TECHNICAL FIELD

The present invention relates to a sintered oxide compact that include a perovskite phase, and to a circuit board using the same.

BACKGROUND ART

Many ceramic products are configured from a ceramic portion, which is a functional and structural member, and an electrode portion made of metal. Examples of combinations of such ceramic products and electrode portions include stacked ceramic capacitors (Ni, Pd, Pt electrodes), LTCC components (Ag, Cu, Agâ€”Pd electrodes), piezo actuators (Pd electrode), semiconductor packages (W electrode), and spark plugs (Ir, Pt electrodes).

However, firing of Ni, Cu, and W with the ceramic portion requires atmosphere control, which makes it difficult to obtain the intended performance of the ceramic portion. Another problem is the high manufacturing cost. On the other hand, since the melting point of Ag is low (962Â° C.), the type of applicable ceramics becomes limited, and further, the low-temperature firing may impair the ceramic properties. Further, noble metal materials such as Pd, Ir, and Pt are expensive, and thus, are not easily applicable to electrodes that require large areas.

Meanwhile, as an example of an oxide for use in ceramic portions, there is known a lanthanum cobalt oxide having a negative resistance temperature property which shows high resistance values at an ordinary temperature and in which the resistance value decreases with increasing temperatures (Patent Literatures 1 and 2). Further, the electrically conductive oxide of the Patent Literature 2 has a high resistance value near room temperature, and moreover, has a B-value with a small gradient near room temperature, and has the B-value with a large gradient at high temperatures.

CITATION LISTPatent Literature

Patent Literature 1: JP-B2-3286906

Patent Literature 2: JP-A-2002-87882

SUMMARY OF INVENTIONTechnical Problem

Meanwhile, since the above-described various problems occur when forming the electrode portion of ceramic products by metal, the present inventors thought of using oxides (ceramics) for the electrode portion. However, it has been difficult to replace metals with oxides because conventional oxides have lower electric conductivity and larger B-values (temperature coefficients) than metals. Here, although ruthenium oxides (e.g., RuO₂, and SrRuO₃) are known to have high electric conductivity, there is a problem that Ru is expensive.

Accordingly, an object of the present invention to provide a sintered oxide compact that has high electric conductivity and a small B-value (temperature coefficient) and is suitable for use as an electrically conductive material, and a circuit board that uses the sintered oxide compact.

Solution to Problem

In order to solve the above-described problem, a sintered oxide compact of the present invention is characterized in that:

the sintered oxide compact is represented by a composition formula: REaCobNicOx (where RE represents a rare earth element, a+b+c=1, and 1.3â‰¦xâ‰¦1.7);

the sintered oxide compact comprises a perovskite phase with a perovskite-type oxide crystal structure; and

the a, b, and c satisfy the following relationships:

0.459â‰¦aâ‰¦0.535,

0.200â‰¦bâ‰¦0.475, and

0.025â‰¦câ‰¦0.300.

With such a sintered oxide compact, the electric conductivity and the B-value (temperature coefficient of electric conductivity) can be controlled by varying the proportions of the trivalent Co and the bivalent Ni. Further, the electric conductivity can be controlled to be high and the B-value (temperature coefficient) can be controlled to be low by setting a, b, and c in the above-described ranges. With the above-described composition formula, an electric conductivity of the sintered oxide compact at 25Â° C. becomes 3.0 S/cm or more as measured by using a DC four-terminal method, and a B-value (temperature coefficient of electric conductivity) at 25Â° C. to 870Â° C. becomes 2500 K or less, whereby the sintered oxide compact can have properties suitable as an electrically conductive material. Further, by setting a, b, and c in the above-described ranges, the coefficient of thermal expansion under varying temperatures of from room temperature to 1000Â° C. can be reduced to 2.0Ã—10^âˆ’5K^âˆ’1or less, and there is an advantage that the coefficient of thermal expansion of the sintered oxide compact can easily be matched to that of the material of a base or a substrate, when forming the sintered oxide compact as an electrically conductive material on the base or the substrate. Further, it is possible to obtain a sintered oxide compact which is suitable for use in high-temperature environment.

