Patent Application
20070211409
1. Field of the Invention
This invention relates to a ceramic powder to be used for forming dielectric ceramic layers in a multilayer ceramic electronic component resulting from alternately stacking dielectric ceramic layers and internal electrode layers, and particularly relates to a ceramic powder useful for enhancing the withstanding voltage property of the multilayer ceramic electronic component. This invention further relates to a dielectric paste using the ceramic powder, a multilayer ceramic electronic component, and a method for the production thereof.
2. Description of the Prior Art
The multilayer ceramic capacitor that is one of multilayer ceramic electronic components possesses a structure resulting from alternately stacking dielectric ceramic layers and internal electrode layers till a plurality of pairs and has been extensively used as an electronic part having a small size, a large capacity, and high reliability. Not infrequently, a great number of multilayer ceramic capacitors are used in one electronic device.
In recent years, electronic devices have been undergoing reduction in size and addition to performance. This trend has been urging the multilayer ceramic capacitor with increasingly more severity to acquire reduction in size, addition to capacity, decrease in price, enhancement of reliability, and the like. For the purpose of enabling the multilayer ceramic capacitor to secure reduction in size and addition to capacity in response to the harsh demand, the dielectric ceramic layers have reached the point where they are required to decrease the layer thickness and increase the number of component layers. The increase in size and the addition to capacity mentioned above are rendered feasible by thinning the dielectric ceramic layers forming the multilayer ceramic capacitor and increasing the number of layers for lamination.
Incidentally, when the thinning of the dielectric ceramic layers and the adding to the number of component layers for lamination mentioned above are taken into account, the formation of the internal electrode layers with an internal electrode-oriented electroconductive paste having such a noble metal as Pd as a main ingredient is disadvantageous from the viewpoint of production cost, for example. When the internal electrode layers are formed of an internal electrode-oriented electroconductive paste having as a main ingredient thereof such a noble metal as Pd, the cost for forming the electrodes is inevitably increased markedly in consequence of the addition to the number of component layers for lamination. In the circumstance, an internal electrode-oriented electroconductive paste that has as a main ingredient thereof such a base metal as Ni has been developed. The multilayer ceramic capacitor that has the internal electrode layers thereof formed of this paste has been befitting practical use.
When the internal electrode layers are formed of the aforementioned internal electrode-oriented electroconductive paste having as a main ingredient thereof such a base metal as Ni, however, the decrease in thickness of the dielectric ceramic layers to below 10 μm or the increase in the number of component layers to above 100 possibly entails such problems as inducing separation (delamination) or inflicting a crack and consequently degrading the yield of production owing to the shrinkage or expansion of internal electrode layers and the difference in shrinkage behavior of dielectric ceramic layers.
For the purpose of ensuring solution of these problems, the suppression of the shrinkage of Ni powder during the course of firing or the enhancement of the strength of a dielectric material fated to form the dielectric ceramic layers is effective. Thus, the practice of adding a ceramic oxide or an organic metal compound as a common material to the internal electrode-oriented electroconductive paste to be used for forming the internal electrode layers, varying the composition of the ceramic used for forming the dielectric ceramic layers, or varying the conditions of firing or the conditions of the treatment of reoxidization has been prevailing (refer to JP-A 2004-221268).
JP-A 2004-221268 discloses a method for producing a multilayer ceramic electronic component such that the difference between the temperature at which the rate of change of shrinkage during the firing of external ceramic layers is maximized and the temperature at which the rate of change of shrinkage during the firing performed in the state having completed formation of the internal electrodes of ceramic layers of the internal electrode-stacking part is maximized may become not more than 60° C. It also discloses the fact that, as compared with the ratio, A/B, of the mol concentration A of the A site ions and the mol concentration B of the B site ions of the ceramics forming the ceramic layers of the internal electrode-stacking part, the mol ratio A/B in the external ceramic layers is made to become small.
