                         11.2 423* 1360      3010    1.8     -12.9                                +3.6 12.9                                         11.1 424* 1280      3160    1.7     -17.3                                -4.2 17.3                                         10.6425   1280      3170    1.6     -10.8                                -4.6 10.8                                         11.5426   1300      3240    1.8     -4.1 -9.2 9.2 11.5427   1280      3160    1.7     -7.6 +4.8 7.6 11.4428   1280      3040    1.6     -9.3 +2.8 9.3 11.2 429* 1280      2820    1.6     -7.8 +2.9 7.9 10.2 430* 1280      2640    1.7     -6.7 +3.3 9.8 11.3 431* 1280      2480    1.6     -7.3 +3.7 10.8                                         11.2__________________________________________________________________________  *indicates out of the scope of the invention 
    
     
                                           TABLE 11__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              Co.sub.2 O.sub.3                   BaO  MnO  NiO Al.sub.2 O.sub.3                                      MgONo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                 (mol %)__________________________________________________________________________501   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  0.3  NiO 1.0  1.0502   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  0.3  NiO 1.0  1.0 503* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  0.3  NiO 1.0  1.0 504* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  0.3  NiO 1.0  1.0505   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  0.3  NiO 1.0  1.0506   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  0.3  NiO 1.0  2.0507   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  0.5  Al.sub.2 O.sub.3                                 1.0  2.0508   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  0.5  Al.sub.2 O.sub.3                                 1.0  2.0 509* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  0.5  Al.sub.2 O.sub.3                                 1.0  2.0510   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  0.5  Al.sub.2 O.sub.3                                 1.0  2.0511   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  0.5  Al.sub.2 O.sub.3                                 1.0  2.0 512* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  0.5  Al.sub.2 O.sub.3                                 1.0  2.0513   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  1.5  NiO 0.5  3.0514   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.0  NiO 0.5  3.0 515* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  NiO 0.5  3.0516   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.2  NiO 0.5  3.0 517* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.1  NiO 0.5  3.0 518* 97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 0.2  2.5519   97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 2.0  2.5520   97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 3.0  2.5 521* 97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 3.5  2.5 522* 97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  Al.sub.2 O.sub.3                                 3.5  2.5523   96.5 Ho.sub.2 O.sub.3          2.0 1.5  1.5  1.0  Al.sub.2 O.sub.3                                 1.5  2.0 524* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  Al.sub.2 O.sub.3                                 1.5  0.2 525* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  Al.sub.2 O.sub.3                                 1.5  0.4526   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  3.0527   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  4.0528   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  5.0 529* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  6.0 530* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.0  1.0 531* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.0  1.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 12__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRICSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       log IRNo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         25° C.                                             125° C.__________________________________________________________________________501   1320      3090    1.6     -11.2                                +4.3 11.2                                         11.7                                             10.5502   1320      3160    1.5     -9.8 -0.9 9.8 11.8                                             10.4 503* 1320      3340    1.7     -16.1                                +17.1                                     42.3                                         11.6                                             10.5 504* 1360      2820    1.6     -8.3 -1.9 8.3 10.9                                             9.3505   1340      3180    1.7     -10.9                                +2.2 10.9                                         11.8                                             10.2506   1320      3260    1.4     -10.3                                -0.8 10.3                                         11.6                                             10.6507   1320      3200    1.7     -11.2                                +2.1 11.2                                         