JP2007258661A - Laminated ceramic capacitor and its manufacturing method - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a laminated ceramic capacitor in which high capacity and high insulation can be acquired even when dielectric powder of particulate is used, for thinning and multi-laminating a dielectric layer, and to provide a method for manufacturing it. <P>SOLUTION: As shown in a figure 1, in the laminated ceramic capacitor, the dielectric layer 5 is constituted by a material comprising a magnesium oxide by 0.5-5.0 mol.prt in terms of MgO as an accessory component to 100 mol.prt of BaTiO<SB>3</SB>, and a silicon oxide by 0.5-5 mol.prt in terms of SiO<SB>2</SB>, and resistance reduction rate of a grain boundary in the dielectric layer at measuring of AC impedance in before and after leaving in a high temperature loading condition of a temperature higher than the Curie temperature indicated by titanic acid barium crystal particles 9 mainly containing a BaTiO<SB>3</SB>constituting the dielectric layer 5, and of a voltage equal to or more than 1/3 of a rated voltage, is 1%/min or below. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

The present invention relates to a ceramic capacitor used in an electronic device, particularly to a multilayer ceramic capacitor having an internal electrode layer made of nickel or a nickel alloy, and a method for manufacturing the same.

The multilayer ceramic capacitor is configured by forming a capacitor main body constituted by alternately laminating dielectric layers and internal electrode layers, and forming an external electrode on an end surface of the capacitor main body where the internal electrode layer is exposed. 2. Description of the Related Art In recent years, dielectric layers and internal electrode layers have been made thinner and multi-layered in response to demands for smaller size and higher capacity. For the dielectric layer constituting such a multilayer ceramic capacitor, for example, a dielectric material mainly composed of BaTiO ₃ is used. On the other hand, a base metal such as Ni is preferably used for the internal electrode in terms of low cost. It has been. When a base metal such as Ni is used for the internal electrode layer, firing is usually performed in a hydrogen-nitrogen mixed gas atmosphere. However, in such an atmosphere, the dielectric layer is reduced and becomes a semiconductor. was there.

  In order to solve such a problem, for example, a dielectric material (for example, Patent Document 1) in which the ratio of barium sites to titanium sites in the barium titanate powder is larger than the stoichiometric ratio, or barium titanate A dielectric material in which additives such as MnO, rare earth element oxides, and MgO are added to powder has been proposed (for example, Patent Document 2).

  The proposed dielectric material has high resistance to reduction and exhibits a high relative dielectric constant, so that it can be suitably used for multilayer ceramic capacitors having a dielectric layer having a thickness of 10 μm or more that has been mass-produced so far. I came. However, for a dielectric layer having a thickness of less than 10 μm like a recent multilayer ceramic capacitor, the above-mentioned dielectric material is likely to grow grains, and the number of crystal grains existing in one layer of the dielectric layer is reduced. As a result, there is a problem that the insulation property is lowered and reliability such as a high temperature load life test cannot be obtained.

Therefore, in recent years, a novel dielectric material having a high relative dielectric constant and high insulation even when the thickness of the dielectric layer is made thinner than 10 μm has been further proposed (for example, Patent Document 3). The dielectric material disclosed in Patent Document 3 has a content of alkali metal oxides contained as impurities in the main component barium titanate powder (BT powder) of 0.02 wt% or less. Two or more rare earth elements having different ionic radii of at least one selected from scandium oxide and yttrium oxide and at least one selected from gadolinium oxide, terbium oxide and dysprosium oxide for BT powder The oxide is added.
Japanese Examined Patent Publication No. 57-42588 Japanese Patent Laid-Open No. 61-101458 JP-A-10-223471

  However, even if the dielectric material disclosed in Patent Document 3 is used, the ratio of the dielectric layer when the BT powder is further atomized in order to apply the thickness of the dielectric layer to 2 μm or less. The dielectric constant decreases greatly and a high capacitance cannot be obtained. Also, as described above, even when two or more rare earth elements are added, grain growth occurs, the dielectric layer's insulating properties decrease, and the high temperature load life There was a problem that reliability could not be obtained in the test.

  SUMMARY OF THE INVENTION Accordingly, an object of the present invention is to provide a multilayer ceramic capacitor and a method for producing the same, which can obtain a high capacity and high insulation even when the dielectric layer is thinned to achieve multi-stacking.

The multilayer ceramic capacitor of the present invention includes a plurality of dielectric layers composed of barium titanate-based crystal particles, a plurality of internal electrode layers formed between the dielectric layers, and electrically connected to the internal electrode layers. In addition, the dielectric layer includes 0.5 to 5 mole parts of silicon oxide as a subcomponent with respect to 100 mole parts of barium titanate (BaTiO ₃ ) in terms of SiO _2. In addition, the AC impedance measurement in the AC impedance measurement before and after being left in a high temperature load state at a temperature higher than the Curie temperature and 1/3 or more of the rated voltage that the barium titanate-based crystal particles constituting the dielectric layer show The resistance reduction rate of the grain boundary in the dielectric layer is 1% / min or less.

In the multilayer ceramic capacitor, the dielectric layer includes barium titanate crystal particles containing Ca at a ratio of 0.2 atomic% or less and barium calcium titanate crystal particles having a Ca component concentration of 0.4 atomic% or more. Barium titanate-based crystal particles mixed, at least one of scandium oxide and yttrium oxide, at least one selected from gadolinium oxide, terbium oxide, dysprosium oxide, holmium oxide, erbium oxide, ytterbium oxide, and manganese oxide Of the barium titanate-based crystal particles, the average particle diameter of the barium titanate crystal particles having a Ca component concentration of 0.2 atomic% or less is D1, and the titanium having a Ca component concentration of 0.4 atomic% or more. When the average particle diameter of the barium calcium oxide crystal particles is D2, 1 is 0.13 to 0.15 μm, D2 / D1 is 1.3 to 1.92, and among the barium titanate-based crystal particles, barium calcium titanate having a Ca component concentration of 0.4 atomic% or more. When the crystal particles are represented by the chemical formula Ba _1-x Ca _x TiO ₃ (x = 0.01 to 0.2), the total amount of Ba and Ca is A mole, and Ti is B mole, A / B ≧ It is desirable to satisfy the relationship of 1.003.

The manufacturing method of the multilayer ceramic capacitor of the present invention is a multilayer ceramic that fires a capacitor body molded body that is formed by alternately laminating green sheets containing a dielectric powder mainly composed of BaTiO ₃ and an organic resin and internal electrode patterns. In the method for producing a capacitor, the dielectric powder is used as a subcomponent with respect to 100 mol parts of BaTiO ₃ , and the first composite oxide having a melting point of 1000 ° C. or higher and the second composite oxide having a melting point lower than 1000 ° C. are combined. It is characterized by adding 0.5 to 5 mole parts.