The trend of the multilayer ceramic electronic components toward decreasing size and increasing capacity has been rendering increasingly difficult the solution of the problems solely by the aforementioned conventional technique. Specifically, when the decrease in size and the increase in capacity of the multilayer ceramic electronic components further advance, the ratio of the Ni part (internal electrode layers) to the whole device increases, the aforementioned problem of delamination and cracking appears more conspicuously, the ratio of occurrence of cracks increases in spite of the countermeasure mentioned above, and the yield of production is degraded possibly to the extent of posing problems. These disadvantages further constitute a cause as for inducing inferior insulation, lowering withstanding voltage, and degrading the reliability of a multilayer ceramic component.
This invention has been proposed in view of the true state of related art mentioned above and is aimed at providing a ceramic powder and a dielectric paste that, even when the decrease in thickness of the dielectric ceramic layers forming a multilayer ceramic electronic component and the increase in number of the component layers are further advanced, enable suppressing inferior insulation and enhancing withstanding voltage, and as well suppressing the occurrence of cracks (structural defect) and enhancing the yield of production. This invention, in consequence of the provision of the ceramic powder and the dielectric paste mentioned above, is also aimed at realizing a multilayer ceramic electronic component excelling in insulating property and durability during the exposure to a high-temperature load and exhibiting high reliability and is further aimed at providing a method for the production thereof.
The present inventors have carried out many studies over a long time with a view to accomplishing the object mentioned above. To be specific, they have performed a further detailed analysis on the ceramic powder for use in the dielectric ceramic layers of the multilayer ceramic electronic component. As a result, they have eventually acquired a knowledge that the ceramic powder possessing a perovskite-type crystal structure contains a tetragonal phase and a cubic phase and the optimization of the ratio (weight ratio) of the tetragonal phase and the cubic phase is effective for the purpose of suppressing the occurrence of delamination and cracking and enhancing the insulating property and the withstanding voltage in the multilayer ceramic electronic component.
This invention has been accomplished based on this knowledge. That is, the ceramic powder of this invention is a ceramic powder that is intended to form dielectric ceramic layers in a multilayer ceramic electronic component resulting from alternately stacking the dielectric ceramic layers and internal electrode layers and is characterized by possessing a perovskite-type crystal structure and satisfying an expression X<3, wherein X denotes the weight ratio Wt/Wc of the tetragonal phase content Wt and the cubic phase content Wc.
The dielectric paste of this invention is a dielectric paste that is intended to form dielectric ceramic layers in a multilayer ceramic electronic component resulting from alternately stacking the dielectric ceramic layers and internal electrode layers and is characterized by containing the aforementioned ceramic powder as a ceramic powder. The multilayer ceramic electronic component of this invention is a multilayer ceramic electronic component that is obtained by alternately stacking dielectric ceramic layers and internal electrode layers and is characterized by the fact that the dielectric ceramic layers resulting from forming dielectric green sheets with the dielectric paste and firing these sheets. The method for producing the multilayer ceramic electronic component of this invention, in the process of obtaining the multilayer ceramic electronic component by alternately stacking dielectric green sheets and electrode precursory layers respectively with a dielectric paste and an electroconductive paste and subsequently firing the resultant multilayer body, is characterized by using the dielectric paste mentioned above.
The ceramic powder for use in a dielectric ceramic layer has been heretofore analyzed by X-ray diffraction, for example, and based on the results of the analysis the ceramic powder about to be used has been tried to optimize. In the case of barium titanate possessing a perovskite-type crystal structure, for example, though the X-ray chart is varied in consequence of the variation of the specific surface area, the idea of comprehending this variation of the X-ray diffraction chart as a variation of the lattice constant of a tetragonal phase and setting a range for the variation accordingly may be cited. The conventional method as mentioned above, however, has not always brought a satisfactory effect.
The present inventors, therefore, inferred that the variation of the X-ray diffraction chart mentioned above was caused by the mixed phase consisting of a tetragonal phase and a cubic phase. When they subjected the X-ray diffraction chart to polyphasic analysis (such as the biphasic analysis presuming the two phases, ie a tetragonal phase and a cubic phase) by the Rietveld Method, the results concurred satisfactorily with the inference and endorsed the correctness of the inference. When the analysis was further advanced, it was found that the ratio of the tetragonal phase and the cubic phase was varied as by the conditions of production of barium titanate and this variation affected characteristic properties. Specifically, when the ceramic powder possessing the perovskite-type crystal structure satisfies the expression X<3, wherein X denotes the weight ratio Wt/Wc of the tetragonal phase content Wt and the cubic phase content Wc, it is rendered possible to suppress the occurrence of cracking and delamination, decrease inferior insulation, and heighten withstanding voltage.
