JP2006347818A - Dielectric ceramic and its production method - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide dielectric ceramics such as BaNd<SB>2</SB>Ti<SB>5</SB>O<SB>14</SB>and BaNd<SB>2</SB>Ti<SB>4</SB>O<SB>12</SB>which are obtained by a combustion synthesis method and have excellent sintering behavior, and to provide a method for production thereof. <P>SOLUTION: There is provided an oxide-based dielectric ceramic represented by the composition formula, BaNd<SB>2</SB>Ti<SB>m</SB>O<SB>2m+4</SB>(3≤m≤7; and m is an integer). The ceramic is obtained by blending the reaction materials including at least the Ti powder having a specific surface area of 0.01-2 m<SP>2</SP>/g, Nd<SB>2</SB>O<SB>3</SB>, BaO<SB>2</SB>and an ionically bonding substance being an oxygen-feeding source in the prescribed ratios, respectively and synthesizing by the combustion synthesis method in which the adiabatic flame temperature is ≥1,500°C. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

The present invention relates to an oxide-based dielectric ceramic represented by the composition formula BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer), particularly BaNd ₂ Ti ₅ O ₁₄ or BaNd ₂ Ti. _{The present} invention relates to ₄ O ₁₂ and its production method.

In recent years, with the remarkable development of high-frequency communication technology such as mobile phone and satellite communication, the demand for dielectric ceramics for high-frequency devices such as dielectric resonators and filters is increasing. As for the frequency of the communication signal and the size of the communication device, for example, when the relative dielectric constant of the antenna substrate incorporated in the communication device is increased, the frequency and size can be further reduced. The relative permittivity is a parameter indicating the degree of polarization inside the dielectric. The higher the relative permittivity of the dielectric ceramic used in the antenna material, the shorter the wavelength of the signal propagating through the electronic component circuit, and the higher the signal Turn into. Therefore, if an electronic component having a high relative dielectric constant can be used, the frequency can be increased, the circuit can be shortened, and the communication device can be downsized. Moreover, low dielectric loss and good temperature stability are simultaneously required for dielectric ceramics used in the above devices.
BaNd ₂ Ti ₅ O ₁₄ , BaNd ₂ Ti ₄ O _{12, and the} like are known as dielectric ceramics that satisfy such required characteristics, and are used in various applications. These are based on the paraelectric phase to keep the dielectric loss low.

For the synthesis of conventional dielectric ceramics, external heating must be performed using a furnace capable of heating from 1000 ° C to around 2000 ° C. For this reason, the synthesis of ceramics requires enormous energy and a large heating mechanism, which increases the manufacturing cost. The production of BaNd ₂ Ti ₅ O ₁₄ and BaNd ₂ Ti ₄ O ₁₂ is no exception, and each powder of BaO, Nd ₂ O ₃ and TiO ₂ is wet-mixed by a ball mill, and the dried powder is 1100 ° C. × 5 hours. Are calcined and pulverized into dielectric ceramic powder (see Non-Patent Document 1 and Non-Patent Document 2).

In addition, as a production method without external heating, synthesis of ceramic powder by a combustion synthesis method (self propagating high temperature synthesis (SHS)) has been proposed. This method uses the heat generated during the formation of intermetallic compounds and ceramics. Powders that are constituent elements of the compound are mixed well to make a green compact. When high temperature is applied to a part of the powder, it ignites. This is a method of obtaining a sintered body by proceeding a synthesis reaction while generating heat of formation.
Combining two types of materials, intermetallic compounds or non-oxide ceramics and oxide ceramics, using three types of raw materials as a starting material: one type of metal oxide and two different types of metal elements. Has been proposed (see Patent Document 1). For example, after mixing nickel oxide powder, aluminum powder, and alumina powder to form a compact, it is stored in a high-pressure reaction vessel, and the upper end surface of the compact is ignited in an argon atmosphere to oxidize and burn the aluminum powder. The combustion reaction proceeds in a chained manner while the reduced nickel reacts with the excessively added aluminum to synthesize NiAl. As a result, an ingot of NiTi that is one of intermetallic compounds can be manufactured without external heating.