In the method for producing the multilayer ceramic capacitor, Ba and Ca in the barium calcium titanate (Ba _1-x Ca _x TiO ₃ : x = 0.01 to 0.2) powder are used as the dielectric powder mainly composed of BaTiO _3. When the total amount of A is A mole and Ti is B mole, a material satisfying the relationship of A / B ≧ 1.003 is used. As the dielectric powder mainly composed of BaTiO ₃ , barium titanate (BaTiO 3). ₃ ) In a barium titanate powder mixed with a powder and a barium calcium titanate (Ba _1-x Ca _x TiO ₃ x = 0.01 to 0.2) powder containing a Ca component, in scandium oxide and yttrium oxide At least one first rare earth powder selected from the group consisting of gadolinium oxide, terbium oxide, dysprosium oxide, and hormiu oxide Or at least one second rare earth powder selected from erbium oxide and ytterbium oxide. As the first composite oxide, BaO is 25 to 35 mol%, CaO is 15 to 25 mol%, SiO ₂ has a composition of 45 to 55 mol%, and as the second composite oxide, SiO ₂ is 75 to 90 _mol%, B 2 _{O 3} sol having a composition of 10 to 25 mol% - using gel glass it, as the first composite oxide, BaO 25 to 35 mol%, CaO 15 to 25 mol%, SiO ₂ has a composition of 45 to 55 mol%, and as the second composite oxide, BaO There 20-30 mol%, CaO is 10-15 mol%, SiO ₂ 30 to 50 mol% and Li ₂ O sol having a composition of 10 to 30 mol% - it is desirable to use a gel glass

According to the present invention, the dielectric layer mainly composed of BaTiO ₃ is in a high temperature load state at a temperature higher than the Curie temperature indicated by the crystal particles and a voltage equal to or higher than 1/3 of the rated voltage of the multilayer ceramic capacitor. When left as it is, the resistance reduction rate of the grain boundary in the dielectric layer in the AC impedance measurement before and after that is 1% / min or less, and since the grain boundary is highly insulative in this way, high insulation is achieved. Thus, high reliability can be obtained in the high temperature load life test.

  According to the method for producing a multilayer ceramic capacitor of the present invention, the first composite oxide having a melting point of 1000 ° C. or higher and the second composite oxide having a melting point lower than 1000 ° C. are added as the additive that becomes the grain boundary phase of the dielectric ceramic. By using a total amount of 0.5 to 5 mol% added, a high-capacity, high-insulating multilayer ceramic capacitor having the above-described configuration can be easily obtained.

  The multilayer ceramic capacitor of the present invention will be described in detail based on the schematic sectional view of FIG. FIG. 1 is a schematic sectional view showing a multilayer ceramic capacitor of the present invention. The enlarged drawing of the drawer is a schematic diagram showing crystal grains and grain boundary phases constituting the dielectric layer. In the multilayer ceramic capacitor of the present invention, external electrodes 3 are formed at both ends of the capacitor body 1. The external electrode 3 is formed, for example, by baking Cu or an alloy paste of Cu and Ni. The capacitor body 1 is configured by alternately laminating dielectric layers 5 and internal electrode layers 7. The dielectric layer 5 is composed of barium titanate crystal grains 9 and a grain boundary phase 11. The thickness is preferably 2 μm or less, particularly 1.5 μm or less in order to reduce the size and capacity of the multilayer ceramic capacitor.

The internal electrode layer 7 is preferably a base metal such as nickel (Ni) or a nickel alloy in that the manufacturing cost can be suppressed even if the internal electrode layer 7 is highly laminated, and in particular, nickel (Ni) in that the simultaneous firing with the dielectric layer 5 can be achieved. Ni) is more desirable. As the crystal particles 9 mainly composed of BaTiO ₃ constituting the dielectric layer 5, in addition to the barium titanate crystal particles having a perovskite structure composed of crystal particles mainly composed of BaTiO ₃ , the Ca component concentration Barium titanate crystal particles having different perovskite type structures are desirable. In particular, barium titanate crystal particles (BCT crystal particles) 9a coexist with barium titanate crystal particles (BT crystal particles) 9b not containing substituted Ca. A thing is more preferable at the point which raises a dielectric constant. Here, the BT crystal particles 9b are barium titanate crystal particles having a Ca component concentration of 0.2 atomic% or less, while the BCT crystal particles 9a have a Ca component concentration of 0.4 atomic% or more, in particular, BCT crystal particles. In view of maintaining the function as a ferroelectric having a high relative dielectric constant of 9a, it is desirable that the Ca component concentration be 0.5 to 2.5 atomic% of barium titanate crystal particles. In this case, the content of the alkali metal oxide contained as an impurity is preferably 0.02% by weight or less from the viewpoint that high insulation can be maintained.

  The average particle diameter of the barium titanate-based crystal particles 9 is preferably 0.2 μm or less and d90 is 0.4 μm or less in terms of achieving high capacity and high insulation by thinning the dielectric layer 5. . d90 is a 90% cumulative cumulative value by mass in the particle size distribution. On the other hand, the lower limit of the particle size of the BCT crystal particles 9a and the BT crystal particles 9b is 0.07 μm or more because the dielectric constant of the dielectric layer 5 is increased and the temperature dependence of the dielectric constant is suppressed. preferable.

  Further, among the barium titanate crystal particles 9, the average particle diameter of the barium titanate crystal particles (BT crystal particles) 9b having a Ca component concentration of 0.2 atomic% or less is D1, and the Ca component concentration is 0.4 atomic%. When the average particle diameter of the barium calcium titanate crystal particles (BCT crystal particles) 9a is D2, D1 is 0.13 to 0.15 μm, and D2 / D1 is 1.3 to 1.92. desirable. By setting the average particle diameter of the BT crystal particles 9b within the above range, the relative dielectric constant is increased. Further, the ratio D2 / D1 between the average particle diameter D1 of the BT crystal particles 9b and the average particle diameter D2 of the BCT crystal particles 9a is set. In the above range, the temperature characteristics of the relative dielectric constant can be stabilized in addition to the high dielectric constant, and the high temperature load life can be increased.

Here, the BCT crystal particle 9a which is one crystal particle constituting the crystal particle 9 is a perovskite-type barium titanate in which a part of the A site is substituted with Ca as described above, and ideally (Ba _1-x Ca _x ) TiO ₃ In the present invention, the amount of Ca substitution in the A site in the BCT crystal particles 9a is preferably X = 0.01 to 0.2, particularly preferably X = 0.02 to 0.07. If the Ca substitution amount is within this range, the phase transition point near room temperature is shifted to a sufficiently low temperature side, and the coexistence structure with the BT crystal particles 9b makes it possible to use the capacitor as an excellent temperature characteristic and AC bias in the temperature range. This is because the characteristics can be secured. The dielectric ceramic composed of BCT crystal particles 9a has a relative dielectric constant increase rate of more than twice when an AC bias is applied, compared to a dielectric ceramic composed only of BT crystal particles. A mixture of crystal particles 9b and BCT crystal particles 9a exhibits a high dielectric constant even if it is a fine particle.

On the other hand, the BT crystal particles 9b are barium titanate having a perovskite structure that does not contain substituted Ca, and are ideally represented by BaTiO ₃ . In the present invention, the BT crystal particles 9b have an analytical Ca concentration of 0.2 atomic% or less.

