DESCRIPTION OF THE PREFERRED EMBODIMENTS

[0020] A dielectric ceramic composition of the present invention will be described in detail below.

[0021] The dielectric ceramic composition of the present invention is characterized by containing a glass component in an amount of 5 to 150 parts by weight based on 100 parts by weight of the main component represented by the formula: xZn ₂ TiO ₄ -(1−x)ZnTiO ₃ -yTiO ₂ , wherein x satisfies 0<x<1 and y satisfies 0≦y≦0.5.

[0022] The composition wherein x satisfies 0<x<1 achieves the absolute value of temperature coefficient τ _f of resonant frequency of 60 ppm/° C. or less, the dielectric constant ε _r of 8 to 30 and high Qxf value, for example greater than 1500 GHz. It is preferable that x satisfies 0.02<x<0.98.

[0023] If y is more than 0.5, the composition is not preferable because τ _f is more than +60 ppm/° C. In the dielectric ceramic composition of the present invention, if the glass component is contained in an amount of less than 5 parts by weight based on 100 parts by weight of the main component served as the ceramic matrix material, the sintering temperature becomes high, whereas if it is contained in excess of 150 parts by weight, the glass is liable to elute to react with a setter which is used in sintering. The glass component is preferably contained in an amount of 9 to 120 parts by weight based on 100 parts by weight of the main component.

[0024] The Zn ₂ TiO ₄ for use in the present invention can be obtained by mixing zinc oxide (ZnO) and titanium oxide (TiO ₂ ) in a molar ratio of 2:1 and calcining the mixture. The ZnTiO ₃ can be obtained by mixing ZnO and TiO ₂ in a molar ratio of 1:1 and calcining the mixture. As starting materials of Zn ₂ TiO ₄ and ZnTiO ₃ , nitrate, carbonate, hydroxide, chloride and an organic metal compound each turning into an oxide of zinc or titanium at the time of calcining, may also be used, in addition to TiO ₂ and ZnO.

[0025] The dielectric ceramic composition of the present invention is characterized by containing a glass component in a predetermined amount. The glass used herein as the glass component means an amorphous solid substance obtained by fusion. A crystallized glass partially containing a crystallized substance in a glass is also included in the glass. The solid substance includes an inorganic substance comprising an oxide and examples of the glass for use in the present invention include a PbO-base glass, a ZnO-base glass, a SiO ₂ -base glass and a glass comprising metal oxides. The PbO-base glass is a glass containing PbO, and examples thereof include a glass containing PbO—SiO ₂ , PbO—B ₂ O ₃ or PbO—P ₂ O ₅ , or a glass containing R ₂ O—PbO—SiO ₂ , R ₂ O—CaO—PbO—SiO ₂ , R ₂ O—ZnO—PbO—SiO ₂ or R ₂ O—Al ₂ O ₃ —PbO—SiO ₂ (herein. R is Na or K). The ZnO-base glass is a glass containing ZnO, and examples thereof include a glass containing ZnO—Al ₂ O ₃ —BaO-SiO ₂ or ZnO—Al ₂ O ₃ —R ₂ O—SiO ₂ . The SiO ₂ -base glass is a glass containing SiO ₂ , and examples thereof include a glass containing SiO ₂ —Al ₂ O ₃ —R ₂ O or SiO ₂ —Al ₂ O ₃ —BaO.

[0026] As the glass for use in the present invention, in addition to the PbO-base glass, the ZnO-base glass and the SiO ₂ -base glass, a glass comprising various metal oxides can also be used, and examples thereof include a glass comprising two or more metal oxides selected from the group consisting of PbO, ZnO, Bi ₂ O ₃ , BaO, B ₂ O ₃ , SiO ₂ , ZrO ₂ , TiO ₂ , Al ₂ O ₃ , CaO ad SrO. Either an amorphous glass or a crystalline glass may be used as the glass. If the glass contains PbO, the sintering temperature is liable to lower, however, the unloaded Q-value is liable to decrease and therefore, the content of the PbO component in the glass is preferably 40% by weight or less. A glass containing a SiO ₂ component and an Al ₂ O ₃ component in a glass at the same time (namely, SiO ₂ —-Al ₂ O ₃ base glass) is more preferably used as the glass for use in the present invention. In the present invention, ZnO—Al ₂ O ₃ —BaO—SiO ₂ is most preferably used in that a high unloaded Q-value can be obtained.

