A method for manufacturing a dielectric ceramic composition, dielectric ceramic and multilayer high frequency device

Abstract: A dielectric ceramic composition that can be sintered at a low temperature of around 1000°C and also can have a high dielectric constant, a high Q value and small temperature coefficient at a resonant frequency includes a glass component that promotes sintering. The dielectric ceramics include: the main component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 not more than 0.50) within the range of not less than 40 parts by weight nor more than 98 parts by weight; the accessory component comprising at least one selected from SiO 2 and B 2 O 3 within the range of not less than 2 parts by weight nor more than 60 parts by weight; and at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 within the range of not less than 0.1 parts by weight nor more than 10 parts by weight. Consequently, the dielectric ceramic composition of the present invention can be sintered at low temperature. The dielectric ceramic composition also has a stability in composition and high Q value, which can used for the dielectric ceramic and multilayer high frequency device.

Description: This invention relates to dielectric ceramic and multilayer high frequency devices used for various filters and resonators using high frequency. Recently, communication systems using electromagnetic waves in the microwave range, such as automobile phones, portable telephones, satellite broadcasting systems or the like have been developed so that miniaturization of their terminal apparatus have been required. In order to miniaturize the terminal apparatus, each part of apparatus needs to be miniaturized. In such apparatus, the dielectric ceramic is placed in a frequency stabilizing device of various filters and oscillators. When the resonant mode is the same, the size of these resonant devices is inversely proportional to the square root of the dielectric constant (ε r ) of the dielectric materials to be used. Consequently, in order to make miniature resonant devices, materials having a high dielectric constant are needed. Other required properties of the dielectric ceramic include: having a low loss in a microwave range, in other words, having a high Q value; and having a small temperature coefficient at a resonant frequency (τ r ). As a material having a high dielectric constant, a (Pb, Ca) ZrO 3 system is disclosed in Japanese Laid-Open Patent No. (Tokkai-Hei) 4-65021. This system has a high dielectric constant (ε r ) of more than 100, a high Q value of approximately 800 at 2-4 GHz and a small temperature coefficient at a resonant frequency. Meanwhile, attempts have been made to miniaturize resonance devices and to improve the function by making a multilayer structure of conductor and dielectric ceramic. Since a conductor to be used in such a high-frequency range as microwave is required to have a high conductivity, Cu, Au, Ag or an alloy of them need to be used. In the case of making the dielectric ceramic multilayer structure, dielectric ceramic is required to be burned at the same time when the conductive metal is burned. The heat of the sintering operation acts on the conductive metal as well as the ceramic, so that the sintering conditions must be mild enough that the metal does not melt or oxidize. In other words, the dielectric ceramic is required to be densely sintered at temperatures below the melting points of the conductive metals to be used (the melting point of Cu is 1083°C, that of Au is 1063°C, that of Ag is 961°C). Furthermore, if the Cu is used for the electrode, the dielectric ceramic is required to be burnt at low oxygen partial pressure. As a microwave dielectric ceramic that can be sintered at low temperature, a Bi 2 O 3 -CaO-Nb 2 O 5 system is disclosed in Japanese Laid-Open Patent No. (Tokkai-Hei) 5-225826. Although the Bi 2 O 3 -CaO-Nb 2 O 5 system ceramic can be sintered at a low temperature around 1000°C, Bi 2 O 3 of the main component evaporates during burning. Thus, the dielectric property is unstable with respect to the burning temperature. In general, when the resonant device is further miniaturized, the Q value drops. Therefore, suitable materials having a high Q value are still needed. EP-A1-0 671 370 provides a dielectric ceramic composition which is attained by sintering composition comprising a