However, the combustion synthesis method of Patent Document 1 cannot obtain oxide-based dielectric ceramics such as BaNd ₂ Ti ₅ O ₁₄ and BaNd ₂ Ti ₄ O ₁₂ . In this method, Al ₂ O ₃ synthesized simultaneously can be easily separated from NiTi due to the difference in wettability, specific gravity, viscosity, melting point, and thermodynamic stability with respect to NiTi. It is difficult to accurately separate these compounds. For example, even when washed with washing water, Al ₂ O ₃ does not dissolve in water and cannot be separated.
In order to completely propagate the combustion wave in the combustion synthesis method, the blending ratio of the powder as each constituent element source and the physical properties (specific surface area) of the metal powder as the heat source are important. It is not easy to produce ceramics having a high quality. For example, when the blending ratio of the stable component and the heat source component is out of a predetermined range, there is a problem that the combustion wave does not completely propagate and the dielectric characteristics deteriorate due to mixing of unreacted components.
Japanese Patent Laid-Open No. 5-9009 British Ceramic Transactions 1996. Vol95. No.2 P79-81 "Dielectric resonators in BaO-Ln2O3-5TiO2 system (Ln = La, Pr, Nd, Sm) 1984.April" Journal of the American Ceramic Society Vol.67.No.4 P278-281 `` Microwave Characteristics of (Zr, Sn) TiO2 and BaO-PbO-Nd2O3-TiO2 Dielectric Resonators '' K.WAKINO, K.MINAMI, H.

The present invention has been made in order to cope with such problems, and is obtained by a combustion synthesis method and has dielectric properties such as BaNd ₂ Ti ₅ O ₁₄ and BaNd ₂ Ti ₄ O ₁₂ having excellent sintered body characteristics. An object of the present invention is to provide a ceramic body and a method for producing the same.

The dielectric ceramic of the present invention is an oxide-based dielectric ceramic represented by the composition formula BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer), and has a specific surface area of 0.01. Reactive raw materials containing at least 2 m ² / g Ti powder, Nd ₂ O ₃ , BaO ₂ , and an ion-binding substance as an oxygen supply source are blended at a predetermined ratio, and the adiabatic flame temperature is 1500 ° C. It is obtained by the combustion synthesis method as described above. Here, each element symbol is Ba (barium), Nd (neodymium), Ti (titanium), and O (oxygen), respectively.
The ion-binding substance is sodium perchlorate.

In the above composition formula, m = 5, which is obtained by the reaction shown in the following formula (1) by the combustion synthesis method.

In the above composition formula, m = 4, which is obtained by the reaction shown in the following formula (2) by the combustion synthesis method.

The reaction raw material contains TiO ₂ .

The method for producing a dielectric ceramic of the present invention is a method for producing an oxide-based dielectric ceramic represented by the composition formula BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer). And a step of blending a reaction raw material containing at least a specific ratio of Ti powder having a specific surface area of 0.01 to ² m ² / g, Nd ₂ O ₃ , BaO ₂ , and an ion-binding substance serving as an oxygen supply source. And a step of reacting the blended compound at the predetermined ratio by a combustion synthesis method with an adiabatic flame temperature of 1500 ° C. or higher, a step of pulverizing the reaction product, and washing the pulverized powder with water And a process.

The dielectric ceramic of the present invention (BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer)) is a Ti powder, Nd ₂ O ₃ , BaO _2, and an oxygen supply source. Since it is obtained by combustion synthesis with adiabatic flame temperature of 1500 ° C or higher using a reaction raw material containing at least an ion-binding substance, it has excellent sintered body characteristics. In particular, BaNd ₂ Ti ₅ O ₁₄ and BaNd ₂ Ti ₄ O ₁₂ are obtained as dielectric ceramics based on the chemical reaction formula of the above formula (1) or (2).

The dielectric ceramic manufacturing method of the present invention uses the above-mentioned raw materials and a combustion synthesis method by setting the specific surface area of the metal powder within a predetermined range, etc., and a dielectric such as BaNd ₂ Ti ₅ O ₁₄ and BaNd ₂ Ti ₄ O _12. Body ceramics can be manufactured. Moreover, since the by-products can be sufficiently removed by pulverizing the synthetic powder and then washing with water, a sintered body close to the theoretical density can be obtained. In addition, by using the combustion synthesis method, dielectric ceramics can be manufactured at a low cost and in a short time compared to the conventional method of external heating.