[0027] According to the present invention, a glass component is incorporated in an amount of 5 to 150 parts by weight based on 100 parts by weight of the main component represented by the formula: xZn ₂ TiO ₄ -(1−x)ZnTiO ₃ -yTiO ₂ , wherein x satisfies 0<x<1 and y satisfies 0≦y≦0.5, whereby a dielectric ceramic composition having such characteristics that a low temperature sintering can be performed at the sintering temperature of 800 to 1000° C., the dielectric constant ε _r is on the order of from 8 to 30, the unloaded Q-value is large, for le Qxf being 1500 GHz or more, and the absolute value of temperature coefficient τ _f of resonant frequency is 60 ppm/° C. or less, can be obtained.

[0028] In the present invention, before the sintering, Zn ₂ TiO ₄ , ZnTiO ₃ , TiO ₂ and glass particles are each independently pulverized and mixed with each other, or respective starting material particles are mixed and pulverized, and when these starting material particles before the sintering have an average particle size of less than 5 μm, preferably 1 μm or less, the sintering at a lower temperature can be performed. However, if the average particle size is excessively reduced, the treating may become difficult and therefore, the average particle size is preferably 0.05 μm or more.

[0029] In the present invention, further, CuO is incorporated into the dielectric ceramic composition as a side component to produce a dielectric ceramic composition containing a glass component in an amount of 5 to 150 parts by weight and CuO in an amount of 40 parts by weight or less, based on 100 parts by weight of the main component represented by the formula: xZn ₂ TiO ₄ -(1−x)ZnTiO ₃ -yTiO ₂ , wherein x satisfies 0<x<1 and y satisfies 0≦y≦0.5, whereby the sintering temperature can be more lowered without deteriorating various characteristics described above. If the CuO is incorporated in excess of 40 parts by weight based on 100 parts by weight of the main component, the composition is not preferable because τ _f is reduced to less than −60 ppm/° C. The CuO is preferably in an amount of 2.5 parts by weight or more based on 100 parts by weight of the main component.

[0030] In the present invention, also, MnO is similarly incorporated into the dielectric ceramic composition as a side component to produce a dielectric ceramic composition containing a glass component in an amount of 5 to 150 parts by weight and MnO in an amount of 30 parts by weight, based on 100 parts by weight of the main component represented by the formula: xZn ₂ TiO ₄ -(1−x)ZnTiO ₃ -yTiO ₂ , wherein x satisfies 0<x<1 and y satisfies 0≦y≦0.5, whereby the sintering temperature can be similarly lowered without deteriorating various properties described above. If the MnO is incorporated in excess of 30 parts by weight based on 100 parts by weight of the main component, the component is not preferable because the Q-value is reduced. The MnO is preferably in an amount of 2.5 parts by weight or more based on 100 parts by weight of the main component.

[0031] The CuO or the MnO, which is added as the side component, may be added individually or both of the components may be added in combination.

[0032] The production method of the dielectric ceramic composition of the present invention is described below.

[0033] The dielectric ceramic composition can be produced by preparing a calcined powder comprising Zn ₂ TiO ₄ and ZnTiO ₃ by calcination of a first mixture of ZnO powder and TiO ₂ powder, and sintering a second mixture of the calcined powder and a glass component in an amount of 5 to 150 parts by weight based on 100 parts by weight of the calcined powder at a temperature of 800 to 1000° C. The second mixture may contain TiO ₂ powder. The second mixture may further contain CuO in an amount of 40 parts by weight or less based on 100 parts by weight of the calcined powder. The second mixture may further contain MnO in an amount of 30 parts by weight or less based on 100 parts by weight of the calcined powder.