first component from 40 to 98 wt% and a second component from 2 to 60 wt% whereby the first component is represented by the formula Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 where 0 ≤ x ≤ 0.50 and the second component includes at least one element from the group consisting of SiO 2 and B 2 O 3 . The object of the present invention is to solve the above-mentioned problems and to provide the dielectric ceramic that is sinterable at lower temperatures, stable in composition, and has a high Q value. Another object of the present invention is to provide the method of manufacturing the dielectric ceramic and also provide a multilayer high frequency device using the dielectric ceramic. In order to accomplish these and other objects and advantages, the dielectric ceramic composition of the present invention provides the following components: the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide, and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 not more than 0.50) within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 within the range of not less than 2 parts by weight nor more than 60 parts by weight; and at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 within the range of not less than 0.1 parts by weight nor more than 10 parts by weight. It is preferable in the dielectric ceramic composition of the present invention that the dielectric constant (ε r ) ranges from 10 to 50. It is preferable in the dielectric ceramic composition of the present invention that the Qf product is not less than 1000GHz nor more than 30000GHz. It is preferable in the dielectric ceramic composition of the present invention that the temperature coefficient at a resonant frequency is not less than -50 ppm/°C nor more than +50 ppm/°C. According to the method of manufacturing the dielectric ceramic of the present invention, the dielectric ceramic is provided by sintering the dielectric ceramic composition. The above-mentioned dielectric ceramic composition comprises: the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 and not more than 0.50) within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 within the range of not less than 2 parts by weight nor more than 60 parts by weight; and at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 within the range of not less than 0.1 parts by weight nor more than 10 parts by weight. This method comprises the procedure of preheat treating a mixture of the second component and additive before sintering. It is preferable in the method of the present invention that the temperature for the preheat treatment ranges from 500°C to 900°C. It is preferable in the method of the present invention that the preheat treatment includes the procedures of melting at a temperature within the range of 1000°C to 1200°C and quenching after melting. It is preferable in the method of the present invention that the sintering temperature ranges from 800°C to 1200°C. It is preferable in the method of the present invention that the first component is calcined at the temperature of 1000°C-1300°C and then ground fine. It is preferable in the method of the present invention that the preheat treatment includes the procedures of: melting the second component at a temperature of 1000°C-1200°C; quenching it; and then grinding it fine. According to the multilayer high frequency device of the present invention comprising conductor and dielectric; all or some of the conductor is composed by Cu, Cu alloy, Au, Au alloy, Ag, and Ag alloy; all or some part of the dielectric is composed of the dielectric ceramic composition comprising: the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 and not more than 0.50) within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 within the range of not less than 2 parts by weight nor more than 60 parts by weight; and at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 within the range of not less than 0.1 parts by weight nor more than 10 parts by weight. It is preferable in the multilayer high frequency device that dielectric constant (ε r ) ranges from 10 to 50. It is preferable in the multilayer high frequency device that the Qf product is not less than 1000 GHz nor more than 30000 GHz. According to the dielectric ceramic composition of the present invention in which the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 not more than 0.50) is present