JPH08119728A - Dielectric porcelain composition - Google Patents

Abstract

PURPOSE: To obtain a dielectric porcelain composition having a high relative permittivity and a low dielectric loss at a relatively low baking temperature by using barium titanate as a principal component and including Nb2 O5 , MgO, La2 O3 , MnO and ZnO at specific ratios therein. CONSTITUTION: This dielectric porcelain composition contains 100 pts.wt. BaTiO3 , 0.8-2.5 pts.wt. Nb2 O5 , 0.06-0.70 pt.wt. MgO, 0.005-0.520 pt.wt. La2 O3 , MnO in an amount of 0.01-0.30 pt.wt. expressed in terms of MnCO3 and 0.01-0.5 pt.wt. ZnO at a molar ratio of the Nb2 O5 to the total content of ZnO and MgO within the range of 0.5-2.2. The composition has >=2500 relative permittivity, <=1300 deg.C baking temperature, a temperature change in electrostatic capacity satisfying the X7R of the Electronic Industries Association(EIA) Standards, a dielectric loss as low as <=2.5, a small voltage dependence and >=10<4> MΩ insulation resistance. Thereby, this composition copes with a smaller size and a larger capacity of a dielectric porcelain.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a dielectric ceramic composition, and more particularly to a dielectric ceramic composition used in capacitors, resonators and the like.

[0002]

2. Description of the Related Art Conventionally, dielectric ceramic compositions have been used as materials for laminated ceramic capacitors and the like. Such a monolithic ceramic capacitor is constructed by laminating a plurality of green sheets of a dielectric ceramic composition having internal electrodes so as to have a predetermined capacity, and then integrally firing them. For example, X7R (EIA standard: temperature characteristic of capacitance is -55
The dielectric ceramic composition used for the laminated ceramic capacitor of +/- 15 ° C at + 25 ° C
It is important that the relative dielectric constant is as high as 2500 or more, the thickness of each green sheet is 15 μm or less, and the firing temperature is 1300 ° C. or less.

That is, the relative dielectric constant at 25 ° C. is 2500
As described above, by setting the thickness of the green sheet to 15 μm or less, the thickness of the green sheet between the internal electrodes and the facing area can be minimized, and the multilayer ceramic capacitor can be downsized. Further, by setting the firing temperature to 1300 ° C. or lower, the selection range of the material of the internal electrodes is increased, and for example,
It is possible to use inexpensive Pd-Ag from expensive 100% Pd material. In addition to the above, the dielectric loss tan δ and the insulation resistance, which are various characteristics of the dielectric ceramic composition, must be fully taken into consideration, and it is further desired that the dielectric loss has a small AC voltage dependency.

Conventionally, as a device having an improved relative dielectric constant,
A dielectric ceramic composition containing BaTiO ₃ , Nb ₂ O ₅ , and ZnO has already been proposed (Japanese Patent Laid-Open No. 59-18162).
JP, JP-A-59-18159, etc.). Such a dielectric ceramic composition has a relative dielectric constant of 2000.
Can be up to 3000. However, even though the above-mentioned dielectric ceramic composition can obtain a high relative permittivity, the dielectric loss tan δ is large, so that the green sheet cannot be thinned, and when used in a multilayer capacitor, a high relative dielectric constant is eventually obtained. Dielectric constant could not be obtained.

As a system developed to reduce the dielectric loss tan δ in this way, BaTiO ₃ , Nb is used.
A dielectric ceramic composition containing ₂ O ₅ , MgO, and La ₂ O ₃ has already been proposed (see Japanese Patent Publication No. 5-10766). In addition, Nb ₂ O ₅ and MgO are mixed so that the molar ratio of Nb ₂ O ₅ / MgO to BaTiO ₃ is in the range of 2.3 to 4.
And a rare earth element is added thereto in an amount of 0.1 to 0.5% by weight (see Japanese Patent Publication No. 55-19007).

[0006]

However, none of the above-mentioned dielectric ceramics has a small relative permittivity of about 2200 or less and cannot cope with a reduction in size and capacity. Further, there is a problem that the dielectric loss is still large and it is difficult to make the green sheet thin.

Furthermore, in any of the above-mentioned dielectric ceramics, it is considered that the AC loss dependency of the dielectric loss becomes large and it becomes impossible to cope with the thinning of the dielectric material.
In this case, there is a problem that it is not possible to cope with the miniaturization and the large capacity of the capacitor.