In the present invention, the BCT crystal particles 9a and BT crystal particles 9b constituting the barium titanate-based crystal particles 9 of the dielectric layer 5 are cross-sections of the dielectric layer 5 in the evaluation based on the index when the Ca concentration is defined. Or, when the ratio of the BCT crystal particles 9a is A _BCT and the ratio of the BT crystal particles 9b is A _{BT in} the area ratio of each crystal particle in the surface crystal structure, A _BT / A _BCT = 0.1-3 it is desirable to coexist in a tissue proportions with the relationship, in particular, dielectric constant, in that to further improve the temperature characteristics and the DC bias _{characteristics, a BT /} a BCT = 0.3~2 preferably . In addition, according to the present invention, the ratio of the A site of barium or Ca and the B site of titanium in the barium titanate constituting the barium titanate crystal grain 9 satisfies the relationship of A / B ≧ 1.003. It is preferable for the reason of suppressing.

Further, each of the BCT crystal particles 9a and the BT crystal particles 9b contains two or more kinds of rare earth elements shown below. The rare earth element includes one of scandium oxide and yttrium oxide, and at least one element selected from gadolinium oxide, terbium oxide, dysprosium oxide, holmium oxide, erbium oxide, and ytterbium oxide. It is more preferable to select yttrium oxide and terbium oxide because the dielectric constant of the barium-based crystal particles 9 is increased, the temperature characteristics of the dielectric constant are stabilized, and high insulation properties can be maintained. The range of yttrium oxide: terbium oxide = 0.5-2 (mole): 0.1-0.5 (mole) is more preferable. The content of the rare earth element is preferably 0.5 to 3 mole parts in total with respect to 100 mole parts of crystal grains mainly composed of BaTiO ₃ .

The effect of yttrium oxide and terbium oxide can be explained as follows. These rare earth elements are 2s and 2p of O (oxygen), which is a source of ferroelectricity of perovskite-type oxides such as barium titanate-based materials, and 3d and 4s of Ti (titanium) and energy levels are close to each other. By using a rare earth having an outermost electron orbit of 5p or more that does not disturb the hybridization with 4p, the dielectric constant of the dielectric ceramic is improved. The effect of rare earth elements on the characteristics of the dielectric ceramic is obtained by performing X-ray spectroscopic analysis on the dielectric ceramic and evaluating the peak intensity in the vicinity of 24 eV derived from the 4p orbit. Actually, in the X-ray spectroscopic analysis chart, the intensity of 0 eV to the intensity of 50 eV is connected to form a baseline, and the intensity of the main peak seen in the vicinity of 36 eV obtained by subtracting the intensity value for the baseline is the same. The intensity ratio of 24 eV obtained by subtracting the intensity value for the baseline is P2 / P1 ≦ 0.25 for Tb ₂ O ₃ , whereas P ₂ /P1>0.25 for Y ₂ O ₃ . Thus, when P2 / P1> 0.25, the 2s and 2p of O, which is the source of the ferroelectricity of the perovskite oxide, disturbs the hybridization of Ti and 3d, 4s and 4p, which are close to the energy level. Although the dielectric constant decreases, Tb ₂ O ₃ is P2 / P1 ≦ 0.25, so that 2s and 2p of O, which are the sources of ferroelectricity of the perovskite oxide, 3d and 4s of Ti, and This is because disturbing hybridization with 4p, which is close to the energy level, is suppressed.

In addition, the dielectric layer 5 in the multilayer ceramic capacitor of the present invention preferably contains MgO or MnO in addition to the rare earth element oxide. The content of MgO and MnO contained in the crystal grains 9 is BaTiO ₃ . If MgO = 0.5-2 mol parts and MnO = 0.2-0.5 mol parts with respect to 100 mol parts of the main crystal particles, the temperature characteristics of the capacitance can be further stabilized and insulated. And the reliability in the high temperature load test is improved.

  Since these MgO, rare earth element oxide and MnO are derived from the sintering aid, the oxides of these elements are dissolved in the BCT crystal particles 9a and BT crystal particles 9b, but some of them are grains. It is likely to exist in the phase 11 as an amorphous material.

  In the dielectric layer 5 in the multilayer ceramic capacitor of the present invention, MgO and rare earth element oxide are components dissolved in the vicinity of the surfaces of the BT crystal particles 9b and the BCT crystal particles 9a to form a core-shell structure, while Mn is reduced. It is possible to compensate for oxygen defects in the BT crystal particles 9b and the BCT crystal particles 9a generated by firing in the atmosphere, and to improve insulation and high temperature load life.

  The barium titanate crystal particles 9 constituting the dielectric layer 5 of the multilayer ceramic capacitor of the present invention will be further described. The dielectric layer 5 is a system in which BCT crystal particles 9a and BT crystal particles 9b coexist. The BCT crystal particles 9a and the BT crystal particles 9b form a core-shell structure in which MgO derived from the sintering aid and oxides of rare earth elements are unevenly distributed on the particle surface side from the particle center. 9b shows a large relative dielectric constant exceeding 4000 due to the atomic fluctuation accompanying the sequential phase transition, but because of the high relative dielectric constant resulting from the atomic fluctuation, which is a precursor of the sequential phase transition, a DC bias is applied. As the relative dielectric constant decreases greatly due to the decrease in the particle size, the effect becomes smaller. Of the three sequential phase transition points found in BT crystal grains, the phase transition temperature at the highest temperature (about 125 ° C) remains almost unchanged even when part of the A site is replaced with Ca, but is near room temperature. The structural phase transition point at a lower temperature than that shifts to a lower temperature in proportion to an increase in the amount of substituted Ca. That is, in the BCT crystal particle 9a in which a part of the A site is substituted with Ca, the transition point at a temperature near room temperature and lower than that is shifted to a low temperature side and the relative permittivity is reduced, but the AC bias characteristic is Since the dielectric constant is greatly improved, the relative dielectric constant is improved. That is, the dielectric layer 5 constituting the multilayer ceramic capacitor of the present invention has a high relative dielectric constant, and realizes a coexistence structure of the BT crystal particles 9b having excellent temperature characteristics and the BCT crystal particles 9a having excellent AC bias characteristics. As a result, the AC bias characteristics are excellent compared to the BT crystal particles 9b and the dielectric constant is high, and the temperature dependence of the dielectric characteristics is small.

Further, the dielectric layer 5 in the multilayer ceramic capacitor of the present invention is obtained by converting silicon oxide into SiO ₂ as a component of the grain boundary phase 11, and 0.5 to 5 mol with respect to 100 mol parts of crystal grains mainly composed of BaTiO _3. It is characterized by containing a part. In the dielectric layer 5 having such a composition, it is important that the grain boundary phase 11 has the following physical structure. This allows the dielectric layer 5 to have a high relative dielectric constant and maintain high insulating properties, and can enhance resistance in an accelerated test. .