It is preferable that the RE is La.

With this configuration, it is possible to obtain a sintered oxide compact having effectively high electric conductivity and a small B-value.

It is preferable that the a, b, and c satisfy the following relationships:

0.474â‰¦aâ‰¦0.524,

0.200â‰¦bâ‰¦0.475, and

0.025â‰¦câ‰¦0.300.

With this configuration, it is possible to obtain a sintered oxide compact having a denser structure.

It is preferable that the RE is La, and the b and c satisfy the following relationships:

0.200â‰¦bâ‰¦0.375, and

0.125â‰¦câ‰¦0.300.

According to such a sintered oxide compact, the electric conductivity at 25Â° C. becomes 250 S/cm or higher and the B-value becomes 600 K or less, that is, the electric conductivity becomes even higher and the B-value becomes even smaller. Further, in such a sintered oxide compact, the coefficient of thermal expansion can be made even smaller to 1.6Ã—10^âˆ’5K^âˆ’1or less.

It is preferable that the sintered oxide compact further comprises RE₄CO₃O₁₀or RE₄Ni₃O₁₀in addition to the perovskite phase.

According to such a sintered oxide compact, the electric conductivity at 25Â° C. becomes 250 S/cm or higher and the B-value becomes 600 K or less, that is, the electric conductivity becomes even higher and the B-value becomes even smaller.

It is preferable that the sintered oxide compact further contains substantially no alkali earth metal element. By containing substantially no alkali earth metal element, the weight of the sintered oxide compact itself does not easily change, that is, oxygen absorption and release do not occur easily, even when the sintered oxide compact is placed in a high-temperature environment (for example, 500Â° C. or higher), and changes in electric conductivity and B-value do not easily occur. Accordingly, it is possible to obtain a sintered oxide compact which is suitable for being used as an electrically conductive material in a high-temperature environment.

A circuit board of the present invention is a circuit board in which the sintered oxide compact is formed as an electrically conductive layer on a surface of a ceramic substrate. In this way, it possible to provide a circuit board that has an electrically conductive layer of a desirable electric conductivity formed on a ceramic substrate surface, without using a noble metal material.

Advantageous Effects of Invention

According to the invention, a sintered oxide compact that has high electric conductivity and a small B-value (temperature coefficient) and is suitable for use as an electrically conductive material (electric conductor), and a circuit board that uses the sintered oxide compact can be provided.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a diagram showing a relationship between electric conductivity and temperature for each Examples and Comparative Example 1.

FIG. 2 is a diagram showing an XRD chart of Example 7.

FIG. 3 is a diagram showing the XRD chart of Comparative Example 1.

FIG. 4 is a diagram showing the XRD chart of Comparative Example 4.

DESCRIPTION OF EMBODIMENTS

Embodiments of the present invention will be described hereinafter.

A sintered oxide compact according to an embodiment of the present invention is represented by the composition formula: REaCobNicOx (where RE represents a rare earth element, a+b+c=1, and 1.3â‰¦xâ‰¦1.7), and includes a perovskite phase with a perovskite-type oxide crystal structure, where a, b, and c satisfy the following relationships 0.459â‰¦aâ‰¦0.535, 0.200â‰¦bâ‰¦0.475, and 0.025â‰¦câ‰¦0.300.

When a is less than 0.459 (that is, the proportion of RE is too small) or when a exceeds 0.535 (that is, the proportion of RE is too large), the sintered oxide compact has poor sinterability.

When c is less than 0.025 (that is, the proportion of Ni is too small), the electric conductivity at 25Â° C. becomes less than 3.0 S/cm, and the B-value exceeds 2500 K, making the sintered oxide compact unsuitable as an electrically conductive material. On the other hand, when c exceeds 0.300 (that is, the proportion of Ni is too large), the sintered oxide compact has poor sinterability.