within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 is present within the range of not less than 2 parts by weight nor more than 60 parts by weight; and at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 is present within the range of not less than 0.1 parts by weight nor more than 10 parts by weight: there can be provided the dielectric ceramic composition capable of being sintered at a low temperature, being stable in composition and having a higher Q value. In other words, since Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 having an excellent microwave dielectric property is used as the first component, and furthermore, since glass components which improve sintering are contained as the second component, there can be provided the dielectric ceramic sinterable at temperatures around 1000°C and having a high dielectric constant, a high Q value and a small temperature coefficient at a resonant frequency. Moreover, since Bi 2 O 3 is not contained as the first component, the dielectric ceramic is stable in composition and excellent in the stability of the dielectric property with respect to the burning temperature. The method for manufacturing the dielectric ceramic composition of the present invention permits manufacturing the dielectric ceramics efficiently and reasonably. According to the multilayer high frequency device of the present invention, the above-mentioned dielectric ceramic composition is used for the dielectric layer and Cu, Au, Ag, or alloys of them are used for the conductor. As a result, a miniature and high performanced high frequency device can be provided. Fig. 1 is a perspective view of the dielectric resonator of Example 4 of the present invention. Fig. 2 is a cross sectional view taken on line I-I of Fig.1. Fig. 3 is a cross sectional view taken on line II-II of Fig.1. Fig. 4A is a cross sectional view taken on line III-III of Fig. 2, Fig. 4B is a cross sectional view taken on line IV-IV of Fig. 2 and Fig. 4C is a cross sectional view taken on line V-V of Fig. 2. This invention will be explained in detail with reference to the following examples. Example 1 In example 1 is described a preferred embodiment to illustrate the dielectric ceramics composition of the present invention. The powder used for the first component is synthesized as follows. As initial materials, compounds of chemical purity (chemical purity hereinafter represents not less than 99wt.% purity), such as CaCO 3 , MgO, Nb 2 O 5 and TiO 2 were used. The purity of the materials was checked, and then the materials were weighed so as to make composition expressed by Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 wherein X is value shown in Tables. Moreover, the powder was blended with zirconia balls and pure water by means of a ball mill for 17 hours. The milled slurry was dried and calcined in the melting pot made of alumina at temperatures of 1000°C-1300°C for 2 hours. The calcined product was milled by the use of the above-mentioned ball mill for 17 hours and dried so that the powder of the first component was made. The powder used for the second component is synthesized as follows. As initial materials, compounds of chemical purity such as SiO 2 , B 2 O 3 , Al 2 O 3 , ZrO 2 , BaCO 3 , SrCO 3 , CaCO 3 , Li 2 O, ZnO, and PbO were used. The purity of these materials was checked and then the materials were weighed so as to make compositions shown respectively in Table 1. Moreover, the powder was blended with ethanol as solvent by using a ball mill and then dried. The blended powder was melted in a melting pot at the temperatures of 1000°C-1200°C and then quenched. After being milled, the blended powder was milled in the same manner as blending and then dried so that the powder of the second component was made. After milling, the particle size of the powder was less than 50µm. The composition of the synthesized second component is shown in Table 1. Sample NO. Composition of second component (parts by weight) SiO 2 B 2 O 3 Al 2 O 3 ZrO 2 BaO SrO CaO Li 2 O ZnO PbO A 50 20 10 20 B 60 10 10 20 C 50 30 20 D 45 27 20 3 5 E 45 26 20 3 5 1 F 45 27 20 3 5 G 55 20 15 4 6 As the additives, the powder of high chemical purity such as MgO, NiO, CuO, MnO 2 ,WO 3 was weighed so as to make the same composition as that shown in Tables 2 and 3. The additives were wet-milled in the ball mill with the powders of the first component and the second component and then dried. The powder was mixed with 6 wt.