11.5                                             10.2508   1320      3090    1.8     -10.9                                +4.1 10.9                                         11.7                                             10.3 509* unmeasurable as being semiconductive510   1360      3160    1.4     -12.3                                -3.3 12.3                                         11.6                                             10.3511   1360      3140    1.5     -10.4                                -4.8 10.4                                         11.7                                             10.4  512* unmeasurble as not sintered enough at 1360° C.513   1320      3180    1.6     -8.1 +8.4 9.8 11.8                                             10.3514   1320      3260    1.7     -7.6 +8.1 8.1 11.7                                             10.2 515* 1320      3080    1.7     -6.8 +4.1 9.8 10.6                                             8.3516   1340      3200    1.8     -9.1 +1.2 9.1 11.8                                             10.4 517* 1340      3050    6.8     -21.9                                -3.8 21.9                                         8.9 6.1 518* 1320      3130    3.8     -14.1                                +2.8 14.1                                         8.8 6.5519   1320      3240    1.8     -10.1                                +5.1 10.1                                         11.6                                             10.2520   1300      3170    1.6     -9.8 +4.2 9.8 11.7                                             10.3 521* 1300      3120    1.7     -6.2 +2.5 6.2 9.5 6.7 522* 1360      2780    2.3     -7.9 +3.9 7.9 10.9                                             9.8523   1360      3180    1.6     -9.1 +3.5 9.1 11.9                                             10.4 524* 1320      3190    1.5     -15.3                                -3.6 15.3                                         10.9                                             9.8 525* 1320      3230    1.5     -15.1                                -8.6 15.1                                         11.2                                             10.1526   1360      3120    1.4     -6.2 -6.9 9.8 11.8                                             10.3527   1360      3070    1.6     -4.6 -5.8 7.1 11.7                                             10.2528   1360      3040    1.8     -4.3 -4.5 8.6 11.6                                             10.1 529* 1360      2910    1.9     -3.1 -7.6 7.6 11.0                                             9.4 530* 1320      2680    1.6     -9.7 +4.8 9.7 11.7                                             10.2 531* 1320      2510    1.7     -8.5 +3.7 10.2                                         11.6                                             10.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 13__________________________________________________________________________SAMPLE BaTiO.sub.2      Re.sub.2 O.sub.3              Co.sub.2 O.sub.3                   BaO  MnO  NiO, Al.sub.2 O.sub.3                                      MgO  OXIDE GLASSNo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)  (mol %)                                           (wt parts)__________________________________________________________________________601   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  0.3  NiO 1.0  1.0  1.0602   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  0.3  NiO 1.0  1.0  1.0 603* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  0.3  NiO 1.0  1.0  1.0 604* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  0.3  NiO 1.0  1.0  1.0605   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  0.3  NiO 1.0  1.0  1.0606   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  0.3  NiO 1.0  2.0  1.0607   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  0.5  Al.sub.2 O.sub.3                                 1.0  2.0  1.0608   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  0.5  Al.sub.2 O.sub.3                                 1.0  2.0  1.0 609* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  0.5  Al.sub.2 O.sub.3                                 1.0  2.0  1.0610   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  0.5  Al.sub.2 O.sub.3                                 1.0  2.0  1.0611   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  0.5  Al.sub.2 O.sub.3                                 1.0  2.0  1.0 612* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  0.5  Al.sub.2 O.sub.3                                 1.0  2.0  1.0613   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  1.5  NiO 0.5  3.0  1.0614   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.0  NiO 0.5  3.0  1.0 615* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  NiO 0.5  3.0  1.0616   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.2  NiO 0.5  3.0  1.0 617* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  0.1  NiO 0.5  3.0  1.0 618* 97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 0.2  2.5  1.5619   97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 2.0  2.5  1.5620   97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 3.0  2.5  1.5 621* 97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  NiO 3.5  2.5  1.5 622* 97.0 Ho.sub.2 O.sub.3          1.5 1.5  1.5  0.5  Al.sub.2 O.sub.3                                 3.5  2.5  1.5623   