When b is less than 0.200 (that is, the proportion of Co is too small) or when b exceeds 0.475 (that is, the proportion of Co is too large), the proportions of the other elements fall outside of the above-described ranges, and the sintered oxide compact is not suitable as an electrically conductive material or has poor sinterability.

It should be noted here that x is theoretically 1.5 when the sintered oxide compact according to the embodiment of the present invention is solely of a perovskite phase. Notwithstanding above, the range 1.3â‰¦xâ‰¦1.7 is specified because the oxygen may deviate from the stoichiometric composition.

It is only necessary that the RE (rare earth element) is at least one selected from Group III elements of the periodic table. Preferably, it is suitable to use at least one selected from La, Pr, Ce, and Gd so as to control the electric conductivity and the B-value. Particularly, La is preferred for its ability to control the electric conductivity to be effectively high and control the B-value to be small.

In the sintered oxide compact according to the embodiment of the present invention, it is only necessary that the sintered oxide compact includes the perovskite phase, and the content of the perovskite phase in the sintered oxide compact according to the embodiment of the present invention is not particularly limited. Here, the sintered oxide compact is regarded as including a perovskite phase when a peak of the ternary oxide in RE.MO₃(M is Co or Ni) is detected in a powder X-ray diffraction (XRD) measurement of the sintered oxide compact (see FIGS. 2 to 4). It is preferable that the sintered oxide compact includes the perovskite phase in 50 mass % or more.

Further, it is preferable for a, b, and c to satisfy the relationships 0.474â‰¦aâ‰¦0.524, 0.200â‰¦bâ‰¦0.475, and 0.025â‰¦câ‰¦0.300 because it makes the structure of the sintered oxide compact denser.

Particularly, it is preferable that La is used as the RE (rare earth element), and b and c satisfy the relationships 0.200â‰¦bâ‰¦0.375 and 0.125â‰¦câ‰¦0.300, because the electric conductivity at 25Â° C. becomes 250 S/cm or higher and the B-value becomes 600 K or less, that is, the electric conductivity becomes even higher and the B-value becomes even smaller. Further, the sintered oxide compact tends to contain RE₄Co₃O₁₀or RE₄Ni₃O₁₀in addition to the perovskite phase, when the molar ratios of b and c fall within the above-described ranges. Note that the sintered oxide compact is regarded as containing RE₄Co₃O₁₀or RE₄Ni₃O₁₀when peaks of RE₄Co₃O₁₀or RE₄Ni₃O₁₀are detected in a powder X-ray diffraction (XRD) measurement of the sintered oxide compact (see FIGS. 2 to 4).

It is preferable that the sintered oxide compact according to the embodiment of the present invention contains substantially no alkali earth metal element, though this does not exclude containing very small amounts of alkali earth metal elements to an extent that the electric conductivity is not adversely affected. The weight of the sintered oxide compact does not easily change, that is, oxygen absorption and release do not occur easily, even when the sintered oxide compact is exposed to temperatures ranging from room temperature to about 900Â° C. Accordingly, it is possible to obtain a sintered oxide compact which can be suitably used as an electrically conductive material in a high-temperature environment. It should be noted that, in the present invention, â€œcontaining substantially no alkali earth metal elementâ€ means that an alkali earth metal element is not detectable or identifiable by the X-ray fluorescence analysis (XRF).

The sintered oxide compact according to the embodiment of the present invention can be produced by firing a mixed slurry of a raw material powder and an organic binder or the like at, for example, 1250 to 1450Â° C. for 1 to 5 hours under the air atmosphere or the oxygen atmosphere. If the firing temperature is below 1250Â° C., it may not be possible to densify the material, and thus, it may not be possible to obtain the desired electric conductivity and B-value. If the firing temperature is above 1450Â° C., oversintering occurs and densification is deteriorated, and thus, it may not be possible to obtain the desired electric conductivity and B-value.

The sintered oxide compact according to the embodiment of the present invention may be used as substitutes for metal in, for example, various electrode materials, electric wire materials, thermoelectric materials, heater materials, and temperature detecting elements. The sintered oxide compact according to the embodiment of the present invention also may be used for, for example, resistor elements.