% of polyvinyl alcohol solution (of 5 wt.% in concentration) as a binder and granulated by sieving through 32 mesh screen. The granulated powder was press-molded into a disk of 13 mm in diameter and approximately 5 mm in thickness at a molding pressure of 100 MPa. After the molded product was heated at the temperature of 600°C for 3 hours to remove binders, the molded product was placed in a closed magnesia magnetic vessel, retained at various temperatures within the range of 800°C-1200°C for 2 hours and burned. The microwave dielectric property of the sintered product, which was burnt at the temperature showing the maximum density, was measured. The dielectric constant of the sample was calculated by means of the resonant frequency of TE 011 mode and sample state. At that time the sample was picked up and held by a parallel conductive plate, The resonant frequency and the Q value were measured by putting samples on the supporting base in the cavity by the dielectric resonator method of TE 01δ mode. As a result, the resonance frequency was 4-8 GHz. The resonant frequencies at temperatures of -25°C, 20°C, and 85°C were measured respectively and then the temperature coefficients (τf) were calculated by the least square method. The results are shown in the Table 2 and 3. Sample No Composition Sintering temperature Dielectric property first component second Component Additives °C εr Qf product τf X parts by wt. Mark parts by wt. element parts by wt. GHz ppm/°C 1 0.0 80 D 20 0 900 14 4500 -41 2 0.0 80 D 20 CuO 2 875 14 4800 -40 3 0.3 80 D 20 0 900 22 3800 -3 4 0.3 80 D 20 CuO 0.1 875 22 4000 -3 5 0.3 80 D 20 MgO 2 875 21 4300 -2 6 0.3 80 D 20 NiO 2 875 21 4300 -4 7 0.3 80 D 20 CuO 2 875 22 4500 -4 8 0.3 80 D 20 MnO 2 2 875 22 4200 -2 9 0.3 80 D 20 WO 3 2 875 21 4100 -4 10 0.3 80 D 20 CuO 5 875 21 4400 -7 11 0.3 80 D 20 CuO 10 850 21 3900 -10 12 0.3 80 D 20 CuO 15 825 20 1800 -13 13 0.3 80 D 20 MgO 0.5 875 21 4300 -4 NiO 0.5 MnO 2 0.5 WO 3 0.5 14 0.5 80 D 20 0 900 29 2400 +48 15 0.5 80 D 20 MgO 2 875 28 2700 +43 16 0.3 98 D 2 0 1150 40 18000 -10 17 0.3 98 D 2 CuO 5 1100 39 19000 -10 18 0.3 70 D 30 0 875 19 2900 -8 19 0.3 70 D 30 NiO 2 850 19 3200 -9 20 0.3 40 D 60 0 850 14 1200 -7 21 0.3 40 D 60 CuO 2 825 14 1500 -7 Sample No Composition Sintering temperature Dielectric property first component second Component Additives °C εr Qf product τf X parts by wt. Mark parts by wt. element parts by wt. GHz ppm/°C 22 0.3 80 A 20 0 1075 23 4100 +2 23 0.3 80 A 20 MgO 2 1025 22 4600 +1 NiO 2 24 0.3 80 B 20 0 875 20 2700 +4 25 0.3 80 B 20 MgO 2 850 20 2900 +3 MnO 2 2 26 0.3 80 C 20 0 950 23 3900 -2 27 0.3 80 C 20 CuO 2 900 22 4100 -2 WO 3 2 28 0.3 80 E 20 0 875 22 3700 -5 29 0.3 80 E 20 MnO 2 2 850 22 3800 -5 30 0.3 80 E 20 CuO 2 800 21 4100 -4 WO 3 2 31 0.3 80 F 20 0 900 22 3800 -3 32 0.3 80 F 20 NiO 2 875 22 4100 -4 33 0.3 80 F 20 CuO 2 850 21 4300 -4 NiO 2 34 0.3 80 G 20 0 950 24 4000 -2 35 0.3 80 G 20 MgO 2 900 23 4300 -2 WO 3 2 36 0.3 65 G 35 0 875 19 3300 -5 37 0.3 65 G 35 MgO 2 850 19 3500 -5 38 0.45 65 G 35 0 875 23 2800 +41 39 0.45 65 G 35 NiO 1 850 22 3000 +38 MnO 2 1 The reason for limiting the composition of the first component and second component will be explained hereinafter. It is not preferable that X in the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 be more than 0.5, since the temperature coefficient at a resonant frequency will be in more than +50. If the amount of second component is less than 2 parts by weight, the burning temperature will be above 1200°C. Consequently, the objective of the present invention is not achieved. Moreover, it is not preferable that the amount of accessory component be more than 60 parts by weight, since the Qf product will become less than 1000 GHz. Consequently, by limiting the composition of the first component and the second component, the dielectric ceramic composition of the present invention could be sintered at low temperatures around 1000°C. Furthermore, as described in Claims 1, there could be provided the dielectric ceramic composition having a high dielectric constant of around 25, a high Qf product of above 1000 GHz and a small temperature coefficient at a resonant frequency with the range of -50 to +50 ppm/°C. As is apparent from Table 2 and Table 3, by adding at least one selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 in the amount of 0.1 parts by weight to 10 parts by weight, the dielectric ceramic composition had a low burning temperature and high Q value. In other words, a dielectric ceramic having a good microwave dielectric property could be obtained. As shown in sample No. 12, if CuO, as a additive, was added at more than 10 parts by weight, the burning temperature could be lowered as compared with the case in which no additives was added, but at the same time Q value was also lowered. Therefore, the case of adding more than 10 parts by weight is not as desirable. Example 2 The method for making the first component and second component and examining the properties were conducted in the same manner as Example 1. As additives, the powder of high chemical purity such as MgO, NiO, CuO, MnO 2 , WO 3 were weighed so as to make the composition shown in Table 4 and 5. The additives were retained and heat treated together with the powder of second component for 2 hours at temperature of 500-900°C. After grinding fine, the additives were milled in a ball mill for 17 hours, dried and then mixed together with powder of the first component. The results were shown in Table 4 and Table 5. Sample No Composition Sintering temperature Dielectric property first component second Component Additives °C εr Qf product τf X parts by wt. Mark parts by wt. element parts by wt. GHz ppm/°C 40 0.3 80 D 20 0 900 22 3800 -3 41 0.3 80 D 20 CuO 0.1 875 22 4000 -3 42 0.3 80 D 20 MgO 2 875 22 4400 -3 43 0.3 80 D 20 NiO 2 875 22 4500 -5 44 0.3 80 D 20 CuO 2 875 23 4700 -4 45 0.3 80 D 20 MnO 2 2 875 23 4300 -2 46 0.3 80 D 20 WO 3 2 850 22 4200 -4 47 0.3 80 D 20 CuO 5 850 24 4600 -6 48 0.3 80 D 20 CuO 10 825 25 4000 -9 49 0.3 80 D 20 CuO 15 825 25 2200 -15 50 0.3 80 D 20 MgO 0.5 850 24 4500 -5 NiO 0.5 MnO 2 0.5 WO 3 0.5 51 0.5 80 D 20 0 900 29 2400 +48 52 0.5 80 D 20 MgO 2 875 29 2900 +42 53 0.3 98 D 2 0 1150 40 18000 -10 54 0.3 98 D 2 CuO 5 1100 41 22000 -11 55 0.3 70 D 30 0 875 19 2900 -8 56 0.3 70 D 30 NiO 2 850 19 3400 -10 57 0.3 40 D 60 0 850 14 1200 -7 58 0.3 40 D 60 CuO 2 825 15 1600 -8 Sample No Composition Sintering temperature °C Dielectric property first component second Component Additives εr Qf product GHz τf ppm/°C X wt.% Mark wt.% element wt.% 59 0.3 80 A 20 0 1075 23 4100 +2 60 0.3 80 A 20 MgO 2 1025 22 4800 +2 NiO 2 61 0.3 80 B 20 0 875 20 2700 +4 62 0.3 80 B 20 MgO 2 825 21 3100 +5 NiO 2 63 0.3 80 C 20 0 950 23 3900 -2 64 0.3 80 C 20 CuO 2 900 24 4400 -2 WO 3 2 65 0.3 80 E 20 0 875 22 3700 -5 66 0.3 80 E 20 CuO 2 825 23 4200 -4 WO 3 2 67 0.3 80 F 20 0 900 22 3800 -3 68 0.3 80 F 20 CuO 2 850 23 4500 -5 NiO 2 69 0.3 80 G 20 0 950 24 4000 -2 70 0.3 80 G 20 MgO 2 900 25 4400 -1 WO 3 2 As is apparent from Table 4 and Table 5, by heat treating at least one selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 at the rate of 0.1 parts by weight to 10 parts by weight together with second component at temperatures of 500-900°C in advance, the dielectric ceramic could be burnt at lower temperature and have a high Q value. Consequently, the dielectric ceramic having a good dielectric property and an excellent microwave property could be provided. Moreover, the reason for limiting the composition of the first component and second component was same reason as Example 1. As is apparent from the sample No. 49, if CuO, as an additive, was added with more than 10 parts by weight, the burning temperature could be lowered as compared with the case when no additive were added. However, at the same time Q value was also lowered. Therefore, the case where the additives are added at 10 parts by weight or more is not as desirable. Example 3 The method of manufacturing the first component and second component, and examining the properties were conducted in the same manner as Example 1. As additives, the powder of high chemical purity, such as MgO, NiO, CuO, MnO 2 , WO 3 as the additives were weighed so as to make the compositions shown in Table 6 and Table 7. The additives were melted together with the powder of the second component at the temperature of 1000°C-1200°C in the same manner as Example 1 and then quenched. Then the powder was ground fine, dried and blended together with the powder of the first component. The results were shown in the Table 6 and Table 7. Sample No Composition Sintering temperature Dielectric property first component second Component Additives °C εr Qf product τf X wt.