The dielectric ceramic of the present invention is represented by a composition formula BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer), and a Ti powder having a specific surface area of 0.01 to ² m ² / g, Reactive raw materials containing at least Nd ₂ O ₃ (neodymium oxide), BaO ₂ (barium peroxide), and an ion-binding substance serving as an oxygen supply source are blended at a predetermined ratio, and the adiabatic flame temperature is 1500 ° C. or higher. Obtained by the combustion synthesis method.

The Ti powder is preferably a fine powder and has a specific surface area of 0.01 to ² m ² / g. A preferable specific surface area is 0.1 to 0.6 m ² / g because the combustion wave propagates and is easy to handle. When the specific surface area is less than 0.01 m ² / g, because the contact area between the Ti powder that is the heat source and the oxygen supply source such as BaO ₂ is small, the combustion wave does not propagate and the dielectric ceramics cannot be synthesized There is. Further, Ti powder having a specific surface area exceeding 2 m ² / g is not preferable because it is very active and difficult to handle.
In the present invention, the specific surface area of Ti powder is a value measured by the BET method.

The Ti fine powder that can be used for the combustion synthesis has a difference in reactivity when the specific surface area is different even if the average particle diameter is the same. That is, when a metal powder having a specific surface area larger than that of a spherical shape was used, the combustion synthesis reaction proceeded more rapidly. As the shape having a large specific surface area, there are a particle having a plurality of irregularities formed on the surface of a spherical particle, a particle having an irregular shape as a whole, or a combination thereof.
The average particle size that can be used in the present invention is 150 μm or less, preferably 0.1 to 100 μm. If it exceeds 150 μm, mixing with other raw materials becomes insufficient, and combustion waves may not propagate.
An image analysis method is preferable as a method for measuring the average particle diameter of particles having irregularities formed on the surface or an irregular shape.

Nd ₂ O ₃ is used as a source of Nd, which is a rare earth element. The rare earth element contributes to improving temperature characteristics such as reducing the temperature change of the relative dielectric constant.
Further, it is preferable to use TiO ₂ (titanium oxide) which is an oxide of Ti. A metal oxide such as TiO ₂ acts as a reaction diluent in the combustion synthesis reaction, and the adiabatic flame temperature can be controlled by adjusting the blending amount of the metal oxide. Specifically, when the blending ratio of TiO ₂ is increased, the reaction progress rate is lowered and the adiabatic flame temperature is lowered. Since TiO ₂ consists only of the elements constituting the target dielectric ceramic of the present invention, no by-product is produced even when used together. Further, in general, purification is necessary to form a simple metal, and the cost of Ti powder is high. Therefore, the combined use of the Ti powder and TiO ₂ has an effect of reducing the cost.

BaO ₂ is used as the Ba supply source. The BaO ₂ is not only a Ba supply source but also an oxygen supply source. BaCO ₃ can also be used as a Ba supply source.

In the present invention, a substance serving as an oxygen supply source is blended together with the Ti powder, Nd ₂ O ₃ , TiO ₂ and BaO ₂ .
As the oxygen supply source, an ion-binding substance that generates oxygen by heating is blended. Examples of the ion binding substance include chlorates such as KClO ₃ , NaClO ₃ and NH ₄ ClO ₃ , perchlorates such as KClO ₄ , NaClO ₄ and NH ₄ ClO ₄ , and chlorites such as NaClO ₂ , Bromates such as KBrO ₃ , nitrates such as KNO ₃ , NaNO ₃ and NH ₄ NO ₃ , iodates such as NaIO ₃ and KIO ₃ , permanganates such as KMnO ₄ and NaMnO ₄ .3H ₂ O, Dichromates such as K ₂ Cr ₂ O ₇ , (NH ₄ ) ₂ Cr ₂ O ₇ , periodates such as NaIO ₄ , metaiodic acids such as HIO ₄ · 2H ₂ O, CrO _3, etc. Anhydrochromates, nitrites such as NaNO ₃ , calcium hypochlorite trihydrate such as Ca (ClO) ₂ .3H ₂ O, and the like.
Among these, perchlorates, chlorates, and chlorites are preferable. Particularly, NaClO ₄ and KClO ₄ are preferable because NaCl and KCl, which are by-products, can be removed by repeatedly washing with pure water. is there. In the case of perchlorates, the generated carbon dioxide gasifies, so it does not remain in the synthetic powder.