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.0  Al.sub.2 O.sub.3                                 1.5  2.0  2.0 624* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.0  Al.sub.2 O.sub.3                                 1.5  2.0  3.0625   96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.0  Al.sub.2 O.sub.3                                 1.5  2.0  0.5 626* 96.5 Er.sub.2 O.sub.3          2.0 1.5  1.5  1.0  Al.sub.2 O.sub.3                                 1.5  2.0  0.3 627* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  Al.sub.2 O.sub.3                                 1.5  0.2  1.0 628* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  Al.sub.2 O.sub.3                                 1.5  0.4  1.0629   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  3.0  1.0630   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  4.0  1.0631   96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  5.0  1.0 532* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.5  6.0  1.0 633* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.0  1.0  1.0 634* 96.0 Dy.sub.2 O.sub.3          1.5 2.5  1.5  0.3  NiO 1.0  1.0  1.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 14__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRICSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       log IRNo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         25° C.                                             125° C.__________________________________________________________________________601   1250      3180    1.8     -10.6                                +3.5 10.6                                         12.8                                             11.0602   1250      3390    1.7     -9.6 -0.8 9.6 12.6                                             10.9 603* 1250      3280    1.8     -15.8                                +16.6                                     41.2                                         12.7                                             10.8 604* 1280      2790    1.7     -7.9 -1.2 7.9 11.8                                             9.8605   1230      3240    1.7     -10.5                                +1.9 10.5                                         12.6                                             10.8606   1230      3300    1.6     -10.1                                -0.3 10.1                                         12.7                                             11.0607   1230      3180    1.8     -10.8                                +1.8 10.8                                         12.6                                             10.7608   1250      3120    1.9     -10.2                                +3.6 10.2                                         12.6                                             10.8 609* unmeasurable as being semiconductive610   1280      3210    1.6     -21.1                                -2.9 12.1                                         12.4                                             10.8611   1280      3110    1.8     -10.7                                -4.5 10.7                                         12.5                                             10.9  612* unmeasurable as not sintered enough at 1360° C.613   1250      3140    1.7     -7.0 +8.5 9.4 12.7                                             10.7614   1230      3290    1.7     -7.3 +8.4 8.4 12.6                                             10.5 615* 1230      3060    1.6     -6.5 +3.5 9.2 11.2                                             8.7616   1250      3190    1.7     -8.6 +0.4 8.6 12.7                                             10.8 617* 1250      3030    9.1     -22.6                                -3.6 22.6                                         9.3 6.3 618* 1280      3150    6.4     -14.7                                +2.8 14.7                                         8.7 6.5619   1250      3210    1.9     -10.8                                +4.2 10.8                                         12.4                                             10.6620   1230      3190    1.7     -9.7 +2.8 9.7 12.5                                             10.8 621* 1230      3150    1.8     -8.7 +2.5 8.7 9.8 6.9 622* 1300      2890    2.6     -9.2 +3.9 9.2 11.8                                             10.1623   1250      3180    1.7     -8.8 +3.2 8.8 12.7                                             10.7 624* 1230      2860    1.6     -8.0 +3.8 8.0 12.5                                             10.1625   1280      3150    1.8     -10.8                                -6.8 10.8                                         12.6                                             10.6 626* 1360      3130    1.6     -11.6                                -7.7 11.6                                         11.7                                             10.0 627* 1250      3160    1.6     -17.1                                -3.6 17.8                                         11.6                                             10.1 628* 1250      3170    1.7     -15.6                                -8.6 15.8                                         11.8                                             10.2629   1280      3220    1.6     -5.6 -6.8 9.2 12.4                                             10.8630   1250      3120    1.7     -5.0 -5.8 7.4 12.2                                             10.6631   