% Mark wt.% element wt.% GHz ppm/°C 71 0.3 80 D 20 0 900 22 3800 -3 72 0.3 80 D 20 CuO 0.1 875 22 3900 -3 73 0.3 80 D 20 MgO 2 875 23 4500 -2 74 0.3 80 D 20 NiO 2 875 23 4500 -5 75 0.3 80 D 20 CuO 2 875 23 4900 -4 76 0.3 80 D 20 MnO 2 2 875 23 4300 -3 77 0.3 80 D 20 WO 3 2 850 23 4300 -4 78 0.3 80 D 20 CuO 5 850 24 4800 -7 79 0.3 80 D 20 CuO 10 825 25 4200 -9 80 0.3 80 D 20 CuO 15 825 26 2400 -15 81 0.3 80 D 20 MgO 0.5 850 25 4600 -6 NiO 0.5 MnO 2 0.5 WO 3 0.5 82 0.5 80 D 20 0 900 29 2400 +48 83 0.5 80 D 20 MgO 0.2 875 30 3000 +41 84 0.3 98 D 2 0 1150 40 18000 -10 85 0.3 98 D 2 CuO 5 1100 42 24000 -12 86 0.3 70 D 30 0 875 19 2900 -8 87 0.3 70 D 30 NiO 2 850 20 3600 -9 88 0.3 40 D 60 0 850 14 1200 -7 89 0.3 40 D 60 CuO 2 825 16 1800 -8 Sample No Composition Sintering temperature °C Dielectric property first component second Component Additives εr Qf product GHz τf ppm/°C X wt.% Mark wt.% element wt.% 90 0.3 80 A 20 0 1075 23 4100 +2 91 0.3 80 A 20 MgO 2 1025 24 4900 +2 NiO 2 92 0.3 80 B 20 0 875 20 2700 +4 93 0.3 80 B 20 MgO 2 825 23 3100 +4 MnO 2 2 94 0.3 80 C 20 0 950 23 3900 -2 95 0.3 80 C 20 CuO 2 900 25 4500 -2 WO 3 2 96 0.3 80 E 20 0 875 22 3700 -5 97 0.3 80 E 20 CuO 2 825 24 4400 -5 WO 3 2 98 0.3 80 F 20 0 900 22 3800 -3 99 0.3 80 F 20 CuO 2 850 23 4700 -3 NiO 2 100 0.3 80 G 20 0 950 24 4000 -2 101 0.3 80 G 20 MgO 2 900 25 4600 -2 WO 3 2 As is apparent from Table 6 and Table 7, by heat treating at least one selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 at the rate of 0.1 parts by weight to 10 parts by weight together with the second component, the dielectric ceramic could have lower sintering temperature and improve the Q value and have a high dielectric constant. Consequently, there could be provided the dielectric ceramic having good property and excellent microwave property. Moreover, the reason for limiting the composition of the first component and second component was the same reason as Example 1. As is apparent from sample No. 80, if CuO, as an additive, was added at more than 10 parts by weight, the burning temperature could be lowered as compared with the case when no additive were added, but at the same time, the Q value was also lowered. Therefore, adding the additives in the amount of more than 10 parts by weight is not as desirable. Example 4 In Example 4 is described a preferred embodiment to illustrate the high frequency device of the present invention. As a multilayer high frequency device, a dielectric resonator was made. The dielectric resonator has a structure in which a stripline conductor is covered with a dielectric layer and a shield conductor and a capacitor for binding are included. Fig.1 is a perspective view of the device. Fig. 2 is a cross sectional view taken on line I-I of Fig.1. Fig. 3 is a cross sectional view taken on line II-II of Fig. 1. Fig.4A is a cross sectional view taken on line III-III of Fig. 2. Fig.4B is a cross sectional view taken on line IV-IV of Fig. 2. Fig.4C is a cross sectional view taken on line V-V of Fig. 2. Herein, 1 shows a dielectric layer; 2, 3 and 4 show internal conductors; 5, 6,and 7 show external electrodes. Following is the method for manufacturing the high frequency device. First, organic binder, solvent and plasticizer were added and mixed in the composition of sample No. 10 of Table 2. The mixed slurry was formed into a sheet by the doctor blade method. As a conductive metal, various metals shown in Table 8 were selected. The metals were mixed with vehicle to make into paste. In the case where the conductor was Cu, CuO paste was used. conductive electrode resonant frequency GHz no-load Q Cu 2.04 180 Ag 2.01 180 99Ag-1Pt 2.00 170 Au 2.02 175 Other sheets were made from the composition of sample No. 47 of Table 4 and that of sample No. 78 of Table 6 by the same method. conductive electrode resonant frequency GHz no-load Q Cu 2.01 185 Ag 1.99 190 99Ag-1Pt 1.99 175 Au 2.00 180 conductive electrode resonant frequency GHz no-load Q Cu 2.00 190 Ag 1.99 190 99Ag-1Pt 1.98 180 Au 2.00 185 A plurality of sheets were layered, and then the conductive pattern 2 of Fig. 4 was screen printed thereon. A further plurality of sheets were layered thereon, and then the conductive pattern 3 was printed thereon. A further plurality of sheets were further layered thereon, and then the conductive