  FIG. 2 is a schematic diagram showing a method for evaluating the resistance of the grain boundary in the dielectric layer 5 using AC impedance measurement in the multilayer ceramic capacitor of the present invention. In FIG. 2, 20a is a thermostatic chamber for controlling the temperature by mounting a multilayer ceramic capacitor as a sample, 20b is a HALT measuring device for applying a DC voltage to the sample, and 20c is an impedance measuring device having an AC power source. In the present invention, the multilayer ceramic capacitor is in a high temperature load state at a temperature higher than the Curie temperature indicated by the perovskite-type barium titanate crystal particles 9 constituting the dielectric layer 5 and a voltage equal to or higher than 1/3 of the rated voltage of the multilayer ceramic capacitor. Leave it alone. In this case, the test is performed by changing the standing time. Then, AC impedance measurement under the same conditions is performed before and after being left in a high temperature load condition under the above-described conditions, and the resistance reduction rate of the grain boundary phase 11 in the dielectric layer 5 is measured. The resistance change rate can be evaluated as a time dependence (amount of change per unit time) by evaluating a plurality of samples with different standing times.

  FIG. 3 shows the impedance at the core (center portion), shell (outer peripheral portion), grain boundary phase 11 and interface between the internal electrode layer 7 and the dielectric layer 5 of the barium titanate crystal grains 9 in the multilayer ceramic capacitor of the present invention. It is a graph of change (Cole-Cole plot). In this evaluation, the dielectric layer 5 is divided into the four components of the core (center portion), the shell (outer peripheral portion), the grain boundary phase 11 and the interface between the internal electrode 7 and the dielectric layer 5 as shown in the equivalent circuit of the figure. To do. The horizontal axis of the graph indicates the real part of the impedance signal, and the vertical axis indicates the imaginary part. The graph showing the change in impedance is the difference between before and after the accelerated life test (HALT) and the fitting by simulation. The evaluation according to the present invention pays attention to the resistance change in the grain boundary phase 11, and it is important that the rate of change of the real part is 1% / min or less. When the rate of change of resistance exceeds 1% / min, the reliability of the high temperature load life is low. In the above evaluation, for example, the Cole-Cole plot of FIG. 3 before and after the accelerated life test (HALT) is performed by using dedicated software for the core (center part), shell (outer peripheral part), grain boundary phase 11 and internal electrode 7 and dielectric layer. It can be obtained by dividing it into four components at the interface with 5. Here, the temperature is the Curie temperature in that the diffusion of ions and the movement of electrons in the dielectric layer 5 before and after the high-temperature load atmosphere treatment are increased, and the resistance reduction rate of the grain boundary phase 11 can be seen remarkably. 1.5 times the voltage is preferably 2 / 5V or more of the rated voltage.

  Next, a method for producing the multilayer ceramic capacitor of the present invention will be described in detail. FIG. 4 is a process diagram showing a method for producing the multilayer ceramic capacitor of the present invention.

  Step (a): In the production method of the present invention, first, a ceramic slurry is prepared by using a ball mill or the like together with the following raw material powder together with an organic resin such as polyvinyl butyral resin and a solvent such as toluene and alcohol. The ceramic green sheet 21 is formed using a sheet forming method such as a doctor blade method or a die coater method. The thickness of the ceramic green sheet 21 is preferably 1 to 3 μm from the viewpoint of reducing the thickness of the dielectric layer 5 for increasing the capacity and maintaining high insulation.

Perovskite-type barium titanate powder (BCT powder) in which a part of the A site used in the production method of the multilayer ceramic capacitor of the present invention is substituted with Ca, and perovskite-type barium titanate powder (BT powder) not containing substituted Ca dielectric powder is is a raw material powder represented by the respective _{(Ba 1-x Ca x)} TiO 3 and BaTiO _3. Here, the Ca substitution amount in the A site in the BCT powder is preferably X = 0.01 to 0.2, particularly preferably X = 0.03 to 0.1. Further, in this BCT powder, the atomic ratio A / B between the A site (barium) and the B site (titanium), which are constituent components, is preferably 1.003 or more, and particularly preferably 1.003 to 1.009. When the atomic ratio A / B between the A site (barium) and the B site (titanium) of the BCT powder is 1.003 or more, the grain growth of the BCT crystal particles 9a can be suppressed, resulting in high insulation and improved high temperature load life. it can. In addition, it is preferable that content of the alkali metal oxide contained as an impurity is 0.02 mass% or less.

  These BT powder and BCT powder are synthesized by mixing a compound containing a Ba component, a Ca component and a Ti component so as to have a predetermined composition. These dielectric powders are obtained by a synthesis method selected from a solid phase method, a liquid phase method (including a method of producing via oxalate), a hydrothermal synthesis method, and the like. Among these, the dielectric powder obtained by the hydrothermal synthesis method is desirable because the particle size distribution of the obtained dielectric powder is narrow and the crystallinity is high.

  The particle size distribution of the barium titanate powder (BT powder) and the barium calcium titanate powder (BCT powder), which are dielectric powders used in the method of manufacturing the multilayer ceramic capacitor of the present invention, facilitates thinning of the dielectric layer 5 and In terms of increasing the dielectric constant of the dielectric powder, it is preferably 0.05 to 0.3 μm. In this case, the average particle size of the BT powder is 0.05 to 0.2 μm, while the average particle size of the BCT powder is The diameter is preferably 0.1 to 0.3 μm. In the mixture of these two powders, it is preferable to use a BCT powder and a BT powder in which the BCT powder is larger in that the dielectric layer can have a higher dielectric constant after firing.

  Further, the rare earth element added to the dielectric powder is preferably 0.5 to 3 mole parts in terms of oxide with respect to 100 mole parts of dielectric powder which is a mixture of BCT powder and BT powder, As the rare earth element oxide powder, it is more preferable to use a mixture of the first rare earth powder and the second rare earth powder.

  Further, MgO is 0.5 to 1 mole part relative to 100 mole parts of dielectric powder which is a mixture of BCT powder and BT powder, and MnO is 100 moles of dielectric powder which is a mixture of BCT powder and BT powder. It is preferable that it is 0.2-0.5 mol part with respect to a part.

In addition, the sintering aid added to these dielectric powders is a dielectric comprising a mixture of BCT powder and BT powder, the first composite oxide having a melting point of 1000 ° C. or higher and the second composite oxide having a melting point lower than 1000 ° C. it is obtained by adding 0.5 to 5 molar parts in terms of SiO ₂ with respect to the body powder 100 parts by mol. In this case, as the first composite oxide, BaO 25 to 35 mol%, CaO 15 to 25 mol%, SiO ₂ has a composition of 45 to 55 mol%, and as the second composite oxide, It is desirable to use a sol-gel glass having a composition of 75 to 90 mol% of SiO _{2 and} 10 to 25 mol% of B ₂ O ₃ . In other words, these sintering aids are used by mixing a high melting point first composite oxide having a melting point of 1000 ° C. or higher and a low melting point second composite oxide having a melting point lower than 1000 ° C. The first composite oxide having a high melting point with a melting point of 1000 ° C. or higher causes a sudden drop in viscosity after reaching the high temperature range in the firing stage, so that the sintering aid is dissolved in the barium titanate powder. This can suppress grain growth. On the other hand, the second composite oxide having a low melting point lower than 1000 ° C. has a viscosity drop from the early stage of the firing step, so that it diffuses thinly and sufficiently on the surface of the barium titanate powder, and the barium titanate powder is fired. It can increase the ligation. When a mixture of sintering aids with different melting points is used, even if the barium titanate powder is fine, grain growth can be suppressed while maintaining high sinterability, and it can be obtained by firing the barium titanate powder. The insulation of the grain boundary phase of the dielectric layer 5 can be improved, and particularly the reliability such as the high temperature load life can be improved.