反応希釈剤としてＴｉＯ₂を含む場合には、上記式（１）において x≠10 である。x＝1である場合、Ｔｉ粉末量が少なく発熱源が不足するため、燃焼波が伝播せず焼結体を得ることができない。また、ＴｉＯ₂を完全に含有しない場合（x＝10）では、反応が急激に進行し、合成粉がチャンバー内に飛散するため、合成粉の回収が困難となる場合がある。
各反応原料を所定割合で配合するとは、上記式を満たすモル質量比で配合することをいう。すなわち、Ｔｉ粉末の配合モル質量を x モルとすると、ＴｉＯ₂は（10-x）モル、ＮａＣｌＯ₄は(x-1)/2モルとなり、Ｔｉ粉末の配合モル質量に関係なく、ＢａＯ₂は 2 モル、Ｎｄ₂Ｏ₃は 2 モル配合する。
この割合で各反応原料を配合して燃焼合成することにより、目的のＢａＮｄ₂Ｔｉ₅Ｏ₁₄を容易に短時間で得ることができる。また、副生成物もＮａＣｌのみであり、後述する水洗浄により容易に分離することができる。 The dielectric ceramic of the present invention is obtained by a combustion synthesis method in which each of the reaction raw materials is blended at a predetermined ratio and then the adiabatic flame temperature is 1500 ° C. or higher. The chemical reaction formula for synthesizing BaNd ₂ Ti ₅ O ₁₄ , which is a specific example of the dielectric ceramic of the present invention, is as shown in the following formula (1).

When TiO ₂ is included as a reaction diluent, x ≠ 10 in the above formula (1). When x = 1, since the amount of Ti powder is small and the heat source is insufficient, the combustion wave does not propagate and a sintered body cannot be obtained. When TiO ₂ is not completely contained (x = 10), the reaction proceeds rapidly and the synthetic powder is scattered in the chamber, which may make it difficult to collect the synthetic powder.
Mixing each reaction raw material at a predetermined ratio means mixing at a molar mass ratio satisfying the above formula. That is, assuming that the blending molar mass of Ti powder is x moles, TiO ₂ is (10-x) moles, NaClO ₄ is (x-1) / 2 moles, and BaO ₂ is 2 moles and 2 moles of Nd ₂ O ₃ are blended.
The target BaNd ₂ Ti ₅ O ₁₄ can be easily obtained in a short time by blending each reaction raw material at this ratio and performing combustion synthesis. Further, the by-product is only NaCl and can be easily separated by water washing described later.

As described above, the blending ratio of Ti powder and TiO ₂ is determined by the value of x in the above formula (1). A preferable range of x during the synthesis of BaNd ₂ Ti ₅ O ₁₄ is 2 ≦ x ≦ 8. If x is less than 2, the heat generation source Ti powder is insufficient and the reaction diluent is too much TiO ₂ . There is. Also, if x exceeds 8, the amount of heat source is large and the reaction progresses rapidly, which may cause problems such as scattering.

反応希釈剤としてＴｉＯ₂を含む場合には、上記式（１）において x≠8 である。上記式（１）の場合と同様に、x＝1である場合、Ｔｉ粉末量が少なく発熱源が不足するため、燃焼波が伝播せず焼結体を得ることができない。また、ＴｉＯ₂を完全に含有しない場合（x＝8）では、反応が急激に進行し、合成粉がチャンバー内に飛散するため、合成粉の回収が困難となる場合がある。
この場合の配合割合は、Ｔｉ粉末の配合モル質量を x モルとすると、ＴｉＯ₂は（8-x）モル、ＮａＣｌＯ₄は(x-1)/2モルとなり、Ｔｉ粉末の配合モル質量に関係なく、ＢａＯ₂は 2 モル、Ｎｄ₂Ｏ₃は 2 モル配合する。該割合で各反応原料を配合して燃焼合成することにより、目的のＢａＮｄ₂Ｔｉ₄Ｏ₁₂を容易に短時間で得ることができる。また、副生成物もＮａＣｌのみであり、後述する水洗浄により容易に分離することができる。 As another specific example of the dielectric ceramic of the present invention, the chemical reaction formula in the case of synthesizing BaNd ₂ Ti ₄ O ₁₂ is as shown in the following formula (2).