A circuit board according to an embodiment of the present invention includes the electrically conductive sintered oxide compact formed as an electrically conductive layer on a surface of a ceramic substrate. As the ceramic substrate, ceramic materials such as alumina, zirconia, and silicon nitride can be used.

It is to be understood that the present invention is not limited by the above-described embodiments, and the invention encompasses various modifications and equivalents within the spirit and scope of the present invention.

Examples

REOH₃or RE₂O₃, Co₃O₄and NiO (RE represents the rare earth elements shown in Table 1, and all of them are commercially available products with 99% or higher purity) were used as raw material powders. These raw material powders were weighed so as to become the compositions REaCobNicOx shown in Table 1, and wet mixed and dried to prepare raw material powder mixtures. No alkali earth metal element was added in the preparation of the raw material powder mixtures. The raw material powder mixtures were each fired at 1000 to 1200Â° C. for 1 to 5 hours to obtain a preform powder. Then, an appropriate amount of organic binder was added to the preform powder, the mixture was put into a resin pot together with ethanol serving as a dispersion medium, and was subjected to wet mixed grinding using zirconia balls to obtain a slurry. The slurry was dried at 80Â° C. for about 2 hours, and granulated through a 250 Î¼m-mesh sieve to obtain a granulated powder.

The granulated powder was molded into a prism-shaped molded article measuring 4.0 mmÃ—4.0 mmÃ—20 mm height by using a pressing machine (molding pressure: 98 MPa), and was fired under the air atmosphere at a temperature of 1250 to 1450Â° C. for 1 to 5 hours. The resulting sintered material was surface ground to obtain a sintered oxide compact measuring 3.0 mmÃ—3.0 mmÃ—15 mm height.

The electric conductivity of each sintered oxide compact was measured by using a DC four-terminal method. Pt was used for the measurement electrodes and electrode wires. A voltage-current generator (Monitor 6242; manufactured by ADC Corporation) was used for the electric conductivity measurement.

From the measured electric conductivity values at 25Â° C. and 870Â° C., the B-value (K) was calculated by using the following equation (1).

B-value=ln(Ï 1/Ï 2)/(1/T1âˆ’1/T2)

Ï 1=1/Ïƒ1

Ï 2=1/Ïƒ2â€ƒâ€ƒ(1)

Ï 1: resistivity (Î©cm) at absolute temperature T1 (K)

Ï 2: resistivity (Î©cm) at absolute temperature T2 (K)

Ïƒ1: electric conductivity (S/cm) at absolute temperature T1 (K)

Ïƒ2: electric conductivity (S/cm) at absolute temperature T2 (K)

T1=298.15 (K)

T2=1143.15 (K)

Further, each of the obtained sintered oxide compact was pulverized into a powder, and subjected to powder X-ray diffraction (XRD) measurement to identify the crystal phase. The measurement conditions are as follows.

Measurement device: RINT-TTR-3 (goniometer radius 285 mm), manufactured by Rigaku

Optical system: Bragg-Brentano focused optical system

X-ray output: 50 kV-300 mA

Other Conditions:

Divergence SLIT: 1/3Â°

Vertical divergence limit SLIT: 10 mm

Scattering SLIT: 1/3Â°

Receiving SLIT: 0.3 mm

Scan mode: FT

Count time: 2.0 sec

Step width: 0.0200Â°

Scan axis: 2Î¸/Î¸

Scan range: 20.00Â° to 120.00Â°

Rotation: Present

Further, the sinterability of each sintered oxide compact was evaluated according to JIS-R-1634. Specifically, the dry weight W1 and the saturation weight W3 of the sample were first measured, and water absorption was calculated by using these values and the following equation (2).

Water absorption(%)=(W3âˆ’W1)/W1Ã—100â€ƒâ€ƒ(2)

Evaluation was made according to the following criteria.

x: water absorption is higher than 0.10 wt %

Î”: water absorption is 0.05 wt % to 0.10 wt %

âˆ˜: water absorption is lower than 0.05 wt %

When the water absorption evaluation result is Î” or âˆ˜, the structure of the sintered oxide compact is dense and the sinterability is good, and such sintered materials do not pose a problem when used as an electric conductor in actual applications.