[0034] More detailed description will be provided hereinafter.

[0035] Titanium oxide (TiO ₂ ) and zinc oxide (ZnO) are weighed in a predetermined molar ratio and wet-mixed together with a solvent such as water or an alcohol. Subsequently, after removing the water, the alcohol or the like, the resulting mixture is pulverized and calcined at from 900 to 1200° C. on the order of from about 1 to 5 hours in an oxygen-containing atmosphere (for example, air atmosphere. The Zr ₂ TiO ₄ , ZnTiO ₃ and a glass, and, if desired, TiO ₂ , CuO or MnO are weighed in a predetermined ratio and then, wet-mixed together with a solvent such as water or an alcohol. Subsequently, after removing the water, the alcohol or the like, the resulting mixture is pulverized to produce a starting material powder.

[0036] ZnTiO ₃ is prepared as the starting material powder in case of the above predetermined molar ratio of TiO ₂ :ZnO=1:1, while Zn ₂ TiO ₄ is prepared as the starting material powder in case of the above predetermined molar ratio of TiO ₂ :ZnO=1:2.

[0037] That is, titanium oxide (TiO ₂ ) and zinc oxide (ZnO) are weighed in a molar ratio of 1:2 and wet-mixed together with a solvent such as water or an alcohol. Subsequently, after removing the water, the alcohol or the like, the resulting mixture is pulverized and calcined at from 900 to 1200° C. on the order of from about 1 to 5 hours in an oxygen-containing atmosphere (for example, air atmosphere). The thus-obtained calcined powder is Zn ₂ TiO ₄ . Then, titanium oxide (TiO ₂ ) and zinc oxide (ZnO) are weighed in a molar ratio of 1:1 to produce ZnTiO ₃ by the same production method as in Zn ₂ TiO ₄ . The Zn ₂ TiO ₄ , ZnTiO ₃ and a glass, and, if desired, TiO ₂ , CuO or MnO are weighed in a predetermined ratio and then, wet-mixed together with a solvent such as water or an alcohol. Subsequently, after removing the water, the alcohol or the like, the resulting mixture is pulverized to produce a starting material powder.

[0038] In case that the above predetermined molar ratio of TiO ₂ :ZnO is a value between 1:1 and 1:2, i.e. TiO ₂ :ZnO=1:Z (wherein Z satisfies 1<Z<2), ZnTiO ₃ and Zn ₂ TiO ₄ are simultaneously produced with a molar ratio (ZnTiO ₃ /Zn ₂ TiO ₄ ) of (2−Z)/(Z−1). In this case, the ZnTiO ₃ and Zn ₂ TiO ₄ can be obtained simultaneously with desired ratio by one step calcination.

[0039] Instead of obtaining the ZnTiO ₃ and Zn ₂ TiO ₄ simultaneously with desired ratio by using the mixture of TiO ₂ and ZnO with their predetermined amounts calculated in advance, the calcined powder of ZnTiO ₃ and the calcined powder of Zn ₂ TiO ₄ may be produced respectively and these calcined powders may be mixed with a glass, and, if desired, TiO ₂ , CuO or MnO.

[0040] The dielectric ceramic composition of the present invention is evaluated in a pellet form on the dielectric properties. Specifically, in the above-described starting material powder, an organic binder such as polyvinyl alcohol is mixed. The mixture is rendered uniform, dried and pulverized, followed by molding under pressure (pressure: on the order of from 100 to 1000 kg/cm ² ) into a pellet form. The molded product obtained is sintered at from 800 to 1000° C. in an oxygen-containing gas atmosphere such as air atmosphere, whereby a pellet of dielectric ceramic composition where a Zn ₂ TiO ₄ phase, a ZnTiO ₃ phase and a glass phase are present together, can be obtained. A TiO ₂ phase may be present in the pellet.