[0008]

[Means for Solving the Problems] As a result of intensive studies made by the present inventors in view of the above problems, barium titanate BaT
iO ₃ as a main component, Nb ₂ O ₅ , MgO, La
₂ O ₃ , MnO, and ZnO are contained in a predetermined composition ratio, and the relative dielectric constant is 250 by setting the molar ratio of Nb ₂ O _{5 to} the total amount of ZnO and MgO to 0.5 to 2.2.
0 or more, the temperature change rate of capacitance is X7R of EIA standard
Is satisfied, the dielectric loss is as small as 2.5% or less, and the dielectric loss is 3.0% even when an AC voltage of 2000 V / cm is applied.
The inventors have found that the following can provide a dielectric porcelain having a small AC voltage dependency and capable of being made thin, and have completed the present invention.

That is, the dielectric ceramic of the present invention is made of BaTiO 3.
₃ Nb ₂ O ₅ 0.8 to 2.5 with respect to 100 parts by weight
Parts by weight, 0.06 to 0.70 parts by weight of MgO, La ₂ O
0.005 to 0.520 parts by weight of ₃ and MnO to MnCO
0.01 to 0.30 parts by weight in terms of ₃ and ZnO to 0.
1 to 0.5 parts by weight, and the molar ratio of Nb ₂ O _{5 to} the total amount of ZnO and MgO is 0.5 to 2.2. Further, for 100 parts by weight of BaTiO ₃ , SiO 2
₂ and Al ₂ O ₃ at least one of 0.05 to
It is desirable to contain 0.50 parts by weight.

In the present invention, 0.8 to 2.5 parts by weight of Nb ₂ O ₅ is contained with respect to 100 parts by weight of BaTiO _{3 when the} content is less than 0.8 parts by weight, the dielectric loss is deteriorated and the temperature is lowered. This is because the characteristics and sinterability are poor, and when it exceeds 2.5 parts by weight, the relative dielectric constant is lowered and the temperature characteristics are greatly deteriorated. Nb ₂ O ₅ is preferably contained in an amount of 1.3 to 2.0 parts by weight based on 100 parts by weight of BaTiO ₃ .

Further, MgO is set to 0.06 to 0.70 parts by weight because when it is less than 0.06 parts by weight, the relative dielectric constant and the insulation resistance are lowered, the temperature characteristics are deteriorated, grain growth is caused, and the voltage of dielectric loss. This is because the dependency becomes large. Also, 0.7
This is because if the amount is more than 0 parts by weight, the dielectric constant decreases and the insulation resistance also decreases. MgO is preferably 0.1 to 0.4 parts by weight.

Further, 0.002 to 0.5 of La ₂ O ₃ is added.
The content of 20 parts by weight means that when La ₂ O ₃ is less than 0.005 parts by weight, the relative dielectric constant is lowered and the sinterability is deteriorated.
This is because if the amount exceeds 0 parts by weight, the temperature characteristics deteriorate. L
a ₂ O ₃ is desirably 0.005 to 0.2 parts by weight.

Further, MnO is converted to MnCO ₃ in an amount of 0.01 to
The amount of 0.30 parts by weight is less than 0.01 parts by weight, the insulation resistance decreases, the dielectric loss and the sinterability deteriorate, and
This is because if the amount exceeds 0 parts by weight, the relative dielectric constant decreases. MnO is preferably 0.04 to 0.10 parts by weight in terms of MnCO ₃ .

Further, ZnO is set to 0.10 to 0.50 parts by weight because the insulation resistance is low when the content is less than 0.10 parts by weight.
This is because the dielectric loss and the sinterability are deteriorated, and when it exceeds 0.50 parts by weight, the relative dielectric constant is decreased and the temperature characteristics are deteriorated. ZnO is preferably 0.10 to 0.30 parts by weight.

N relative to the total amount of ZnO and MgO
The molar ratio of b ₂ O ₅ is set to 0.5 to 2.2, because when the molar ratio is less than 0.5, the relative dielectric constant is deteriorated and the temperature characteristics are poor. This is because the characteristics are poor and the relative dielectric constant is lowered. In the present invention, ZnO and MgO
The molar ratio of Nb ₂ O _{5 to} the total amount of
It is desirable to set it to 1.4.