The coefficient of thermal expansion of each sintered oxide compact was measured under varying temperatures of from room temperature to 1000Â° C. The measurement conditions are as follows.

Measurement device: TMA8310, manufactured by Rigaku

Standard sample: SiO₂,

Measurement atmosphere: air atmosphere

Rate of temperature increase: 10.0Â° C./min

The obtained results are shown in Table 1 and FIGS. 1 to 4. Here, although not shown in Table 1, as a result of the X-ray fluorescence diffraction (XRF) measurement, which was separately electric conducted for each obtained sintered oxide compact, no alkali earth metal element was detected for all of them.

TABLE 1EvaluationComposition: RE_aCo_bNi_cO_xElectricCoefficientConstituting elementsconductivity ÏƒB_25-870of thermal(molar ratio)(S/cm)constantexpansionREabcCrystal phase25Â° C.870Â° C.(K)Sinterability(K^âˆ’1)Example 1La0.5000.4750.025REMO₃178811589âˆ˜2.1 Ã— 10^âˆ’5Example 2La0.5000.4500.050REMO₃458811201âˆ˜2.0 Ã— 10^âˆ’5Example 3La0.5000.4000.100REMO₃1481082802âˆ˜1.9 Ã— 10^âˆ’5Example 4La0.5000.3750.125REMO₃, RE₄M₃O₁₀2911030510âˆ˜1.8 Ã— 10^âˆ’5Example 5La0.5000.3500.150REMO₃, RE₄M₃O₁₀4611193383âˆ˜1.8 Ã— 10^âˆ’5Example 6La0.5000.3000.200REMO₃, RE₄M₃O₁₀1037121062âˆ˜1.6 Ã— 10^âˆ’5Example 7La0.5000.2500.250REMO₃, RE₄M₃O₁₀19031465âˆ’106âˆ˜1.4 Ã— 10^âˆ’5Example 8La0.5000.2000.300REMO₃, RE₄M₃O₁₀2751051540âˆ˜1.3 Ã— 10^âˆ’5Example 9La0.4740.2630.263REMO₃, RE₄M₃O₁₀16811389âˆ’77âˆ˜1.6 Ã— 10^âˆ’5Example 10La0.4870.2560.256REMO₃, RE₄M₃O₁₀18081317âˆ’128âˆ˜1.6 Ã— 10^âˆ’5Example 11La0.5120.2440.244REMO₃, RE₄M₃O₁₀5051236361âˆ˜1.6 Ã— 10^âˆ’5Example 12La0.5240.2380.238REMO₃, RE₄M₃O₁₀373943374âˆ˜1.5 Ã— 10^âˆ’5Example 13La0.4590.2700.270REMO₃, RE₄M₃O₁₀5341074282Î”1.6 Ã— 10^âˆ’5Example 14La0.5350.2330.233REMO₃, RE₄M₃O₁₀, NiO256702407Î”1.6 Ã— 10^âˆ’5Example 15Pr0.5000.2500.250REMO₃, RE₄M₃O₁₀1478141619âˆ˜1.4 Ã— 10^âˆ’5Example 16Nd0.5000.2500.250REMO₃, RE₄M₃O₁₀, NiO3.27982226âˆ˜1.5 Ã— 10^âˆ’5Comparative Example 1La0.5000.5000.000REMO₃0.3310313245Î”2.2 Ã— 10^âˆ’5Comparative Example 2La0.5000.1500.350REMO₃, RE₄M₃O₁₀, NiO83809919x1.7 Ã— 10^âˆ’5Comparative Example 3La0.5000.1000.400RE₄M₃O₁₀, NiO75757934x1.8 Ã— 10^âˆ’5Comparative Example 4La0.5000.0000.500RE₂MO₄, NiO415311032x1.9 Ã— 10^âˆ’5Comparative Example 5La0.4440.2780.278REMO₃, RE₄M₃O₁₀, NiO127901790x1.6 Ã— 10^âˆ’5Comparative Example 6La0.5450.2270.227REMO₃, RE₄M₃O₁₀, NiO, Co₃O₄101326473x1.7 Ã— 10^âˆ’5Comparative Example 7La0.5000.4950.005REMO₃2110912522Î”2.1 Ã— 10^âˆ’5*RE = rare earth metal, M = Co or Ni