This invention, as the index of the selection of raw material (ceramic powder), adopts the weight ratio Wt/Wc (=X) of the tetragonal phase content Wt and the cubic phase content Wc. By using the ceramic powder that is selected based on this index, it is rendered possible to suppress inferior insulation and enhance withstanding voltage even when the dielectric ceramic layers forming the multilayer ceramic electronic component are required to incur decrease in thickness and increase in the number of layers in consequence of a reduction in size or a large addition to capacity, for example. It is further made possible to suppress the occurrence of cracking and delamination and enhance the yield of the production of a multilayer ceramic electronic component.
Now, the ceramic powder and the dielectric paste that make use of this invention and further the multilayer ceramic electronic component (specifically a multilayer ceramic capacitor herein) and the method for production thereof will be described in detail below.
First, to explain the multilayer ceramic capacitor that uses the ceramic powder of this invention, the main body of device is configured in a multilayer ceramic capacitor 1 by alternately stacking a plurality of pairs of dielectric ceramic layers and internal electrode layers as illustrated in
Though the shape of the main body does not need to be particularly restricted, it is generally in the shape of a rectangular body. The size of the main body does not need to be particularly restricted but may be properly set to suit the purpose of use. For example, it may approximately measure 0.6 mm to 5.6 mm (preferably 0.6 mm to 3.2 mm) in length×0.3 mm to 5.0 mm (preferably 0.3 mm to 1.6 mm) in width×0.1 mm to 1.9 mm (preferably 0.3 mm to 1.9 mm (preferably 0.3 mm to 1 6 mm) in thickness.
The dielectric ceramic layers 2 mentioned above are made of a dielectric ceramic composition and formed by sintering the powder of the dielectric ceramic composition (ceramic powder). This invention contemplates causing the dielectric ceramic composition to contain as a main ingredient a dielectric oxide possessing a perovskite-type crystal structure represented by the constitutional formula, ABO3 (wherein A site is formed of at least one element selected from the group consisting of Sr, Ca, and Ba and B site is formed of at least one element selected from the group consisting of Ti and Zr). Here, the amount of oxygen (O) may deviate to a certain extent from the stoichiometric composition of the aforementioned constitutional formula. Of all the dielectric oxides answering the constitutional formula, barium titanate that is obtained by forming the A site mainly of Ba and the B site mainly of Ti proves to be favorable. More favorably, the dielectric oxide is barium titanate represented by the constitutional formula, BamTiO2+m (wherein 0.995≦m≦1.010 and 0.995≦Ba/Ti≦1.010 are satisfied).
Besides the main ingredient, the dielectric ceramic composition may contain various kind of accessory ingredient. As the accessory ingredient, at least one oxide selected from the group consisting of oxides of Sr, Zr, Y, Gd, Tb, Dy, V, Mo, Zn, Cd, Ti, Sn, W, Ba, Ca, Mn, Mg, Cr, Si, and P may be cited. The addition of such an accessory ingredient results in enabling the sintering to proceed at a low temperature without degrading the dielectric property of the main ingredient. It also results in suppressing the inferior reliability taking place when the dielectric ceramic layers 2 are given a decreased thickness and as well allowing addition to the service life.
The conditions of the dielectric ceramic layers 2 such as the number of layers and the thickness of each layer may be properly decided to suit the purpose of use. The thickness of the dielectric ceramic layers 2 is about 1 μm to 50 μm and preferably not more than 5 μm. From the viewpoint of enabling the multilayer ceramic capacitor to acquire a decreased size and an increased capacity, the dielectric ceramic layers 2 prefer to have a thickness of not more than 3 μm and the dielectric ceramic layers 2 prefer to be stacked up to a total of not less than 150 layers.
Though the electroconductive material to be contained in the internal electrode layers 3 is not particularly restricted, such a base metal as, for example, Ni, Cu, Ni alloy, or Cu alloy may be used. The thickness of the internal electrode layers 3 may be properly decided to suit the purpose of use. It is, for example, about 0.5 μm to 5 μm and preferably not more than 1.5 μm.