If at least one of SiO ₂ and Al ₂ O ₃ is contained in an amount of 0.05 to 0.50 parts by weight with respect to 100 parts by weight of BaTiO ₃ , the firing temperature is further lowered depending on the composition, and the electrostatic capacity is increased. The capacity and relative permittivity can be increased. The above effects of SiO ₂ and Al ₂ O ₃ are not so remarkable when the amount is less than 0.05 parts by weight, and the relative permittivity tends to decrease when the amount is more than 0.50 parts by weight. Is. At least one of SiO ₂ and Al ₂ O ₃ is BaTiO ₃ 1
It is desirable to contain 0.1 to 0.2 parts by weight with respect to 00 parts by weight.

The dielectric porcelain of the present invention is mainly composed of BaTiO ₃ powder having an average crystal grain size of 1.0 μm or less, which is produced by a solid phase method sol-gel method, oxalic acid method, hydrothermal synthesis method or the like. , With respect to 100 parts by weight of this BaTiO ₃ , Nb ₂ O ₅ , MgO, La ₂ O ₃ , MnCO ₃ , S
iO _2, Al ₂ O _3, a ZnO powders were weighed in predetermined amounts, a ball mill or the like and 20 to 48 hours wet grinding, dried, and adding a predetermined amount of organic binder or the like, and molded into a predetermined shape, 1-2 at 1200 ° C to 1300 ° C in the atmosphere
It is manufactured by firing for a time. In the case of producing a monolithic ceramic capacitor, the above powder is slurried, formed into a sheet by a method such as a doctor blade, and an internal electrode such as Ag-Pd is appropriately applied to the sheet formed body, A plurality of these may be laminated and cofired under the above firing conditions.

The Nb ₂ O ₅ and M used in the present invention are
gO, La ₂ O ₃ , MnCO ₃ , SiO ₂ , Al
Instead of ₂ O ₃ and ZnO powders, Nb, Mg, L
It is also possible to use hydroxides, carbonates, nitrates, oxalates, alkoxides, etc. of a, Mn, Si, Al, Zn, which decompose into oxides at a sintering temperature or lower.

In order to improve the AC voltage dependency, it is preferable to control the average crystal grain size d of the sintered body to d <1.0 μm. Thus, the average crystal grain size d of the sintered body is d <
To control to 1.0 μm, use barium titanate powder having an average crystal grain size of 1.0 μm or less as a starting material,
It is necessary to perform wet pulverization for a long period of time and control the particle size after pulverization to 0.8 μm or less, and set the firing temperature as low as possible to shorten the firing time.

[0020]

In the dielectric ceramic composition of the present invention, the temperature characteristic of capacitance is within ± 15% in the range of -55 ° C to 125 ° C, the relative dielectric constant at + 25 ° C is 2500 or more, and the thickness of the green sheet is Is 15 μm, the dielectric loss is as small as 2.5% or less, and the AC voltage is 2000 V / cm.
The dielectric loss in 3 can be as small as 3% or less. Therefore, a small-sized and large-capacity multilayer capacitor can be obtained. Moreover, since the firing temperature is 1300 ° C. or less, it is easy to manufacture industrially, and inexpensive silver-palladium (Ag / Pd = 20/80 to 40/6) is used for the internal electrodes.
A dielectric porcelain that can be used for a multilayer capacitor using 0) is achieved. Furthermore, the dielectric loss, which is a basic characteristic of dielectric ceramics, is 2.5% or less, and the insulation resistance (IR)
Of 10 ⁴ MΩ or more, which is a satisfactory dielectric ceramic.

[0021]

EXAMPLES Examples of the present invention will be described in detail below.

Average particle size produced by hydrothermal method 1.
Based on BaTiO ₃ powder of 0 μm or less as the main component,
100 parts by weight of aTiO ₃ , Nb ₂ O ₅ , Mg
Each powder of O, La ₂ O ₃ , MnCO ₃ , and ZnO was weighed as shown in Table 1, wet-milled for 20 to 48 hours with a ball mill, added with an organic binder, and then stirred,
It was formed into a tape having a thickness of 15 μm by the doctor blade method. Cut this tape into 130 mm x 100 mm and cut it into 2
A stack is prepared by stacking 0 sheets and hot pressing at 80 ° C.