As clearly shown in Table 1 and FIG. 1, in the Examples which were represented by the composition formula: REaCobNicOx and in which a, b, and c satisfied the relationships 0.459â‰¦aâ‰¦0.535, 0.200â‰¦bâ‰¦0.475, and 0.025â‰¦câ‰¦0.300, the perovskite phase was included, the electric conductivity at 25Â° C. was 3.0 S/cm or more, and the B-value (temperature coefficient of electric conductivity) at 25Â° C. to 870Â° C. was 2500 K or less, thereby having properties suitable as an electrically conductive material.

Referring to the Examples 1 to 14 that used the same RE (La), in the Examples 4 to 14 in which b and c satisfied the relationships 0.200â‰¦bâ‰¦0.375 and 0.125â‰¦câ‰¦0.300, the electric conductivity at 25Â° C. was 250 S/cm or more and the B-value was 600 K or less, which were higher than the electric conductivities and the B-values of Examples 1 to 3 that did not satisfy these relationships. It was also found that, in the Examples 4 to 16 in which the molar ratios of b and c fell within the above-described ranges, the sintered oxide compact contained RE₄Co₃O₁₀or RE₄Ni₃O₁₀in addition to the perovskite phase.

In the Examples 7, 15, and 16 that had the same molar ratio of the constituting elements (the ratio of a, b, and c) but used different types of RE, the electric conductivity was the highest and the B-value was the smallest in the Example 7 in which RE was La. The result suggests that La is preferable as RE.

Meanwhile, in the Comparative Examples 1 and 7 in which c was less than 0.025 (that is, the proportion of Ni is too small), the electric conductivity at 25Â° C. was less than 3.0 S/cm, and the B-value exceeded 2500 K, showing that these sintered oxide compacts were not easily usable as the electrically conductive material. Note that the Comparative Example 7 is the reproduction of the composition of Patent Literature 2.

In the Comparative Examples 2 to 4 in which c was larger than 0.300 (that is, the proportion of Ni is too large), the water absorption by the sintered oxide compacts was relatively large, and the sinterability was poor.

Relatively large water absorption, and poor sinterability were also observed in the Comparative Example 5 in which a was less than 0.459 (that is, the proportion of RE is too small), and in the Comparative Example 6 in which a was larger than 0.535 (that is, the proportion of RE is too large).

FIG. 1 shows the relationship between the electric conductivity and the temperature for the Examples 1 to 3, Examples 5 to 7, and Comparative Example 1. As clearly shown in FIG. 1, the Examples 1 to 7 had higher electric conductivities than the Comparative Example 1 even at low temperatures, and the temperature-dependent electric conductivity change (B-value) was smaller. The Examples 5 to 7, in which b and c satisfied the relationships 0.200â‰¦bâ‰¦0.375 and 0.125â‰¦câ‰¦0.300, had even higher electric conductivity than the Examples 1 to 3 even at low temperatures, and even smaller B-values.

Further, FIGS. 2 to 4 show the XRD charts of the Example 7, Comparative Example 1, and Comparative Example 4, respectively. It can be seen that a peak of the ternary oxide of RE.MO₃(M is Co or Ni) is detected in the Example 7 and the Comparative Example 1 (FIGS. 2 and 3), and that these sintered oxide compacts include the perovskite phase. On the other hand, the peak of the ternary oxide of RE.MO₃was not detected in the Comparative Example 4 (FIG. 4). Further, in Example 7, a peak attributed to RE(La)₄Co₃O₁₀was also observed in addition to the peak of the ternary oxide of RE.MO₃.