Though the electroconductive material contained in the external electrodes 4 and 5 is not particularly restricted, generally Cu, Cu alloy, Ni, Ni alloy, Ag, or Ag—Pd alloy are used. Cu, Cu alloy, Ni, and Ni alloy prove to be advantageous because they are inexpensive materials. While the thickness of the external electrodes 4, 5 may be properly decided to suit the purpose of use, it is about 10 μm to 50 μm, for example.
In the multilayer ceramic capacitor 1 possessing the structure mentioned above, the dielectric ceramic composition (body material) that is used for the dielectric ceramic layers 2 exerts a great influence on the characteristic properties. This invention realizes enhancement of the dielectric property by rendering appropriate the ceramic powder destined to serve as the body material. Specifically, this invention subjects a ceramic powder possessing a perovskite-type crystal structure to powder X-ray diffraction analysis, performs polyphasic analysis by the Rietveld method on the results of the powder X-ray diffraction analysis, and selects a ceramic powder that satisfies the expression X<3, wherein X denotes the weight ratio Wt/Wc of the tetragonal phase content Wt and the cubic phase content Wc.
Now, the polyphasic analysis by the Rietveld method mentioned above will be described below. In the powder X-ray diffraction analysis, for example, the lattice constant can be derived from the peak position, the crystal structure parameters (polarization coordinates, population, atomic displacement parameter, etc.) from the area (integrated intensity) of the diffraction profile, the lattice strain and the crystallite size from the broadening of profile, and the mass fractions of the component phases of a mixture. In the powder neutron diffraction analysis, the magnetic moments of various magnetic atomic sites can be derived further from the integrated intensity.
The Rietveld method mentioned above is a general-purpose technique for powder diffraction data analysis that can be simultaneously determining fundamentally important physical quantities in solid-state physics, chemistry, and materials chemistry and serves as a tool for comprehending physical phenomena and chemical properties manifested by polycrystalline materials from the structural aspect. The important object of the Rietveld Method is to refine crystal structure parameters included in crystal structure factors Fk and serves the purpose of directly précising the structural parameters and the lattice constants with respect to the whole of powder X-ray-diffraction patterns and powder neutron diffraction patterns. That is, this method implements the fitting of a diffraction pattern computed based on an approximate structure model in order that the computed diffraction pattern may agree as closely with the actually measured pattern as possible. As the salient advantages of the Rietveld method, the ability to determine not only the crystal structure parameters but also the lattice constant with high accuracy and precision and also the ability to determine the lattice strain, the crystallite size, and the contents of components in a mixture may be cited in respect of the fact the method admits all the analysis patterns as the objects of fitting and pays due respect to the presence of K α2 reflection in the case of the X-ray characteristic.
In the ceramic powder possessing a Perovskite-type crystal structure such as barium titanate, the presence of a tetragonal phase and a cubic phase has been known. The X-ray diffraction pattern of this ceramic powder is varied in concert with variation of the mean particle diameter (specific area) thereof.
Heretofore, it has been proposed to grasp a variation of the X-ray diffraction chart as a variation of the lattice constant and use it as an index of the ceramic powder to be used. It is proposed that when a=b is presumed in the lattice constants a, b, and c in the tetragonal phase as shown in
The rule set forth above takes the dielectric property into account but makes no great difference from defining the mean particle diameter or the specific surface area of the ceramic powder to be used. It pays no consideration whatever as to the improvement of the withstanding voltage property. The present inventors, therefore, have tried a detailed analysis of the X-ray diffraction chart. Specifically, the present inventors, by assuming that the state varying from
The results of the biphasic analysis mentioned above suggest firstly that the analysis excelling in precision has been implemented accurately. This fact may be safely regarded as endorsing the correctness of the aforementioned assumption (purporting the mixed phase between the tetragonal phase and the cubic phase) and has led the inventors to the comprehension that the ceramic powder having a relatively small mean particle diameter (a large specific surface area) is the mixed phase of a tetragonal phase and a cubic phase. To date, the barium titanate powder has never been recognized as the mixed phase of a tetragonal phase and a cubic phase.