[0023]

[Table 1]

As an internal electrode, an Ag-based paste (A
g / Pd = 30/70) was printed. This laminated body is 3.
Cut into 2 mm x 1.6 mm and 1250 to 1 in air
It was baked at 320 ° C. for 2 hours. Further, electrodes made of silver paste were baked on both end faces at 800 ° C. for 10 minutes to prepare samples for measurement.

The capacitance and the dielectric loss of the sample thus formed were measured at a reference temperature of 25 ° C. and a frequency of 1.0 k.
It was measured at Hz and a measurement voltage of 1.0 Vrms. The temperature change rate of the capacity is measured in the range of −55 to + 125 ° C.,
The capacity at + 25 ° C was used as a standard. Further, the insulation resistance was measured when a DC voltage of 25 V was applied for 1 minute.

The relative permittivity was calculated back from the capacitance.

The average particle size of the sintered body was calculated by observing the surface of the sintered body at 15,000 times with a scanning electron microscope and measuring 500 or more particles by the line intercept method. Further, the dielectric loss was measured when a voltage of 2000 Vrms / cm was applied at a frequency of 1 kHz. Table 2 shows the above results.

[0028]

[Table 2]

All of the dielectric porcelains within the scope of the present invention have a large relative permittivity of 2,500 or more, and moreover, have an EIA standard of X.
7R characteristics (capacity change rate within ± 15% in the temperature range of −55 ° C. to 125 ° C.) are satisfied. Furthermore, the dielectric loss tan
δ is as small as 2.5% or less, AC voltage 2000 Vrms
A loss of 3.0% or less is shown even under / cm. Further, the insulation resistance (IR) is 10 ⁴ MΩ or more.

In Table 1, sample Nos. 1 to 5 are Nb ₂ added to BaTiO ₃ which is the main component of the dielectric ceramic composition.
The amount of O ₅ added was varied from 0.7 to 2.6 parts by weight. At this time, the amounts of MgO, La ₂ O ₃ , MnCO ₃ and ZnO added were 0.1 parts by weight, 0.2 parts by weight and 0.1 parts by weight, respectively.
Part by weight, 0.1 to 0.2 parts by weight.

Sample No. 1 (Nb ₂ O ₅ addition amount: 0.7
(Parts by weight), the relative dielectric constant εr is 3700, which is a good product, but the dielectric loss tan δ is 3.4%. Further, the temperature characteristic becomes -25%. Further, in the sample numbers 2 to 4 (addition amount of Nb ₂ O ₅ : 0.8 to 2.5% by weight), the relative dielectric constant εr becomes 2700 to 3600,
Dielectric loss tan δ is 2.5% or less, and temperature characteristics are ±
Within 13%, tan δ when an AC voltage of 2000 V / cm is applied is 3.0% or less, and the insulation resistance (IR) is 4 to 6 as well.
The range is × 10 ⁴ MΩ, which is a good product. That is, the relative permittivity εr
High, excellent temperature characteristics, small dielectric loss tan δ,
Further, a dielectric ceramic having a small dielectric loss AC voltage dependency is achieved. Further, Sample No. 5 (addition amount of Nb ₂ O ₅ :
At 2.6 parts by weight), the relative dielectric constant ε is 2300, and the temperature characteristics deteriorate. Therefore, in the present invention, the weight of Nb ₂ O ₅ added to barium titanate BaTiO ₃ is in the range of 0.8 to 2.5 parts by weight with respect to 100 parts by weight of barium titanate BaTiO ₃ .

In Sample Nos. 6 to 10, the amount of MgO added to BaTiO ₃ , which is the main component of the dielectric ceramic composition, was changed to 0.05 to 0.75 parts by weight. At this time, Nb ₂ O ₅ , La ₂ O ₃ , MnCO ₃ and ZnO
Were added to 1.8 to 2.5 parts by weight, 0.2 parts by weight, 0.1 parts by weight, and 0.1 to 0.2 parts by weight, respectively.