When TiO ₂ is included as a reaction diluent, x ≠ 8 in the above formula (1). As in the case of the above formula (1), when x = 1, since the amount of Ti powder is small and the heat source is insufficient, the combustion wave does not propagate and a sintered body cannot be obtained. Further, when TiO ₂ is not completely contained (x = 8), the reaction proceeds rapidly and the synthetic powder is scattered in the chamber, which may make it difficult to collect the synthetic powder.
The mixing ratio in this case is (8-x) mol for TiO ₂ and (x-1) / 2 mol for NaClO _4, where x mol is the molar mass of the Ti powder, and is related to the molar mass of the Ti powder. 2 mol of BaO _{2 and} 2 mol of Nd ₂ O ₃ are blended. The target BaNd ₂ Ti ₄ O ₁₂ can be easily obtained in a short time by blending each reaction raw material at this ratio and performing combustion synthesis. Further, the by-product is only NaCl and can be easily separated by water washing described later.

As described above, the blending ratio of Ti powder and TiO ₂ is determined by the value of x in the above formula (2). A preferable range of x during the synthesis of BaNd ₂ Ti ₄ O ₁₂ is 2 ≦ x ≦ 6. If x is less than 2, the heat generation source Ti powder is insufficient and the reaction diluent is too much TiO ₂ . There is. In addition, if x exceeds 6, the amount of heat source is large and the reaction progresses rapidly, which may cause problems such as scattering.

In the step of blending the reaction raw materials at a predetermined ratio, mixing of the reaction raw materials can be used without any particular limitation such as mixing using a ball mill, a mortar and a pestle or the like. In particular, mixing using a ball mill excellent in mass productivity is preferable.
The mixed powder is put into a crucible and subjected to combustion synthesis. The material of the crucible is preferably a non-oxide such as carbon (C), silicon carbide (SiC), silicon nitride Si ₃ N ₄ or the like. Among these, a carbon (C) material is preferable because it is excellent in heat conduction and shape workability.
As a method for charging the mixed powder into the crucible, there can be used a method in which the mixed powder is spread in the form of a powder bed, compressed after being spread, or a powder that has been pressed and consolidated into a crucible.

The mixture blended at the predetermined ratio is reacted by the combustion synthesis method. Regarding the conditions of the combustion synthesis method, the adiabatic flame temperature of the reaction system is 1500 ° C. or higher. This is because the combustion wave propagates at 1500 ° C. or higher.
Combustion synthesis is performed in a chamber, and the atmosphere is preferably a rare gas atmosphere such as helium (He), neon (Ne), argon (Ar), or krypton (Kr). Note that a nitrogen gas, carbon dioxide atmosphere, or the like can be used as long as the dielectric properties of the reaction product are not deteriorated. Also, oxygen gas can be used if the oxygen partial pressure can be controlled.
The method for igniting the mixed powder for initiating combustion synthesis is not particularly limited as long as the metal powder can ignite and generate heat. A method in which a carbon film is ignited to generate heat and used as a heat source and brought into contact with the mixed powder to ignite and generate heat is preferable because it is excellent in handling. The combustion synthesis reaction is completed in about 1 to 60 seconds.

  The reaction product is agglomerated in the crucible. The pulverization of the reaction product is not particularly limited as long as the average particle diameter is 100 μm or less, and can be performed with a jet mill, a ball mill, a mortar and a pestle. When the average particle size exceeds 100 μm, the washing in the subsequent washing step becomes insufficient, and the ion-binding salt as a by-product tends to remain.