Secondly, it has been ascertained that, when the ceramic powder is used as the body material for the dielectric ceramic layers 2 of the multilayer ceramic capacitor 2, the ratio of the tetragonal phase and the cubic phase exerts an influence on the characteristic properties and, particularly when importance is attached to the insulating property and the withstanding voltage property, satisfaction of the expression X<3, wherein X denotes the weight ratio Wt/Wc of the tetragonal phase content Wt and the cubic phase content Wc, is advantageous. By satisfying this expression X<3, it is rendered possible to suppress inferior insulation and enhance withstanding voltage even when the dielectric ceramic layers 2 forming the multilayer ceramic capacitor 1 are given a reduced thickness or the number of component layers is increased. It is also made possible to suppress the occurrence of cracking and delamination.
The weight ratio X mentioned above varies with the conditions for the production of the ceramic powder, for example. The X-ray diffraction chart, notwithstanding an unchanged appearance, possibly produces a value different from the weight ratio X mentioned above when it is actually subjected to polyphasic analysis by the Rietveld method mentioned above. Since this difference defies comprehension by the conventional X-ray diffraction analysis, it becomes necessary to find the value by the polyphasic analysis according to the Rietveld method mentioned above and select what satisfies the aforementioned condition.
As regards the aforementioned weight ratio Wt/Wc (=X) of the tetragonal phase content Wt and the cubic phase content Wc, the expression X<3 constitutes the basis for the selection of the ceramic powder possessing the perovskite-type crystal structure as already pointed out. In this case, the fact that the ceramic powder is the mixed phase between a tetragonal phase and a cubic phase serves as a prerequisite and the ceramic powder consisting solely of a cubic phase (the value of X is zero) is not included. The value of the X mentioned above has its own limit in spite of all efforts to contrive the condition of production, for example. The value of this X, therefore, prefers to be 2 at the least (namely X≧2).
This invention aims to maintain high withstanding voltage property while thinning the dielectric ceramic layers 2 and, therefore, prefers to give the component dielectric ceramic layers 2 a thickness of not more than 3 μm as described above. Abreast with the thickness, the specific surface area SSA of the ceramic powder to be used prefers to exceed 4 m2/g (mean particle diameter not more than 0.25 μm) and more favorable fall in the range of 4 m2/g to 10 m2/g. When the specific surface area SSA is 10 m2/g, the mean particle diameter is approximately 0.1 μm.
By using for the multilayer ceramic capacitor 1 the raw material (ceramic powder) selected by the method of selection of raw material based on the polyphasic analysis in accordance with the Rietveld method, it is rendered possible to realize further reduction in size and further addition to capacity of the multilayer ceramic capacitor 1. Thus, the multilayer ceramic capacitor contemplated by this invention is most suitable for uses involving high withstanding voltage. Now, therefore, the method for producing the multilayer ceramic capacitor using the aforementioned ceramic powder will be explained below.
To produce the multilayer ceramic capacitor possessing the aforementioned configuration, dielectric green sheets destined to form dielectric ceramic layers 2, electrode precursory layers destined to form internal electrode layers 3 subsequent to firing, and external cladding green sheets destined to form external cladding dielectric layers 6 are prepared and they are stacked to complete a multilayer body.
The dielectric green sheets can be obtained by preparing a dielectric paste containing a ceramic powder, applying this dielectric paste to carrier sheets as base materials by the doctor blade method, and drying the resultant coated carrier sheets. The dielectric paste is prepared by kneading the ceramic powder destined to serve as a body material and an organic vehicle or a water-based vehicle. For the preparation of the dielectric paste, the ceramic powder selected by the method of selection of raw material based on the polyphasic analysis in accordance with the Rietveld method is used. Then, the mean particle diameter and the specific surface area thereof are selected in conformity with the thickness of the dielectric ceramic layers 2 within the range mentioned above.