In the present invention, as the first composite oxide, BaO 25 to 35 mol%, CaO 15 to 25 mol%, SiO ₂ has a composition of 45 to 55 mol%, and the second composite oxide things as, BaO 20-30 mol%, CaO is 10-15 mol%, SiO ₂ 30 to 50 mol% and Li ₂ O sol having a composition of 10 to 30 mol% - it is desirable to use gel glass. When the BaO—CaO—SiO ₂ —Li ₂ O system is used as the first composite oxide, the melting point can be lowered as compared with the BaO—B ₂ O ₃ system, so the viscosity is increased from the early stage of the firing stage. It can be further reduced, and even if the addition amount is small, it can be thinly and sufficiently diffused on the surface of the barium titanate powder. For this reason, there is an advantage that the dielectric constant of the dielectric ceramic can be increased by the amount that the amount of additive can be reduced.

  (B) Step: Next, a rectangular internal electrode pattern 23 is printed and formed on the main surface of the ceramic green sheet 21 obtained above. The conductive paste to be the internal electrode pattern 23 is prepared by mixing Ni or an alloy powder thereof as a main component metal, mixing ceramic powder as a co-material with this, and adding an organic binder, a solvent and a dispersant. As the ceramic powder, a BT powder having a low Ca concentration is preferable. However, when the ceramic paste is contained in the conductor paste, the internal electrode layer 7 constituting the multilayer ceramic capacitor of the present invention penetrates through the internal electrode layer 7 and moves up and down. Columnar ceramics are formed so as to connect the dielectric layers 5. Thereby, peeling between the dielectric layer 5 and the internal electrode layer 7 can be prevented. The ceramic powder used here can suppress abnormal grain growth of columnar ceramics during firing and can increase mechanical strength.

  Further, by suppressing the abnormal grain growth of the columnar ceramics formed in the internal electrode layer 7, the capacitance temperature dependency of the multilayer ceramic capacitor can be reduced. The thickness of the internal electrode pattern 23 is preferably 1 μm or less because the multilayer ceramic capacitor is miniaturized and the steps due to the internal electrode pattern 23 are reduced.

  According to the present invention, the ceramic pattern 25 is formed around the internal electrode pattern 23 with substantially the same thickness as the internal electrode pattern 23 in order to eliminate the step due to the internal electrode pattern 23 on the ceramic green sheet 21. Is preferred. As the ceramic component constituting the ceramic pattern 25, it is preferable to use the dielectric powder used for the ceramic green sheet 21 in that the firing shrinkage in the simultaneous firing is the same.

  Step (c): Next, a desired number of ceramic green sheets 21 on which internal electrode patterns 23 are formed are stacked, and a plurality of ceramic green sheets 21 on which no internal electrode patterns 23 are formed are the same in upper and lower layers. A temporary laminated body is formed by overlapping the number of sheets. The internal electrode pattern 23 in the temporary laminate is shifted by a half pattern in the longitudinal direction. By such a laminating method, the internal electrode patterns 23 can be formed so as to be alternately exposed on the end faces of the cut laminate.

  In the manufacturing method of the multilayer ceramic capacitor of the present invention, as described above, the ceramic green sheet 21 is temporarily placed on the lower layer side in addition to the method of forming the internal electrode pattern 23 in advance on the main surface of the ceramic green sheet 21 and laminating it. Then, the internal electrode pattern 23 is printed and dried, and the ceramic green sheet 21 on which the internal electrode pattern 23 is not printed is overlaid on the printed and dried internal electrode pattern 23 to temporarily adhere. In addition, the ceramic green sheet 21 can be formed by a method in which the adhesion of the ceramic green sheet 21 and the internal electrode pattern 23 are sequentially printed.

  Next, the temporary laminated body is pressed under conditions of higher temperature and higher pressure than the temperature pressure during the temporary lamination to form a laminated body 29 in which the ceramic green sheet 21 and the internal electrode pattern 23 are firmly adhered.

  Next, the multilayer body 29 is cut along the cutting line h to form a capacitor body molded body in which the end portion of the internal electrode pattern 23 is exposed. In this case, cutting is performed in such a manner that the approximate center of the ceramic pattern 29 formed in the laminate 29 is perpendicular to the longitudinal direction of the internal electrode pattern 25 ((c1) in FIG. 4 and (c2) in FIG. 4). In parallel with the longitudinal direction of the internal electrode pattern 23, the process is performed. In this case, the internal electrode pattern 29 is exposed on the end margin side, but the internal electrode pattern 23 is not exposed on the side margin portion side.

  Next, this capacitor body molded body is fired under a predetermined atmosphere at a temperature condition to form a capacitor body. In some cases, the ridge line portion of the capacitor body 1 is chamfered and the capacitor body 1 faces the capacitor body 1. Barrel polishing may be performed to expose the internal electrode layer 7 exposed from the end face. In the manufacturing method of the multilayer ceramic capacitor of the present invention, degreasing is in the temperature range up to 500 ° C., the heating rate is 5 to 20 ° C./h, and the firing temperature is in the range of 1000 to 1250 ° C., from degreasing to the maximum temperature. Temperature rising rate is 200 to 500 ° C / h, holding time at maximum temperature is 0.5 to 4 hours, temperature decreasing rate from maximum temperature to 1000 ° C is 200 to 500 ° C / h, atmosphere is hydrogen-nitrogen, after firing It is preferable that the maximum temperature of the heat treatment (reoxidation treatment) is 900 to 1100 ° C. and the atmosphere is nitrogen.

  Next, an external electrode paste is applied to the opposite ends of the capacitor body 1 and baked to form the external electrode 1. A plating film is formed on the surface of the external electrode 3 in order to improve mountability.

A multilayer ceramic capacitor was produced as follows. Table 1 shows the amounts of barium titanate-based powder, rare earth powder and sintering aid used, and the firing temperature. The BT powder (BaTiO ₃ ) and BCT powder (Ba _1-x Ca _x TiO ₃ x = 0.05) used here had an A / B site ratio of 1 or 1.003. Further, as shown in Table 1, the particle sizes of BT powder and BCT powder were 0.07 to 0.23 μm. The BCT powder used here was one having a ratio C _high / C _ave = 2.3 where the highest concentration in the Ca concentration distribution in the powder was C _high and the average concentration was C _ave . This BCT powder having C _high / C _ave = 2.3 had C _high / C _ave = 2.1 after firing. The sintering aid includes BaO = 30, CaO = 20, and SiO ₂ = 50 (mol%) having melting points of 1050 ° C. as the first composite oxide, and the second composite oxide has melting point of 950 ° C. It was from _{SiO 2 = 90, B 2 O} 3 = 10 ( mol%). 1 mol part of MgO and 0.3 mol part of MnO were added in the form of MnCO ₃ with respect to 100 mol parts of the barium titanate powder. The average particle size of MgO was 0.2 μm, the average particle size of MnO was 0.2 μm, and the average particle size of the sintering aid was 0.3 μm.