[0041] If desired, the dielectric ceramic composition is processed to a proper shape and size, formed to a sheet by the doctor blade method and laminated by using the sheet and electrodes, whereby the composition may be used as materials for various laminated ceramic parts. Examples of the laminated ceramic parts include a laminated ceramic capacitor, an LC filter, a dielectric resonator and a dielectric substrate.

[0042] The laminated ceramic parts of the present invention comprises a plurality of dielectric layers, an internal electrode formed between the dielectric layers and an external electrode electrically connected to the internal electrode, wherein the dielectric layer is constituted of dielectric ceramics obtained by sintering the dielectric ceramic composition and the internal electrode is made of elemental Cu or elemental Ag, or an alloy material mainly comprising Cu or Ag. The laminated ceramic parts of the present invention can be obtained by laminating the dielectric layers each containing the dielectric ceramic composition and a layer of elemental Cu, elemental Ag or an alloy material mainly comprising Cu or Ag, and simultaneously sintering then.

[0043] Examples of one embodiment of the laminated ceramic parts include a tri-plate type resonator shown in FIGS. 1 and 2 .

[0044] FIG. 1 is a perspective view showing the tri-plate type resonator as one embodiment according to the present invention, and FIG. 2 is a cross-sectional view of the resonator. As shown in FIGS. 1 and 2 , the tri-plate type resonator is laminated ceramic parts comprising a plurality of dielectric layers 1 , an internal electrode 2 formed between the dielectric layers and an external electrode 3 electrically connected to the internal electrode. The internal electrode 2 is disposed at the center of the laminated dielectric layers 1 . As shown in FIGS. 1 and 2 , the internal electrode 2 is formed so as to pass through the resonator from a first face A to a second face B opposing the first face A. The first face A is an open face, while the second face B is a closed face. That is, five faces of the resonator including the second face B exclusive of the first face A are covered by an external electrode 3 , and the internal electrode 2 and the external electrode 3 are connected to each other on the second face B. The material of the internal electrode 2 Comprises Cu or Ag, or mainly comprises Cu or Ag. When the dielectric ceramic composition of the present invention is used, the sintering can be performed at a low temperature and therefore, these materials for the internal electrode can be used.

EXAMPLE 1

[0045] 0.33 mol of titanium oxide (TiO ₂ ) and 0.66 mol of zinc oxide (ZnO) were charged into a ball mill together with ethanol and wet-mixed for 12 hours. After removing the solvent from the solution, the resulting mixture was pulverized and calcined in an air atmosphere of 1000° C. to obtain a Zn ₂ TiO ₄ calcined powder Then, 0.5 mol of TiO ₂ and 0.5 mol of ZnO were wet-mixed and calcined in the same method to obtain a ZnTiO ₃ calcined powder. The Zn ₂ TiO ₄ calcined powder, the ZnTiO ₃ calcined powder and TiO ₂ powder were prepared in the blended amount shown in Table 1 to serve as a matrix material. To the matrix material, 10 parts by weight of a glass powder comprising 52% by weight of ZnO, 6% by weight of SiO ₂ , 12% by weight of Al ₂ O ₃ and 30% by weight of B ₂ O ₃ were added based on 100 parts by weight of the matrix material, and the mixture was charged into a ball mill, followed by wet-mixing for 24 hours. After removing the solvent from the solution, the resulting mixture was pulverized to an average particle size of 1 μm, To the pulverized product, an appropriate amount of a polyvinyl alcohol solution was added, followed by drying. Thereafter, the resulting pulverized product was molded into a pellet having a diameter of 12 mm and a thickness of 4 mm and the pellet obtained was sintered in an air atmosphere at 900° C. for two hours. The X-ray diffraction diagram of the sintered body produced was shown in FIG. 3 . As shown in FIG. 3 , it is found that a Zn ₂ TiO ₄ phase, a ZnTiO ₃ phase and a TiO ₂ phase are present together also in the sintered body of the dielectric ceramic composition of the present invention.