The fine powder after the pulverization step contains an ion-binding salt that is a by-product. For example, when NaClO ₄ is used as a raw material, NaCl is generated, and when KClO ₄ is used as a raw material, KCl is generated. These salts can be removed by washing with water.
When salts are present in the synthetic powder after the combustion synthesis reaction, the sinterability is hindered. As a standard for reducing the salt to such an extent that the sinterability is not hindered, the electrical conductivity of the cleaning liquid is 150 μS / cm or less. That is, regardless of the number of washings and the amount of washing, the electric conductivity of the washing water after washing should be 150 μS / cm or less when the synthetic powder is washed with water.

The electrical conductivity of water used for washing is preferably less than 50 μS / cm. When it is 50 μS / cm or more, the electrical conductivity of the cleaning liquid increases even if the amount of eluted ionic substances such as Na ⁺ and Cl ⁻ is sufficiently small. As the washing water having an electric conductivity of less than 50 μS / cm, pure water such as distilled water is particularly preferable for handling. The refined synthetic powder and cleaning liquid are put into a cleaning container, and ultrasonic cleaning is performed, and by-products are converted into ions such as Na ⁺ and Cl ⁻ and eluted in pure water. The removal amount can be increased by increasing the number of times the cleaning liquid is replaced or increasing the amount of the cleaning liquid with respect to the synthetic powder. In order to promote elution, it is also effective to raise the temperature of the cleaning solution. When the residual amount of the ionic substance as a by-product increases, it is not preferable because the ionic substance inhibits sintering when the ceramic powder is fired. As a technique for managing residual ionic substances, there is a measurement of electrical conductivity of a cleaning liquid. If the electric conductivity of the washing water after washing exceeds 150 μS / cm, the sinterability of the dielectric ceramic is hindered.

The synthetic powder is washed and dried and then sintered to obtain a dielectric ceramic. When sintering, a molding binder such as polyvinyl butyral can be blended. Examples of the sintering condition include a condition of molding at a pressure of 10 to 100 MPa and firing at a temperature of 1200 to 1500 ° C. in an air atmosphere.
Moreover, in order to further stabilize the crystal structure of the synthetic powder obtained by the combustion synthesis and to remove a trace amount of impurities, it is possible to calcine at 900 to 1100 ° C.

The resulting dielectric ceramics (BaNd ₂ Ti ₅ O ₁₄ , BaNd ₂ Ti ₄ O _12, etc.) are densified close to the theoretical density and have excellent dielectric properties, so that dielectric antennas, capacitors, dielectric resonators, Can be used for filters, pressure sensors, ultrasonic motors, etc.

Examples 1 to 7, Comparative Examples 1 to 3
Each reaction raw material was mixed at a molar ratio shown in Table 1 for 5 hours using a ball mill to obtain a mixed powder. A carbon crucible was installed in the chamber in the synthesizer, the mixed powder (100 g) was spread in the carbon crucible, and the ignition carbon film was brought into contact with a part of the mixed powder to close the chamber. After reducing the residual oxygen in the chamber using a vacuum pump, argon (Ar) gas was sealed, and the internal pressure of the chamber was set to 0.1 MPa.

Table 1 shows whether combustion synthesis is possible. The synthetic powder and by-product (NaCl) obtained were pulverized using an alumina mortar to obtain an unwashed dielectric ceramic powder having an average particle diameter of 1 μm.
The unwashed dielectric ceramic powder was sufficiently washed with water, and NaCl adhered to the powder was removed to obtain a dielectric ceramic.
The crystal phase of the obtained dielectric ceramic powder was identified using an X-ray diffractometer (XRD). The results are shown in Table 1. The relative dielectric constant and dielectric loss tangent were measured by the following methods.
1% by mass of a molding binder (polyvinyl butyral resin) was added to and mixed with the obtained dielectric ceramic powder. Next, the mixed powder was put into a 10 mm × 80 mm mold, and a pressure of 1.5 ton / cm ² was applied to obtain a green body (10 mm × 90 mm × 3 mm). The green body was held at 600 ° C. for 1 hour to remove organic components, and then fired at 1300 ° C. for 3 hours. The obtained sintered body was 70 mmxl. 5 mmxl. The sample was processed into a 5 mm test piece, and the dielectric constant and dielectric loss tangent were measured in the 1, 3, and 5 GHz frequency bands using the cavity resonator method. The results are shown in Table 2.