  Next, the mixed powder was wet-mixed by adding a mixed solvent of toluene and alcohol as a solvent using zirconia balls having a diameter of 5 mm. Next, a polyvinyl butyral resin and a mixed solvent of toluene and alcohol are added to the wet-mixed powder, and the mixture is wet-mixed using zirconia balls having a diameter of 5 mm, and a ceramic slurry is prepared. A green sheet was produced.

  Next, a plurality of rectangular internal electrode patterns mainly composed of Ni were formed on the upper surface of the ceramic green sheet. The conductor paste used for the internal electrode pattern was Ni powder having an average particle size of 0.3 μm, and 30 parts by mass of BT powder used for the ceramic green sheet as a co-material was added to 100 parts by mass of Ni powder.

Next, 100 ceramic green sheets on which internal electrode patterns were printed were laminated, and 20 ceramic green sheets on which the internal electrode patterns were not printed were laminated on the upper and lower surfaces, respectively, and a temperature of 60 ° C. and pressure were used using a press. The layers were laminated together under the conditions of 10 ⁷ Pa and time 10 minutes, and cut into predetermined dimensions.

Next, the laminated molded body was subjected to binder removal treatment at 300 ° C./h in the air at a temperature rising rate of 10 ° C./h, and the temperature rising rate from 500 ° C. was 300 ° C./h. -Calcination in nitrogen at 1040-1200 ° C for 2 hours, followed by cooling to 1000 ° C at a temperature decrease rate of 300 ° C / h, reoxidation treatment at 1000 ° C for 4 hours in a nitrogen atmosphere, and temperature decrease of 300 ° C / h The capacitor body was manufactured by cooling at a speed. The capacitor body had a size of 1 × 0.5 × 0.5 mm ³ and the dielectric layer had a thickness of 1.8 μm. The area per internal electrode layer was 0.258 mm ² .

  Next, the fired capacitor body was barrel-polished, and then an external electrode paste containing Cu powder and glass was applied to both ends of the capacitor body and baked at 850 ° C. to form external electrodes. Thereafter, Ni plating and Sn plating were sequentially performed on the surface of the external electrode by using an electrolytic barrel machine to produce a multilayer ceramic capacitor.

The dielectric layer composing the produced multilayer ceramic capacitor has an area ratio of the respective crystal grains in the crystal structure of the cross section. When the ratio of BCT crystal grains is A _BCT and the ratio of BT crystal grains is A _BT , A _BT / A _BCT = 0.8 to 1.2. This was determined by observation with an analytical electron microscope. The photo magnification was 30000 times. Further, the rare earth element (yttrium) contained in the barium titanate crystal particles had a concentration gradient of 0.05 atomic% / nm from the crystal particle surface to the inside of the particle, with the grain boundary layer on the particle surface being the highest concentration. This was measured with an analyzer attached to the transmission electron microscope. The concentration distribution of the Ca component in the BCT crystal particles was also measured by the same method. The concentration distribution of the Ca component in the BCT crystal particles is measured by arbitrarily selecting 10 crystal particles in the dielectric layer, performing EDS analysis every 5 nm from the interface to the center of the crystal particles, and from the concentration distribution curve. Average concentration and maximum concentration were determined.

  Next, the following evaluation was performed on these multilayer ceramic capacitors. Capacitance, relative permittivity, and temperature characteristics of relative permittivity (X5R) were performed under measurement conditions of a frequency of 1.0 kHz and a measurement voltage of 0.5 Vrms. The relative dielectric constant was calculated from the capacitance, the effective area of the internal electrode layer, and the thickness of the dielectric layer.

  Moreover, the average particle diameter of the BT type crystal particles and the BCT type crystal particles constituting the dielectric layer was determined by a scanning electron microscope (SEM). The polished surface was etched, 20 crystal particles in an electron micrograph taken at a magnification of 30000 were arbitrarily selected, the maximum diameter of each crystal particle was determined by the intercept method, and the average value thereof was determined.

  Regarding the Ca concentration, an arbitrary place near the center was analyzed using a transmission electron microscope and EDS. At that time, dielectric particles having a high Ca concentration were used for those having a Ca concentration higher than 0.4 atomic% (rounded to the second decimal place). This analysis was performed on 100 to 150 main crystal particles.

  The composition of the dielectric layer is obtained by cutting a portion of the dielectric layer from the obtained multilayer ceramic capacitor, mixing the molten portion with boric acid and sodium carbonate, and dissolving it in hydrochloric acid to contain 1000 ppm of each element. A solution obtained by diluting the standard solution was quantified by ICP emission spectroscopic analysis as a standard sample.

  As an evaluation of the grain boundary phase as a high-temperature load test, it was separately measured using an alternating current impedance method. As high temperature load conditions in this case, the temperature was 250 ° C., and the voltage applied to the external electrode of the multilayer ceramic capacitor was 2 V / μm. The measurement voltage was 0.1 V, the frequency was between 10 mHz and 10 kHz, the standing time was 1 hour, and the AC impedance before and after the treatment was evaluated for 30 samples.

As a comparative example, when only BT powder was used as the barium titanate-based powder, the above-mentioned BT and BCT powders were used as the barium titanate-based powder. A product to which only a product was added and a product to which only a second composite oxide having a melting point lower than 1000 ° C. was added were prepared by the production method in the same manner as described above and evaluated in the same manner. The results are shown in Tables 1-4.

  As is clear from the results of Tables 1 to 4, 0.5 to 5 mole parts of the first composite oxide having a melting point of 1000 ° C. or higher and the second composite oxide having a melting point lower than 1000 ° C. are added in total. In the obtained sample of the present invention, the relative dielectric constant was 1890 or more, and the rate of change in the high temperature load life test was 1% / min or less. In the case where two kinds of Y and Tb were added simultaneously to the dielectric powder, the relative dielectric constant was 4000 or more. Further, among the barium titanate crystal particles, the average particle diameter D1 of the barium titanate crystal particles (BT crystal particles) having a Ca component concentration of 0.2 atomic% or less is set to 0.13 to 0.15 μm, and D2 / D1 Of sample Nos. In the range of 1.3 to 1.92. In 3, 4, 12, 14, 17, 18 and 27, the relative dielectric constant is 4350 to 5300, and the temperature change rate of the capacitance at 85 ° C. is −8.77% to −9.9%, Good characteristics with a high temperature load life of -0.6 to -0.9 were obtained. On the other hand, in the sample to which only one of the first composite oxide having a melting point of 1000 ° C. or higher or the second composite oxide having a melting point lower than 1000 ° C. is added, the relative permittivity is low or the change in the high temperature load life test The rate was greater than 1% / min.