[0046] The thus-obtained dielectric ceramic composition was processed to a size of 7 mm in diameter and 3 mm in thickness and then, determined on the unloaded Q-value (Q) at the resonant frequency of 7 to 11 GHz, the dielectric constant ε _r and the temperature coefficient τ _f of resonant frequency by the dielectric resonance method. The rests thereof are shown in Table 2. 1

[0047] 2

[0048] Also, to 100 g of a mixture of the matrix material and the glass, 9 g of polyvinyl butyral as a binder, 6 g of dibutylphthalate as a plasticizer, and 60 g of toluene and 30 g of isopropyl alcohol both as a solvent were added to produce a green sheet having a thickness of 100 μm by the doctor blade method. Then, 22 layers of the green sheets were laminated by the thermo compression bonding of applying a pressure of 200 kg/cm ² at a temperature of 65° C. At this time, a layer having been printed with Ag pattern as an internal electrode was disposed such that it was provided at the center in the thickness direction. After sintering the obtained laminated product at 900° C. for two hours, an external electrode was formed to produce a tri-plate type resonator having a size of 4.9 mm in width, 1.7 nm in height and 8.4 mm in length.

[0049] The obtained tri-plate type resonator was evaluated on the unloaded Q-value at a resonant frequency of 2 GHz. As a result, the percentage of contraction or shrinkage was 19% at the sintering temperature of 900° C., the dielectric constant ε _r was 21, the temperature coefficient τ _f of resonant frequency was 0 ppm/° C. and the unloaded Q-value was 210. As such, when the dielectric ceramic composition according to the present invention was used, the tri-plate type resonator having excellent characteristics could be obtained.

EXAMPLES 2 TO 15

[0050] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended amount shown in Table 1 to serve as a matrix material. After blending the matrix material with various glass components in the blended amount shown in Table 1, pellet-form sintered bodies were produced under the same conditions as in Example 1 and evaluated on various Properties in the same method as in Example 1. The results thereof are shown in Table 2.

EXAMPLES 16 And 17

[0051] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended amount shown in Table 1 to serve as a matrix material. After blending the matrix material with various glass components in the blended amount shown in Table 1, the blends were pulverized till the particle sizes were reduced to the average particle size described in Table 1, pellet-form sintered bodies were produced under the same conditions as in Example 1 and evaluated on various properties in the same method as in Example 1. The results thereof are shown in Table 2.

EXAMPLES 18 TO 20

[0052] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended amount shown in Table 1 to serve as a matrix material. After blending the matrix material with MnO and various glass components in the blended amount shown in Table 1, pellet-form sintered bodies were produced under the same conditions as in Example 1 and evaluated on various properties in the same method as in Example 1. The results thereof are shown in Table 2.

EXAMPLES 21 TO 23

[0053] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended amount shown in Table 1 to serve as a matrix material. After blending the matrix material with CuO and various glass components in the blended amount shown in Table 1, pellet-form calcined bodies were produced under the same conditions as in Example 1 and evaluated on various properties in the same method as in Example 1. The results thereof are shown in Table 2.

EXAMPLES 24 AND 25

[0054] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended aunt shown in Table 1 to serve as a matrix material. After blending the matrix material with MnO, CuO and various glasses described in Table 1 in the blended amount shown in Table 1, pellet-form sintered bodies were produced under the same conditions as in Example 1 and evaluated on various properties in the same method as in Example 1. The results thereof were shown in Table 2.

COMPARATIVE EXAMPLES 1 TO 4

[0055] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended amount shown in Table 1 to serve as a matrix material. After blending the matrix material and the glass described in Table 1 in the blended amount shown in Table 1, pellet-form sintered bodies were intended to be produced under the same conditions as in Example 1. However, when the conditions were such that the glass was added in an amount of less than 5 parts by weight based on 100 parts by weight of the matrix material, the sintering was not realized at 1000° C. or less and the sintered bodies were rendered dense when the sintering temperature was elevated up to 1200° C. When the glass was added in excess of 150 parts by weight based on 100 parts by weight of the matrix material, the glass was eluted to react with the setter, as a result, preferable sintered bodies were not obtained. The results thereof are shown in Table 2.