pattern 4 was printed thereon. A further plurality of sheets were layered thereon, which were pressed by a heat pressing method. After cutting it into individual devices, the devices were heat treated in the air to flash the binder. In the case that CuO paste was used, the conductor was heat treated in H 2 for reducing to Cu and then burned in N 2 . In the case that another conductor was used, the conductor was burned in the air. The burning temperature was 900°C. The external electrodes 5, 6, and 7 were burned in the air, and Cu was burnt in N 2 so that a multilayer dielectric resonator was obtained. After burning, the size of device was 8mm in length, 4.5mm in width, and 2.5mm in height. The conductor, a strip line, was 1mm wide and 7mm long. Ten devices were made per each conductor and the average value was taken as the property. The resonant frequency and the Q value of the obtained resonator are shown in Table 8, 9 and 10. As seen in in Table 8, 9 and 10, the resonant frequency of resonator were approximately 2.0 GHz and the Q values are high when any of Cu, Au, Ag and alloys of them were used, thus showing excellent properties. Since the dielectric constant of the conventional substrate materials was approximately 8, in order to obtain the resonator which has the same structure and same resonant frequency, the length of the strip line is required to be approximately 12mm. However, the dielectric constant of the dielectric of the present invention was from 21 to 24, so that the length of the strip line was 7mm. Consequently, the miniature device could be provided. Moreover, by making the strip line in a curved or layered form, a smaller resonant device could be provided. In addition, by combining a plurality of resonators and capacitors, a band-pass filter could be provided. Furthermore, other than the elements described above, any elements that have no harmful effect on the dielectric properties may be included. As stated above, according to the dielectric ceramics of the present invention, wherein: the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 nor more than 0.50) is present within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 is present within the range of not less than 2 parts by weight nor less than 60 parts by weight; and at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 is present within the range of not less than 0.1 parts by weight nor less than 10 parts by weight; there can be provided the dielectric ceramic compositions that can be sintered at a low temperature and are stable in composition and have a higher Q value. In other words, since Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 having an excellent microwave dielectric property is used as the first component and glass components that improve the sintering are contained as the second component, the dielectric ceramic that can be sintered around 1000°C and have a high dielectric constant, a high Q value and a small temperature coefficient at a resonant frequency can be provided. Moreover, Bi 2 O 3 is not included in the first components so that the dielectric ceramic is stable in composition and also in the dielectric property with respect to the burning temperature. Consequently, the use of the dielectric ceramic of the present invention permits miniaturizing and improving the function of high frequency devices such as filters and resonators. According to the method for manufacturing the dielectric ceramic composition of the present invention, the dielectric ceramic composition can be effectively and reasonably manufactured. Moreover, according to the dielectric ceramic composition of the present invention, there can be provided the dielectric ceramic having a low burning temperature, high Q value, a high dielectric constant of around 25 and a small temperature coefficient at a resonant frequency (τ r ). As a result, a multilayer resonant device in which Cu, Au or Ag are used for an internal conductor can be provided. The miniature and highly performance resonator could provide a miniature and high performance automobile phone or portable phone. Moreover, the dielectric ceramic of the present invention can be used for not only a resonant device but also a microwave circuit substrate or multilayer ceramic capacitor. Consequently, the dielectric ceramics of the present invention can be valuable for industrial purposes.