As is apparent from the results of Tables 3 and 4, when the combined amount of the composite oxide is converted to SiO ₂ and exceeds 5.0 mole parts, a decrease in the dielectric constant is observed, and the high temperature The rate of change in the load life test was greater than 1% / min.

A multilayer ceramic capacitor was produced as follows. Table 1 shows the amounts of barium titanate-based powder, rare earth powder and sintering aid used, and the firing temperature. The BT powder (BaTiO ₃ ) and BCT powder (Ba _1-x Ca _x TiO ₃ x = 0.05) used here had an A / B site ratio of 1 or 1.003. Further, as shown in Table 1, the particle sizes of BT powder and BCT powder were 0.07 to 0.23 μm. The BCT powder used here had a ratio C _high / C _ave of 1.2 to 4 when the highest concentration in the Ca concentration distribution in the powder was C _high and the average concentration was C _ave . In this case, the BCT powder of C _high / C _ave = 1.2 to 1.5 was obtained by the coprecipitation method, and the BCT powder of C _high / C _ave = 2 to 4 was BaCO ₃ , TiO ₂ , It was obtained by a solid phase method using CaCO ₃ . The BCT powders in Tables 5 and 6 each have a C _high / C _ave of 2.3. The C _high / C _ave of the BCT crystal particles obtained from the BCT powder in the samples of Tables 5 and 6 was 2.1. Table 7, for samples in Table 8, as shown in Table _7, was C _high / C ave = 1.2~4. The sintering aid includes BaO = 30, CaO = 20, and SiO ₂ = 50 (mol%) having melting points of 1050 ° C. as the first composite oxide, and the second composite oxide has melting point of 800 ° C. BaO = 25, CaO = 15, SiO ₂ = 40, and Li ₂ O = 20 (mol%) were used. 1 mol part of MgO and 0.3 mol part of MnO were added in the form of MnCO ₃ with respect to 100 mol parts of the barium titanate powder. The average particle size of MgO was 0.2 μm, the average particle size of MnO was 0.2 μm, and the average particle size of the sintering aid was 0.3 μm.

  Next, the mixed powder was wet-mixed by adding a mixed solvent of toluene and alcohol as a solvent using zirconia balls having a diameter of 5 mm. Next, a polyvinyl butyral resin and a mixed solvent of toluene and alcohol are added to the wet-mixed powder, and the mixture is wet-mixed using zirconia balls having a diameter of 5 mm, and a ceramic slurry is prepared. A green sheet was produced.

  Next, a plurality of rectangular internal electrode patterns mainly composed of Ni were formed on the upper surface of the ceramic green sheet. The conductor paste used for the internal electrode pattern was Ni powder having an average particle size of 0.3 μm, and 30 parts by mass of BT powder used for the ceramic green sheet as a co-material was added to 100 parts by mass of Ni powder.

Next, 100 ceramic green sheets on which internal electrode patterns were printed were laminated, and 20 ceramic green sheets on which the internal electrode patterns were not printed were laminated on the upper and lower surfaces, respectively, and a temperature of 60 ° C. and pressure were used using a press. The layers were laminated together under the conditions of 10 ⁷ Pa and time 10 minutes, and cut into predetermined dimensions.

Next, the laminated molded body was subjected to binder removal treatment at 300 ° C./h in the atmosphere at a heating rate of 10 ° C./h, and the temperature rising rate from 500 ° C. was 300 ° C./h. -Calcination in nitrogen at 1040-1200 ° C for 2 hours, followed by cooling to 1000 ° C at a temperature decrease rate of 300 ° C / h, reoxidation treatment at 1000 ° C in nitrogen atmosphere for 4 hours, temperature decrease of 300 ° C / h The capacitor body was manufactured by cooling at a speed. The capacitor body had a size of 1 × 0.5 × 0.5 mm ³ and the dielectric layer had a thickness of 1.8 μm. The area per internal electrode layer was 0.258 mm ² .

  Next, the fired capacitor body was barrel-polished, and then an external electrode paste containing Cu powder and glass was applied to both ends of the capacitor body and baked at 850 ° C. to form external electrodes. Thereafter, Ni plating and Sn plating were sequentially performed on the surface of the external electrode by using an electrolytic barrel machine to produce a multilayer ceramic capacitor.

The dielectric layer composing the produced multilayer ceramic capacitor has an area ratio of the respective crystal grains in the crystal structure of the cross section. When the ratio of BCT crystal grains is A _BCT and the ratio of BT crystal grains is A _BT , A _BT / A _BCT = 0.8 to 1.2. This was determined by observation with an analytical electron microscope. Further, the rare earth element (yttrium) contained in the barium titanate crystal particles had a concentration gradient of 0.05 atomic% / nm from the crystal particle surface to the inside of the particle, with the grain boundary layer on the particle surface being the highest concentration. This was measured with an analyzer attached to the transmission electron microscope. The concentration distribution of the Ca component in the BCT crystal particles was also measured by the same method. The concentration distribution of the Ca component in the BCT crystal particles is measured by arbitrarily selecting 10 crystal particles in the dielectric layer, performing EDS analysis every 5 nm from the interface to the center of the crystal particles, and from the concentration distribution curve. Average concentration (C _ave ) and maximum concentration (C _high ) were determined.

  Next, the following evaluation was performed on these multilayer ceramic capacitors. Capacitance, relative permittivity, and temperature characteristics of relative permittivity (X5R) were performed under measurement conditions of a frequency of 1.0 kHz and a measurement voltage of 0.5 Vrms. The relative dielectric constant was calculated from the capacitance, the effective area of the internal electrode layer, and the thickness of the dielectric layer.

  Moreover, the average particle diameter of the BT type crystal particles and the BCT type crystal particles constituting the dielectric layer was determined by a scanning electron microscope (SEM). The polished surface was etched, 20 crystal particles in an electron micrograph taken at a magnification of 30000 were arbitrarily selected, the maximum diameter of each crystal particle was determined by the intercept method, and the average value thereof was determined.

  Regarding the Ca concentration, an arbitrary place near the center was analyzed using a transmission electron microscope and EDS. At that time, dielectric particles having a high Ca concentration were used for those having a Ca concentration higher than 0.4 atomic% (rounded to the second decimal place). This analysis was performed on 100 to 150 main crystal particles.

  The composition of the dielectric layer is obtained by cutting a portion of the dielectric layer from the obtained multilayer ceramic capacitor, mixing the molten portion with boric acid and sodium carbonate and dissolving in hydrochloric acid, and containing 1000 ppm of each element. A solution obtained by diluting the standard solution was quantified by ICP emission spectroscopic analysis as a standard sample.

  As an evaluation of the grain boundary phase as a high-temperature load test, it was separately measured using an alternating current impedance method. As high temperature load conditions in this case, the temperature was 250 ° C., and the voltage applied to the external electrode of the multilayer ceramic capacitor was 2 V / μm. The measurement voltage was 0.1 V, the frequency was between 10 mHz and 10 kHz, the standing time was 1 hour, and the AC impedance before and after the treatment was evaluated for 30 samples.