Incidentally, the expression “the organic vehicle” that is used for the preparation of the dielectric paste mentioned above” refers to what results from dissolving a binder in an organic solvent. The binder to be used for the organic vehicle is not particularly restricted but may be properly selected from among various ordinary binders such as ethyl cellulose and polyvinyl butyral. The organic solvent to be used for the organic vehicle also is not particularly restricted but may be properly selected from among various organic solvents such as terpineol, diethylene glycol monobutyl ether, acetone, and toluene. The term “water-based vehicle” refers to what results from dissolving a water-soluble binder or dispersant in water. The water-soluble binder is not particularly restricted. The use of polyvinyl alcohol, cellulose, water-soluble acrylic resin, or the like suffices.
Then, the electrode precursory layer is formed by having the prescribed region of the dielectric green sheet mentioned above printed with an electroconductive paste containing an electroconductive material. The electroconductive paste is prepared by causing the electroconductive material and a common material (ceramic powder) to be kneaded with the organic vehicle.
After the multilayer body is formed, the sinter (main body of device) is obtained by performing a treatment for the removal of binder, a firing work, and a heat treatment adapted to re-oxidize the dielectric ceramic layers 2 and the external cladding dielectric layers 6. The treatment for the removal of binder, the firing work, and the heat treatment for the sake of re-oxidization may be performed continuously or independently.
The treatment for the removal of binder may be performed under ordinary conditions. When such a base metal as Ni or Ni alloy is used in the electroconductive material for the internal electrode layers 3, however, this treatment prefers to be carried out under the following conditions. The rate of temperature increase is in the range of 5 to 300° C./hour, particularly 10 to 50° C./hour, the standing temperature is in the range of 200 to 400° C., particularly 250 to 340° C., the standing time is in the range of 0.5 to 20 hours, particularly 1 to 10 hours, and the atmosphere is a humidified mixed gas of N2 and H2.
As the firing conditions, the rate of temperature increase is in the range of 50 to 500° C./hour, particularly 200 to 300° C./hour, the standing temperature is in the range of 1100 to 1300° C., particularly 1150 to 1250° C., the standing time is in the range of 0.5 to 8 hours, particularly 1 to 3 hours, and the atmosphere is preferably a humidified mixed gas of N2 and H2.
During the firing, the oxygen partial pressure in the atmosphere prefers to be not more than 10−2 Pa. If the oxygen partial pressure exceeds the upper limit mentioned above, the excess will possibly result in oxidizing the internal electrode layers 3. If the oxygen partial pressure is unduly low, the shortage will tend to induce abnormal sintering of the electrode material and inflict a break on the internal electrode layers 3. The oxygen partial pressure of the firing atmosphere, therefore, prefers to be in the range of 10−2 Pa to 10−8 Pa.
The heat treatment after the firing is carried out with the holding temperature or the highest temperature set generally at not less than 1000° C. and preferably in the range of 1000° C. to 1100° C. If the holding temperature or the highest temperature mentioned above falls short of 1000° C., the shortage will possibly result in oxidizing the electroconductive material (Ni) in the internal electrode layers 3 and exerting an adverse effect on the capacity and the service life of the multilayer ceramic capacitor.
The atmosphere for the heat treatment mentioned above is given a higher oxygen partial pressure than that of the firing, preferably in the range of 10−3 Pa to 1 Pa and more preferably in the range of 10−2 Pa to 1 Pa. If the oxygen partial pressure of the atmosphere for the heat treatment falls short of the range, the shortage will render the re-oxidation of the dielectric layers difficult. Conversely, if it exceeds the range, the excess will possibly result in re-oxidizing the internal electrode layers 3. As the conditions of the heat treatment, the holding time is in the range of 0 to 6 hours, particularly 2 to 5 hours, the rate of temperature decrease is in the range of 50 to 500° C./hour, particularly 100 to 300° C./hour, and the atmosphere is humidified N2 gas, for example.
Finally, the multilayer ceramic capacitor 1 illustrated in
Now, a working example embodying this invention will be explained below based on the results of an experiment.
XRD (Powder X-Ray Diffraction) Measurement
The powder X-ray diffraction (XRD) measurement was performed by the use of a powder X-ray diffraction device (made by Rigaku K.K. and sold under the product name of Rint2000), and measurement range of 2θ is from 10 to 130°. As a result, XRD profile data for the Rietveld analysis was obtained. In this measurement, the electrical current and the electrical voltage were so set that the step width would reach 0.01° and the largest peak count about 10000 counts.