Sample No. 6 (amount of MgO added: 0.05 parts by weight) has a tan when an AC voltage of 2000 V / cm is applied.
δ becomes 3.8%. In addition, sample numbers 7 to 9
(In the addition amount of MgO: 0.06 to 0.70 parts by weight),
The relative permittivity εr becomes 2600 to 2900, and the dielectric loss t
anδ is 2.0% or less, temperature characteristics are within ± 13%, tanδ when an AC voltage of 2000 V / cm is applied is 2.8% or less, and insulation resistance (IR) is also 3 to 5 × 10 ⁴ M.
Ω and good product range. That is, a dielectric ceramic having a high relative permittivity εr, excellent temperature characteristics, a small dielectric loss tan δ, and a small AC voltage dependency of the dielectric loss can be achieved. Further, in sample No. 10 (amount of MgO added: 0.75 parts by weight), the dielectric loss tan δ is 1.8%, which is in the range of good products, but the relative dielectric constant εr is 2100. Therefore, in the present invention, barium titanate BaT
The weight of MgO added to iO ₃ is barium titanate Ba.
The range was 0.06 to 0.70 parts by weight with respect to 100 parts by weight of TiO ₃ . Sample Nos. 11 to 15 are La ₂ O ₃ added to BaTiO ₃ which is the main component of the dielectric ceramic composition.
The value was changed from 0.004 to 0.53 parts by weight.

At this time, Nb ₂ O ₅ , MgO, MnCO ₃
The amounts of ZnO and ZnO added were 1.8 parts by weight, 0.2 parts by weight, 0.1 parts by weight, and 0.2 parts by weight, respectively.

Sample No. 11 (amount of La ₂ O ₃ added: 0.
004 parts by weight), the dielectric loss tan δ becomes 2.4%, but the relative dielectric constant εr becomes as low as 2400. Sample Nos. 12 to 14 (amount of La ₂ O ₃ added:
0.005 to 0.52 parts by weight), the relative permittivity εr is 2
800-3500, dielectric loss tan δ 2.1%
Below, the temperature characteristics are within ± 11%, and the tan δ when an AC voltage of 2000 V / cm is applied is 2.8% or less,
The insulation resistance (IR) is also in the range of good products of 3 to 6 × 10 ⁴ MΩ. That is, a dielectric ceramic having a high relative permittivity εr, excellent temperature characteristics, a small dielectric loss tan δ, and a small AC voltage dependency of the dielectric loss can be achieved. Further, in sample No. 15 (amount of La ₂ O ₃ added: 0.53 parts by weight), the relative dielectric constant εr was 3700 and the dielectric loss tan δ was 1.8%, which was in the range of good products, but the temperature characteristics deteriorated. Will end up.
Therefore, in the present invention, barium titanate BaTiO 3
Added to ₃ weight of La ₂ O ₃ is barium titanate B
0.005-0.5 with respect to 100 parts by weight of aTiO ₃
The range was 2 parts by weight.

In Sample Nos. 16 to 20, the amount of MnCO ₃ added to BaTiO ₃ which is the main component of the dielectric ceramic composition was varied from 0.005 to 0.31 parts by weight.

At this time, Nb ₂ O ₅ , MgO, La ₂ O ₃
And ZnO added amount of 1.8 parts by weight, 0.2 parts by weight,
The amount was 0.2 parts by weight and 0.2 parts by weight.

Sample No. 16 (Amount of MnCO ₃ added: 0.
005 parts by weight), the relative dielectric constant εr becomes 3000, but the dielectric loss tan δ becomes 2.5%. Furthermore, the insulation resistance becomes 8 × 10 ³ MΩ. Moreover, (the addition amount of MnCO _3: 0.01 to 0.3 wt%) Sample No. 17 to 19 in relative dielectric constant εr is next 2800-3000, the dielectric loss tanδ of not more than 2.2%, the temperature characteristic Is within ± 7%, tan δ is 3.0% or less when an AC voltage of 2000 V / cm is applied, and the insulation resistance (IR) is 2 ×.
It is in the range of good products of 10 ^{4 to} 9 × 10 ⁴ MΩ. That is, the relative dielectric constant εr is high, the temperature characteristics are excellent, and the dielectric loss tanδ
And a dielectric porcelain in which the dielectric loss is less dependent on the AC voltage is achieved. Furthermore, sample number 20 (MnCO
₃ addition amount: 0.31 parts by weight), dielectric loss tan δ
Is 1.4%, which is in the range of non-defective products, but the relative dielectric constant εr is as low as 2200. Therefore, in the present invention, MnCO ₃ added to barium titanate BaTiO ₃ is used.
Was 0.01 to 0.3 parts by weight with respect to 100 parts by weight of barium titanate BaTiO ₃ .