COMPARATIVE EXAMPLES 5

[0056] In the same manner as in Example 1, Zn ₂ TiO ₄ , ZnTiO ₃ and TiO ₂ were blended in the blended amount shown in Table 1 to serve as a matrix material. After blending the matrix material and the glass described in Table 1 in the blended amount shown in Table 1, pellet-form sintered body was produced under the same conditions as in Example 1. However, when the condition was such that the molar ratio y of the TiO ₂ was 0.6, the temperature coefficient τ _f of resonant frequency was more than +60 pp/° C. The results thereof are shown in Table 2.

EXAMPLE 1′

[0057] 0.45 mol of titanium oxide (TiO ₂ ) and 0.55 mol of zinc oxide (ZnO) were charged into a ball mill together with ethanol and wet-red for 12 hours. After removing the solvent from the solution, the resulting mixture was pulverized and calcined in an air atmosphere of 1000° C. to obtain a matrix material. To the matrix material, 10 parts by weight of a glass comprising 52% by weight of ZnO, 6% by weight of SiO ₂ , 12% by weight of Al ₂ O and 30% by weight of B ₂ O ₃ were added based on 100 parts by weight of the matrix material, and the mixture was charged into a ball mill, followed by wet-mixing for 24 hours. After roving the solvent from the solution, the resulting mixture was pulverized to an average particle size of 1 μm. To the pulverized product, an appropriate amount of a polyvinyl alcohol solution was added, followed by drying. Thereafter, the resulting pulverized product was molded into a pellet having a diameter of 12 nm and a thickness of 4 mm and the pellet obtained was sintered in an air atmosphere at 900° C. for two hours. The X-ray diffraction diagram of the-sintered body produced was shown in FIG. 4 . As shown in FIG. 4 , it is found that a Zn ₂ TiO ₄ phase and a ZnTiO ₃ phase are present together in the sintered body of the dielectric ceramic composition of the present invention.

[0058] The thus-obtained dielectric ceramic composition was processed to a size of 7 mm in diameter and 3 mm in thickness and then, determined on the unloaded Q-value (Qxf) at the resonant frequency of 7 to 11 GHz, the dielectric constant ε _r and the temperature coefficient τ _f of resonant frequency by the dielectric resonance method. The results thereof are shown in Table 4. 3

[0059] 4

[0060] Also, to 100 g of a mixture of the matrix material and the glass, 9 g of polyvinyl butyral as a binder, 6 g of dibutylphthalate as a plasticizer, and 60 g of toluene and 30 g of isopropyl alcohol both as a solvent were added to produce a green sheet having a thickness of 100 μm by the doctor blade method. Then, 22 layers of the green sheets were laminated by the thermo compression bonding of applying a pressure of 200 kg/cm ² at a temperature of 65° C. At this time, a layer having been printed with Ag pattern as an internal electrode was disposed such that it was provided at the center in the thickness direction. After sintering the obtained laminated product at 900° C. for two hours, an external electrode was formed to produce a tri-plate type resonator having a size of 4.9 mm in width, 1.7 mm in height and 8.4 mm in length.

[0061] The obtained tri-plate type resonator was evaluated on the unloaded Q-value at a resonant frequency of 2 GHz. As a result, the percentage of contraction or shrinkage was 19% at the sintering temperature of 900° C., the dielectric constant ε _r was 21, the temperature coefficient τ _f of resonant frequency was 0 ppm/° C. and the unloaded Q-value was 210. As such, when the dielectric ceramic composition according to the present invention was used, the tri-plate type resonator having excellent characteristics could be obtained.