Examples 8 to 14 and Comparative Examples 4 to 6
Each reaction raw material was mixed at a molar ratio shown in Table 3 using a ball mill for 5 hours to obtain a mixed powder. A carbon crucible was installed in the chamber in the synthesizer, the mixed powder (100 g) was spread in the carbon crucible, and the ignition carbon film was brought into contact with a part of the mixed powder to close the chamber. After reducing the residual oxygen in the chamber using a vacuum pump, argon (Ar) gas was sealed, and the internal pressure of the chamber was set to 0.1 MPa.

Table 3 shows whether combustion synthesis is possible. The synthetic powder and by-product (NaCl) obtained were pulverized using an alumina mortar to obtain an unwashed dielectric ceramic powder having an average particle diameter of 1 μm.
The unwashed dielectric ceramic powder was sufficiently washed with water, and NaCl adhered to the powder was removed to obtain a dielectric ceramic.
The crystal phase of the obtained dielectric ceramic powder was identified using an X-ray diffractometer (XRD). The results are shown in Table 3. The relative dielectric constant and dielectric loss tangent were measured in the same manner as in Example 1. The results are shown in Table 4.

From Tables 1 and 3, the combustion waves propagated in all Examples, and BaNd ₂ Ti ₅ O ₁₄ could be obtained respectively. From Tables 2 and 4, the dielectric ceramics obtained in each example have excellent dielectric properties with a dielectric constant of 74 or more and a dielectric loss tangent of less than 0.001. Moreover, in each Example, since it can manufacture only by carrying out the combustion synthesis | combination after dry-type mixing, compared with the case where it manufactures by wet mixing and calcining, it can manufacture in a short time and low cost Moreover, Comparative Example 1 and Comparative Example 4 Then, since the specific surface area of Ti powder was smaller than 0.01, the combustion wave did not propagate and synthetic powder could not be obtained. In Comparative Example 2 and Comparative Example 5, since the adiabatic flame temperature was lower than 1500 ° C., the combustion wave did not propagate and synthetic powder could not be obtained.

Since the dielectric ceramics of the present invention (BaNd ₂ Ti ₅ O ₁₄ , BaNd ₂ Ti ₄ O _12, etc.) are close to the theoretical density and have excellent dielectric properties, dielectric antennas, capacitors, and dielectric resonators Can be used for filters, pressure sensors, ultrasonic motors, etc.

Claims (6)

An oxide-based dielectric ceramic represented by a composition formula BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer),
Reactive materials containing at least a predetermined ratio of Ti powder having a specific surface area of 0.01 to ² m ² / g, Nd ₂ O ₃ , BaO ₂ , and an ion-binding substance serving as an oxygen supply source are blended in predetermined proportions, respectively. A dielectric ceramic obtained by a combustion synthesis method having a temperature of 1500 ° C. or higher.   The dielectric ceramic according to claim 1, wherein the ion binding substance is sodium perchlorate. 3. The dielectric ceramic according to claim 2, wherein m = 5 in the composition formula, and obtained by a reaction represented by the following formula (1) in the combustion synthesis method.

3. The dielectric ceramic according to claim 2, wherein m = 4 in the composition formula and obtained by a reaction represented by the following formula (2) in the combustion synthesis method.

The dielectric ceramic according to claim 1, wherein the reaction raw material contains TiO ₂ . A method for producing an oxide-based dielectric ceramic represented by a composition formula BaNd ₂ Ti _m O _{2m + 4} (where 3 ≦ m ≦ 7; m is an integer),
A step of blending a predetermined amount of reaction raw materials each including at least a Ti powder having a specific surface area of 0.01 to ² m ² / g, Nd ₂ O ₃ , BaO ₂ , and an ion-binding substance serving as an oxygen supply source;
A step of reacting the compound formulated at the predetermined ratio by a combustion synthesis method in which the adiabatic flame temperature is 1500 ° C. or higher;
Crushing the reaction product;
And a step of washing the pulverized powder with water.