Rietveld Analysis
The XRD profile data consequently obtained was analyzed by the use of the software, RIETAN-2000 (Rev. 2. 4. 1) (for Windows), intended for Rietveld analysis. For the determination of the mass fractions of the component phases, the Microabsorption with due correction was adopted.
Study on Reliability of Polyphasic Analysis by Rietveld Method
Analysis of a barium titanate powder possessing a perovskite-type crystal structure (specific surface area SSA 6.16 m2/g and mean particle diameter 0.16 μm determined by a scanning electron microscope) was tried by the Rietveld method. The Rietveld analysis was executed in three modes, ie the monophasic analysis of a tetragonal phase (tetragonal crystal), the monophasic analysis of a cubic phase (cubic crystal), and the biphasic analysis of the tetragonal phase (tetragonal crystal)+the cubic phase (cubic crystal). The reliability factors in these analyses are shown in Table 1.
[Table 1]
Of the indexes for evaluating the condition of progress of the Rietveld analysis and the degree of agreement between the actual intensity and the calculated intensity, the most important R factor is Rwp. Since Rwp is prone to the influences of diffraction intensity and background intensity, however, the index S value (=Rwp/Re) destined to compare Re equaling the smallest statistically expected Rwp with Rwp serves as a substantial yardstick for indicating good fitness of analysis. S=1 signifies perfection of precision. So long as S is smaller than 1.3, the results of analysis may well be regarded as satisfactory. A review of Table 1 from this point of view reveals that the s value resulting from the biphasic analysis of the tetragonal phase and the cubic phase is not more than 1.3, namely a smaller s value than is the s value obtained by the monophasic analysis. This fact indicates properness of conclusion that the analyzed ceramic powder consists of the two, one tetragonal and one cubic, phases.
Study Regarding the Weight Ratio Wt/Wc (=X) of Tetragonal Phase Content Wt and Cubic Phase Content Wc in Ceramic Powder
Multilayer ceramic capacitors were manufactured by following the method of production described above while using varying kinds of ceramic powders (barium titanate powders) (Examples 1 to 3 and Comparative Examples 1). The multilayer ceramic capacitors so manufactured had a size of 1.0 mm×0.5 mm×0.5 mm, the number of stacked dielectric ceramic layers was 160, the thickness of each of the component dielectric ceramic layers was 1.6 μm, and the thickness of each of the internal electrodes was 1.0 μm. The specific surface area SSA of the ceramic powder used, the content Wt of the tetragonal phase, the content Wc of the cubic phase, the weight ratio Wt/Wc thereof, the particle diameter of the sinter, the dispersion a of particle diameter, the IR fraction defective of the manufactured multilayer ceramic capacitors, the withstanding voltage, and the number of occurrences of structural defects are shown in Table 2.
[Table 2]
It is clear from Table 2 that in the ceramic powder to be used, the increase of the IR fraction defective and the withstanding voltage are realized by satisfying the weight ratio Wt/Wc (=X)<3 of the tetragonal phase and the cubic phase. There is remarkably little number that occurred of a structure defect
Study Regarding Specific Surface Area of Ceramic Powder
Ceramic powders differing in specific surface area SSA were compared with respect to their characteristic properties exhibited when the weight ratio Wt/Wc of the tetragonal phase and the cubic phase was not less than 3 and the weight ratio Wt/Wc is less than 3. The results are shown in Table 3.
[Table 3]
It is clear from Table 3 that whenever the specific surface area SSA of the ceramic powder is in the range of 4 m2/g to 10 m2/g, the IR fraction defective can be suppressed, the withstanding voltage can be enhanced, and the structural defect can be suppressed so long as the weight ratio, Wt/Wc, of the tetragonal phase and the cubic phase satisfies the expression Wt/Wc<3. When the ceramic powder to be used has a specific surface area SSA in the range of 4 m2/g to 10 m2/g and a weight ratio of the tetragonal phase and the cubic phase, Wt/Wc, of not less than 3, therefore, it is rendered possible to manufacture a multilayer ceramic capacitor that excels in terms of relative permittivity and dielectric loss.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2006-065947 | Mar 2006 | JP | national |