EXAMPLES 2′ TO 14′

[0062] In the same manner as in Example 1′, TiO ₂ and ZnO were blended and calcined so that the calcined powders of Zn ₂ TiO ₄ and ZnTiO ₃ were obtained in the blended amount shown in Table 3 after the calcination. After blending the calcined powders used as the matrix material with various glass components in the blended amount shown in Table 3, pellet-form sintered bodies were produced under the same conditions as in Example 1′ and evaluated on various properties in the same method as in Example 1′. The results thereof are shown in Table 4.

EXAMPLES 15′ AND 16′

[0063] In the same manner as in Example 1′, TiO ₂ and ZnO were blended and calcined so that the calcined powers of Zn ₂ TiO ₄ and ZnTiO ₃ were obtained in the blended amount shown in Table 3 after the calcination. After blending the calcined powders used as the matrix material with various glass components in the blended amount shown in Table 3, the blends were pulverized till the particle sizes were reduced to the average particle size described in Table 3, pellet-form sintered bodies were produced under the same conditions as in Example 1′ and evaluated on various properties in the same method as in Example 1′. The results thereof are shown in Table 4.

EXAMPLES 17′ TO 19′

[0064] In the same manner as in Example 1′, Zn ₂ TiO ₄ and ZnTiO ₃ were blended in the blended amount shown in Table 3 to serve as a matrix material. After blending the matrix material with MnO and various glass components in the blended amount shown in Table 3, pellet-form sintered bodies were produced under the same conditions as in Example 1′ and evaluated on various properties in the same method as in Example 1′. The results thereof are shown in Table 4.

EXAMPLES 20′ TO 22′

[0065] In the same manner as in Example 1′, Zn ₂ TiO ₄ and ZnTiO ₃ were blended in the blended amount shown in Table 3 to serve as a matrix material. After blending the matrix material with CuO and various glass components in the blended amount shown in Table 3, pellet-form sintered bodies were produced under the same conditions as in Example 1′ and evaluated on various properties in the same method as in Example 1′. The results thereof are shown in Table 4.

EXAMPLES 23′ and 24′

[0066] In the same manner as in Example 1′, Zn ₂ TiO ₄ and ZnTiO ₃ were blended in the blended amount shown in Table 3 to serve as a matrix material. After blending the matrix material with MnO, CuO and various glass components in the blended amount shown in Table 3, pellet-form sintered bodies were produced under the same conditions as in Example 1′ and evaluated on various properties in the same method as in Example 1′. The results thereof are shown in Table 4.

COMPARATIVE EXAMPLES 1′ TO 4′

[0067] In the same manner as in Example 1′, Zn ₂ TiO ₄ and ZnTiO ₃ were blended in the blended amount shown in Table 3 to serve as a matrix material. After blending the matrix material and the glass described in Table 3 in the blended amount shown in Table 3, pellet-form sintered bodies were intended to be produced under the same conditions as in Example 1′. However, when the conditions were such that the glass was added in an amount of less than 5 parts by weight based on 100 parts by weight of the matrix material, the sintering was not realized at 1000° C. or less and the sintered bodies were rendered dense when the sintering temperature was elevated up to 1200° C. When the glass was added in excess of 150 parts by weight based on 100 parts by weight of the matrix material, the glass was eluted to react with the setter, as a result, preferable sintered bodies were not obtained. The results thereof are shown in Table 4.

[0068] According to the dielectric ceramic composition of the present invention, a dielectric ceramic composition can be provided such that the dielectric constant ε _r is from 8 to 30, the unloaded Q-value is large, and the absolute value of temperature coefficient τ _f of resonant frequency is as small as 60 ppm/° C. or less. Also, the dielectric ceramic composition can be sintered at a temperature of 1000° C. or less and therefore, can be reduced in the electric power cost required for the sintering and moreover, can be sintered simultaneously with a low resistant conductor comprising elemental Cu or elemental Ag, or an alloy material mainly comprising Cu or Ag, so that laminated parts using the low resistant conductor as the internal electrode can be further provided.