Sample Nos. 21 to 26 are cases in which the amount of ZnO added to BaTiO ₃ which is the main component of the dielectric ceramic composition was changed to 0.1 to 0.8 parts by weight. At this time, Nb ₂ O ₅ , MgO, La ₂ O ₃ and M
The amount of nCO ₃ added is 1.8 to 2.1 parts by weight,
0.1 to 0.15 part by weight, 0.2 part by weight, and 0.1 part by weight.

Sample Nos. 21 to 25 (ZnO addition amount:
0.1 to 0.5 parts by weight), the relative dielectric constant εr is 2800.
.About.3200, the dielectric loss tan δ is 1.8% or less, the temperature characteristic is within ± 14%, and the AC voltage is 200%.
The tan δ at the time of applying 0 V / cm is 2.8% or less, and the insulation resistance (IR) is 4 to 5 × 10 ⁴ MΩ.

That is, a dielectric ceramic having a high relative permittivity εr, excellent temperature characteristics, a small dielectric loss tan δ, and a small AC voltage dependency of the dielectric loss is achieved. Further, in the sample No. 26 (ZnO addition amount: 0.8 parts by weight), the dielectric loss tan δ was 2.0%, which was a good product, but the relative dielectric constant εr was as low as 2200, and the temperature characteristics and insulation resistance were deteriorated. To do. Therefore, in the present invention, barium titanate Ba
The amount of ZnO added to TiO ₃ is barium titanate Ba.
The range was 0.1 to 0.5 parts by weight with respect to 100 parts by weight of TiO ₃ .

Example 2 SiO ₂ and Al ₂ O ₃ powder were added to the composition of sample No. 13 in Table 1 as shown in Table 3 and formed into a tape in the same manner as in Example 1. Then, the tape was laminated to form internal electrodes to prepare a laminated body. Then, each characteristic was measured in the same manner as in Example 1 and is shown in Table 4.

The composition of the sample was such that 1.8 parts by weight of Nb ₂ O ₅ , 0.2 parts by weight of MgO, 0.2 parts by weight of La ₂ O ₃ and MnO were added to 100 parts by weight of BaTiO _3. Mn
It contains 0.1 parts by weight of CO ₃ , 0.2 parts by weight of ZnO, and a predetermined amount of SiO ₂ and Al ₂ O ₃ with respect to 100 parts by weight of BaTiO ₃ .

[0044]

[Table 3]

[0045]

[Table 4]

From these Tables 3 and 4, SiO ₂ , Al ₂
It can be seen that the inclusion of O ₃ results in a lower firing temperature and a higher dielectric constant than in the case where these compounds are not included (Sample No. 13).

[0047]

As described above, according to the present invention, X7R
The characteristics are satisfied, the relative dielectric constant εr is 2500 or more, and the firing temperature is 1300 ° C. or less. As other characteristics, the dielectric loss tan δ is 2.5% or less, the insulation resistance (I
It is possible to obtain a dielectric ceramic composition in which R) is 10 ⁴ MΩ or more and tan δ is 3% or less when an AC voltage of 2000 V / cm is applied.

Thus, for example, when a monolithic ceramic capacitor is composed of the above-mentioned dielectric ceramic composition, a compact and large-capacity capacitor having excellent temperature characteristics can be obtained, and the firing temperature is 1300 ° C. or lower, and Inexpensive silver-palladium can be used as an internal electrode between the formed sheets, and an inexpensive monolithic ceramic capacitor can be obtained.

Claims (2)

[Claims] 1. Nb based on 100 parts by weight of BaTiO _3.
0.8 to 2.5 parts by weight of ₂ O ₅ and 0.06 to MgO
0.70 parts by weight, La ₂ O ₃ and 0.005 to 0.520
0.01 to 0 in terms parts by weight of MnO to MnCO _3.
30 parts by weight and 0.1 to 0.5 parts by weight of ZnO, and the molar ratio of Nb ₂ O _{5 to} the total amount of ZnO and MgO is in the range of 0.5 to 2.2. A dielectric ceramic composition. 2. Si based on 100 parts by weight of BaTiO ₃
0.05 at least one of O ₂ and Al ₂ O ₃
The dielectric ceramic composition according to claim 1, wherein the dielectric ceramic composition is contained in an amount of 0.50 parts by weight.