As a comparative example, when only BT powder was used as the barium titanate-based powder, the above-mentioned BT and BCT powders were used as the barium titanate-based powder. A product to which only a product was added and a product to which only a second composite oxide having a melting point lower than 1000 ° C. was added were prepared by the production method in the same manner as described above and evaluated in the same manner. The results are shown in Tables 5 and 6.

  As is apparent from the results of Tables 5 and 6, 0.5 to 3 mole parts of the first composite oxide having a melting point of 1000 ° C. or higher and the second composite oxide having a melting point lower than 1000 ° C. were added in total. In the obtained sample of the present invention, the relative dielectric constant was 2120 or more, and the change rate of the Cole-Cole plot in the high temperature load life test was 1% / min or less. In the case where two types of Y and Tb were simultaneously added to the dielectric powder and BT crystal particles and BCT crystal particles coexisted as barium titanate crystal particles, the relative dielectric constant was 3780 or more. Further, among the barium titanate crystal particles, the average particle diameter D1 of the barium titanate crystal particles (BT crystal particles) having a Ca component concentration of 0.2 atomic% or less is set to 0.13 to 0.16 μm, and D2 / D1 Of sample Nos. In the range of 1.3 to 1.85. In 30, 31, 39 to 41, 46, 47 and 52, the relative dielectric constant is 4180 to 4800, and the temperature change rate of the capacitance at 85 ° C. is −7.81% to −9.82%, Good characteristics were obtained with a change rate of Cole-Cole plot at a high temperature load life of -0.6 to -1.

Here, as shown in Table 7 and Table 8, if the _high / C _ave of the BCT crystal particles after firing is in the range of 2.1 to 2.9, the other additives have the same composition, The change rate of the Cole-Cole plot in the high temperature load life test was as small as -0.6 to -0.8%.

  On the other hand, in the sample in which only one of the first composite oxide having a melting point of 1000 ° C. or higher or the second composite oxide having a melting point lower than 1000 ° C. is added, the relative dielectric constant is low or the high-temperature load life test The Cole-Cole plot change rate was larger than 1% / min.

It is a schematic sectional drawing which shows the multilayer ceramic capacitor of this invention. It is a schematic diagram which shows the evaluation method of the resistance of the grain boundary in the dielectric material layer using the alternating current impedance measurement concerning this invention. It is a typical example of the resistance evaluation result of the grain boundary in a dielectric material layer using the alternating current impedance measurement of this invention. It is process drawing which shows the manufacturing method of the multilayer ceramic capacitor of this invention.

Explanation of symbols

DESCRIPTION OF SYMBOLS 1 Capacitor body 3 External electrode 5 Dielectric layer 7 Internal electrode layer 9 Crystal particle 9a BCT crystal particle 9b BT crystal particle 21 Ceramic green sheet 23 Internal electrode pattern 25 Ceramic pattern 29 Laminate

Claims (9)

A laminate comprising a plurality of dielectric layers composed of barium titanate-based crystal particles, a plurality of internal electrode layers formed between the dielectric layers, and an external electrode electrically connected to the internal electrode layers In the ceramic capacitor, the dielectric layer contains 0.5 to 5 mol parts of silicon oxide in terms of SiO ₂ as a subcomponent with respect to 100 mol parts of barium titanate (BaTiO ₃ ). The grain boundary in the dielectric layer in the AC impedance measurement before and after being left in a high-temperature load state at a temperature higher than the Curie temperature indicated by the constituent barium titanate-based crystal particles and a voltage equal to or higher than 1/3 of the rated voltage. A monolithic ceramic capacitor having a resistance reduction rate of 1% / min or less. Barium titanate system in which the dielectric layer contains barium titanate crystal particles containing Ca at a ratio of 0.2 atomic% or less and barium calcium titanate crystal particles having a Ca component concentration of 0.4 atomic% or more. The crystal particle, at least one of scandium oxide and yttrium oxide, at least one selected from gadolinium oxide, terbium oxide, dysprosium oxide, holmium oxide, erbium oxide, ytterbium oxide, and manganese oxide. The multilayer ceramic capacitor described. Of the barium titanate-based crystal particles, the barium titanate crystal particles having an average particle diameter of D1 and a Ca component concentration of 0.4 atomic% or more are included. 3. The multilayer ceramic capacitor according to claim 1, wherein D1 is 0.13 to 0.15 μm and D2 / D1 is 1.3 to 1.92, where D2 is an average particle diameter of the multilayer ceramic capacitor. Among the barium titanate crystal grains, represent a Ca component concentration of 0.4 atomic% or more barium calcium titanate crystal grains by the chemical formula _{Ba 1-x Ca x TiO 3} (x = 0.01~0.2) The multilayer ceramic capacitor according to any one of claims 1 to 3, wherein a relationship of A / B ≧ 1.003 is satisfied when the total amount of Ba and Ca is A mol and Ti is B mol. In a method for producing a multilayer ceramic capacitor, in which a dielectric body composed mainly of BaTiO ₃ and green sheets containing organic resin and internal electrode patterns are alternately laminated, and a capacitor body molded body is fired, BaTiO ₃ having a melting point as an auxiliary component with respect to 100 molar parts was added 0.5 to 5 molar parts in total and a lower second composite oxide than 1000 ° C. is first mixed oxide and a melting point above 1000 ° C. A method for producing a multilayer ceramic capacitor, characterized by: As the dielectric powder mainly composed of BaTiO ₃ , the total amount of Ba and Ca in the barium calcium titanate (Ba _1-x Ca _x TiO ₃ : x = 0.01 to 0.2) powder is A mol, Ti is The method for producing a multilayer ceramic capacitor according to claim 5, wherein a material satisfying a relationship of A / B ≧ 1.003 when B mole is used. As the dielectric powder mainly composed of BaTiO ₃ , barium titanate (BaTiO ₃ ) powder and barium calcium titanate (Ba _1-x Ca _x TiO ₃ x = 0.01 to 0.2) powder containing a Ca component Barium titanate powder mixed with at least one first rare earth powder selected from scandium oxide and yttrium oxide, and gadolinium oxide, terbium oxide, dysprosium oxide, holmium oxide, erbium oxide, ytterbium oxide The method for producing a multilayer ceramic capacitor according to claim 5 or 6, wherein at least one kind of second rare earth powder selected from: As the first composite oxide, BaO 25 to 35 mol%, CaO 15 to 25 mol%, SiO ₂ has a composition of 45 to 55 mol%, and as the second composite oxide, SiO ₂ is preparation of multilayer ceramic capacitor according to any one of claims 5 to 7 using gel glass - 75-90 _mol%, B 2 _{O 3} sol having a composition of 10 to 25 mol%. As the first composite oxide, BaO 25 to 35 mol%, CaO 15 to 25 mol%, the SiO ₂ has a composition of 45 to 55 mol%, and the second composite oxide, the BaO 20 30 mol%, CaO is 10-15 mol%, SiO ₂ 30 to 50 mol% and Li ₂ O sol having a composition of 10 to 30 mol% - according to any one of claims 5 to 7 using gel glass Of multilayer ceramic capacitors.

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