Claims: A dielectric ceramic composition, wherein the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 not more than 0.50) is present within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 is present within the range of not less than 2 parts by weight nor more than 60 parts by weight; and characterized in that at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 is added within the range of not less than 0.1 parts by weight nor more than 10 parts by weight. The dielectric ceramic composition according to claim 1, wherein dielectric constant (ε r ) ranges from 10 to 50. The dielectric ceramic composition according to claim 1, wherein the Qf product is not less than 1000 GHz nor more than 30000 GHz. A method for manufacturing the dielectric ceramic composition comprising of: the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 not more than 0.50) within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 within the range of not less than 2 parts by weight nor more than 60 parts by weight; and characterized in that at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 is added within the range of not less than 0.1 parts by weight nor more than 10 parts by weight; and said method includes sintering of said composition and preheat treating a mixture of at least one selected from the second component and additive before said sintering process. The method for manufacuring the dielectric ceramic composition according to claim 4, wherein the temperature for the preheat treatment ranges from 500°C to 900°C. The method for manufacturing the dielectric ceramic composition according to claim 4, wherein the melting temperature of the preheat treatment is 1000°C-1200°C; and said heat treatment includes quenching after melted. The method for manufacturing the dielectric ceramic composition according to claim 4, wherein the sintering temperature ranges from 800°C to 1200°C. The method for manufacturing the dielectric ceramic composition according to claim 4, wherein the first component is calcined at the temperature of 1000°C-1300°C and then ground fine. The method for manufacturing the the dielectric ceramic composition according to claim 4, wherein the preheat treatment comprises the steps of melting the second component at the temperature of 1000°C-1200°C, quenching them and grinding them fine. A multilayer high frequency device comprising conductor and dielectric, wherein the conductor comprises Cu, Cu alloy, Au, Au alloy, Ag, and Ag alloy; and all or one part of the dielectric layer comprises: the first component comprising calcium oxide, magnesium oxide, niobium oxide and titanium oxide and expressed by the Formula: Ca{(Mg 1/3 Nb 2/3 ) 1-x Ti x }O 3 (wherein X is more than 0 not more than 0.50) within the range of not less than 40 parts by weight nor more than 98 parts by weight; the second component comprising at least one selected from SiO 2 and B 2 O 3 within the range of not less than 2 parts by weight nor more than 60 parts by weight; and characterized in that at least one oxide selected from the group consisting of MgO, NiO, CuO, MnO 2 and WO 3 is added within the range of not less than 0.1 parts by weight nor more than 10 parts by weight. The multilayer high frequency device according to claim 10, wherein dielectric constant (ε r ) ranges from 10 to 50.

Inventors: INOUE TATSUYA, KAGATA HIROSHI, KATO JUNICHI, NISHIMOTO KEIKI, INOUE, TATSUYA, KAGATA, HIROSHI, KATO, JUNICHI, NISHIMOTO, KEIJI, NISHIMOTO, KEIKI
Applicants: MATSUSHITA ELECTRIC IND CO LTD, MATSUSHITA ELECTRIC INDUSTRIAL CO., LTD
Application year: 1996
Main classification: H01B3
IPC codes: C04B35, H01B3