1250      3040    1.6     -4.2 -3.5 9.6 12.3                                             10.6 632* 1280      2890    1.5     -3.1 -9.6 9.6 11.6                                             9.7 633* 1250      2630    1.6     -9.1 +3.5 9.1 12.2                                             10.6 634* 1250      2450    1.7     -8.0 +3.7 10.6                                         12.1                                             10.3__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 15__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   CaO  MnO  MgO  OXIDE GLASSNo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                  (wt parts)__________________________________________________________________________701   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0  1.0702   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0  1.0 703* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0  1.0 704* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0  1.0705   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0  1.0706   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  1.0  2.0  1.0707   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0  1.0708   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0  1.0 709* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.0  1.0710   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.0  1.0711   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0  1.0 712* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  1.5  2.0  1.0713   97.5 Tb.sub.2 O.sub.3          1.0 1.5  1.5  2.5  3.0  1.5714   97.5 Tb.sub.2 O.sub.3          1.0 1.5  2.0  3.0  3.0  1.5 715* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  2.0  3.5  3.0  1.5716   97.5 Tb.sub.2 O.sub.3          1.0 1.5  2.0  0.3  3.0  1.5 717* 97.5 Tb.sub.2 O.sub.3          1.0 1.5  2.0  0.1  3.0  1.5718   96.5 Er.sub.2 O.sub.3          2.0 1.5  2.0  1.5  2.0  2.0 719* 96.5 Er.sub.2 O.sub.3          2.0 1.5  2.0  1.5  2.0  3.0720   96.5 Er.sub.2 O.sub.3          2.0 1.5  2.0  1.5  2.0  0.5 721* 96.5 Er.sub.2 O.sub.3          2.0 1.5  2.0  1.5  2.0  0.3 722* 98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  0.2  1.5 723* 98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  0.4  1.5724   98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  3.0  1.5725   98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  4.0  1.5726   98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  5.0  1.5 727* 98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  6.0  1.5 728* 98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  1.0  1.5 729* 98.0 Dy.sub.2 O.sub.3          1.5 0.5  1.5  1.0  1.0  1.5__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 16__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRIC            INSULATIONSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       RESISTANCENo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         log IR__________________________________________________________________________701   1280      3120    1.6     -6.8 -3.2 9.7 12.5702   1280      3390    1.7     -7.6 -3.3 8.6 12.6 703* 1300      3360    1.6     -10.6                                +24.4                                     24.4                                         12.6 704* 1300      2810    1.6     -9.8 -6.6 9.8 11.8705   1280      3280    1.7     -9.4 -3.3 9.4 12.6706   1280      3240    1.6     -9.8 -1.3 9.8 12.6707   1280      3210    1.8     -11.8                                -3.8 11.8                                         12.5708   1280      3170    1.6     -10.6                                -4.8 10.6                                         12.6 709* unmeasurable as being semiconductive710   1300      3230    2.0     -10.6                                -4.7 10.8                                         12.2711   1300      3070    2.1     -9.7 -5.2 9.7 12.1 712* unmeasurable as not sintered enough at 13602  C.713   1260      3180    1.7     -7.8 -4.6 8.6 12.4714   1260      3220    1.6     -5.4 -7.4 8.4 12.1 715* 1260      3070    1.8     -3.4 -9.2 9.2 11.1716   1280      3190    1.7     -9.6 -3.3 9.6 12.2 717* 1280      2950    8.7     -20.6                                -3.6 20.6                                         9.4718   1260      3090    1.6     -9.1 -4.3 9.1 12.6 719* 1260      2890    1.7     -7.8 -3.8 8.8 12.4720   1300      3160    1.7     -9.8 -6.8 9.8 12.5 721* 1360      3130    1.8     -8.3 -3.1 9.6 11.4 722* 1280      3130    1.6     -17.6                                -4.1 17.6                                         11.7 723* 1280      3220    1.6     -14.8                                -7.1 14.8                                         11.9724   1300      3220    1.7     -7.8 -9.2 9.2 12.5725   1280      3170    1.7     -7.4 -6.8 9.4 12.3726   1280      3030    1.7     -8.6 -5.8 8.6 12.2 727* 1280      2860    1.6     -8.2 -3.6 9.2 11.6 728* 1280      2630    1.7     -7.2 -3.3 9.8 12.2 729* 1280      2460    1.6     -7.0 -3.7 8.9 12.0__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 17__________________________________________________________________________SAMPLE BaTiO.sub.3      Re.sub.2 O.sub.3              CO.sub.2 O.sub.3                   SrO  MnO  MgO  OXIDE GLASSNo.   (mol %)      (mol %) (mol %)                   (mol %)                        (mol %)                             (mol %)                                  (wt parts)__________________________________________________________________________801   97.0 Dy.sub.2 O.sub.3          1.5 1.5  1.5  1.0  1.0  1.0802   99.0 Dy.sub.2 O.sub.3          0.5 0.5  1.5  1.0  1.0  1.0 803* 99.6 Dy.sub.2 O.sub.3          0.2 0.2  1.5  1.0  1.0  1.0 804* 90.0 Dy.sub.2 O.sub.3          5.0 5.0  1.5  1.0  1.0  1.0805   93.0 Dy.sub.2 O.sub.3          3.0 4.0  1.5  1.0  1.0  1.0806   97.5 Ho.sub.2 O.sub.3          1.5 1.0  2.0  1.0  2.0  1.5807   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.5  1.5  2.0  1.5808   96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.3  1.5  2.0  1.5 809* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  0.1  1.5  2.0  1.5810   96.5 Ho.sub.2 O.sub.3          1.5 2.0  3.0  1.5  2.0  1.5811   96.5 Ho.sub.2 O.sub.3          1.5 2.0  4.0  1.5  2.0  1.5 812* 96.5 Ho.sub.2 O.sub.3          1.5 2.0  5.0  1.5  2.0  1.5813   98.5 Tb.sub.2 O.sub.3          1.0 0.5  1.5  2.5  3.0  1.0814   98.5 Tb.sub.2 O.sub.3          1.0 0.5  1.5  3.0  3.0  1.0 815* 98.5 Tb.sub.2 O.sub.3          1.0 0.5  1.5  3.5  3.0  1.0816   98.5 Tb.sub.2 O.sub.3          1.0 0.5  1.5  0.3  3.0  1.0 817* 98.5 Tb.sub.2 O.sub.3          1.0 0.5  1.5  0.1  3.0  1.0818   96.0 Er.sub.2 O.sub.3          2.0 2.0  1.5  1.5  2.0  2.0 819* 96.0 Er.sub.2 O.sub.3          2.0 2.0  1.5  1.5  2.0  3.0820   96.0 Er.sub.2 O.sub.3          2.0 2.0  1.5  1.5  2.0  0.5 821* 96.0 Er.sub.2 O.sub.3          2.0 2.0  1.5  1.5  2.0  0.3 822* 97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  0.2  1.5 823* 97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  0.4  1.5824   97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  3.0  1.5825   97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  4.0  1.5826   97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  5.0  1.5 827* 97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  6.0  1.5 828* 97.5 Dy.sub.2 O.sub.3          1.5 1.0  1.5  1.0  1.0  1.5 829* 97.5 Dy.sub. 2 O.sub.3          1.5 1.0  1.5  1.0  1.0  1.5__________________________________________________________________________ *indicates out of the scope of the invention 
    
     
                                           TABLE 18__________________________________________________________________________ FIRING    DIELECTRIC                   DIELECTRIC            INSULATIONSAMPLE TEMPERATURE           CONSTANT                   LOSS    TCC (%)       RESISTANCENo.   (°C.)           ε                   tan δ (%)                           -55° C.                                +125° C.                                     C.sub.MAX                                         log IR__________________________________________________________________________801   1280      3260    1.7     +2.6 -6.7 8.3 12.5802   1280      3390    1.8     +3.1 -2.5 7.6 12.6 803* 1300      3380    1.5     -13.6                                +26.7                                     43.5                                         12.6 804* 1280      2780    1.8     +2.8 -3.6 8.8 11.7805   1280      3190    1.8     +3.2 -3.8 9.4 12.4806   1280      3270    1.7     +1.6 -3.5 8.4 12.6807   1260      3290    1.8     +2.2 -6.7 12.7                                         12.5808   2160      3180    1.7     +0.8 -5.6 9.8 12.6 809* unmeasurable as being semiconductive810   1300      3090    1.9     +1.6 -3.6 7.8 12.4811   1300      3030    1.9     +2.3 -7.7 11.6                                         12.2 812* unmeasurable as not sintered enough at 1360° C.813   1280      3310    1.7     +3.2 -8.6 11.8                                         12.4814   1260      3260    1.8     +3.6 -8.3 12.1                                         12.3 815* 1260      3030    1.8     +3.9 -8.5 12.4                                         10.3816   1280      3210    1.6     +2.1 -6.1 8.2 12.5 817* 1280      3360    16.7    -3.6 -6.3 9.1 8.6818   1260      3040    1.7     +2.1 -4.4 8.6 12.3 819* 1260      2810    1.8     +3.0 -4.7 8.8 12.1820   1300      3410    1.7     +2.2 -7.2 10.3                                         12.5 821* 1360      3310    1.9     +1.9 -8.8 10.7                                         11.4 822* 1280      3210    1.4     -16.3                                -8.6 16.3                                         11.6 823* 1280      3170    1.4     -14.9                                -7.7 14.9                                         11.8824   1280      3200    1.7     +2.7 -7.8 10.6                                         12.4825   1280      3130    1.7     +3.2 -8.2 11.7                                         12.3826   1300      3110    1.6     +3.6 -8.6 12.4                                         12.1 827* 1280      2830    1.8     +3.8 -9.0 12.7                                         11.6 828* 1280      2780    1.7     +2.7 -6.0 8.6 12.5 829* 1280      2660    1.6     +2.9 -6.2 8.9 12.3__________________________________________________________________________ *indicates out of the scope of the invention 
    
     Although the present invention has been described in relation to particular embodiments thereof, many other variations and modifications and other uses will become apparent to those skilled in the art. It is preferred, therefore, that the present invention be limited not by the specific disclosure herein, but only by the appended claims.