Patent Grant
7629282
This application is based upon and claims the benefit of priority from a Japanese Patent Application No. TOKUGAN 2006-76680, filed on Mar. 20, 2006; the entire contents of which are incorporated herein by reference.
1. Field of the Invention
The present invention relates to an aluminum nitride sintered body suitable for use in a member for a semiconductor-manufacturing device such as a substrate material for an electrostatic chuck, and a method of manufacturing the same.
2. Description of the Related Art
Since aluminum nitride (AlN) exhibits high corrosion resistance to a halogen gas, it has been widely used as a material for a substrate of an electrostatic chuck. In the electrostatic chuck using a Johnson-Rahbek force, a material for the substrate desirably has a volume resistivity of about 108 to 1012 Ω·cm in order to attain a high adsorption force and a high responsiveness of the electrostatic chuck. However, in general, the volume resistivity of aluminum nitride decreases to 107 Ω·cm or less at high temperature of 300° C. or more. Therefore, aluminum nitride cannot be used as a material for the substrate of an electrostatic chuck at high temperatures. In view of these circumstances, as disclosed in Japanese Patent Application Laid-open Nos. H9-315867 and 2003-55052, attempts have been made to improve the volume resistivity of aluminum nitride at high temperatures.
However, because the volume resistivity of conventional aluminum nitride has a high dependency upon temperature, when the conventional aluminum nitride is used as a substrate material for an electrostatic chuck, the workable temperature range for the electrostatic chuck is limited.
The present invention has been achieved in order to solve the above problem, and an object of the invention is to provide an aluminum nitride sintered body that exhibits suitable volume resistivity when it is used in a substrate material for an electrostatic chuck at high temperatures, and low in temperature dependency of the volume resistivity, and a method of manufacturing the aluminum nitride sintered body.
A feature of the aluminum nitride sintered body according to the present invention resides in that a conductive channel made of (Sm, Ce)Al11O18 is interconnected in the grain boundaries of aluminum nitride particles; at the same time, an aluminum nitride particle forms a solid solution with at least one of C and Mg.
A feature of a method of manufacturing an aluminum nitride sintered body according to a first aspect of the present invention resides in that the method comprises a step of blending at least either one of a B4C powder and a MgO powder, (Sm, Ce)Al11O18 powder with an aluminum nitride powder to obtain a powder mixture and forming the powder mixture into a product; and a step of subjecting the formed product to hot press sintering in a nitrogen atmosphere of 1700° C. or more, thereby manufacturing the aluminum nitride sintered body.
A feature of a method of manufacturing an aluminum nitride sintered body according to a second aspect of the present invention resides in that the method comprises a step of raising the temperature of an aluminum nitride powder together with a metal oxide powder to a temperature of 2000° C. or more in a carbon-reducing atmosphere, thereby heat treating the aluminum nitride powder; a step of blending at least a (Sm, Ce)Al11O18 powder with the heat treated aluminum nitride powder to obtain a powder mixture and forming the powder mixture into a product; and a step of subjecting the formed product to hot press sintering in a nitrogen atmosphere of 1700° C. or more, thereby manufacturing the aluminum nitride sintered body.
A feature of a method of manufacturing an aluminum nitride sintered body according to a third aspect of the present invention resides in that the method comprises a step of raising the temperature of an aluminum nitride powder together with a metal oxide powder to a temperature of 2000° C. or more in a carbon-reducing atmosphere, thereby heat-treating the aluminum nitride powder; a step of blending at least a non-heat-treated aluminum nitride powder, a MgO powder and a (Sm, Ce)Al11O18 powder with the heat-treated aluminum nitride powder to obtain a powder mixture and forming the powder mixture into a product; and a step of subjecting the formed product to hot press sintering in a nitrogen atmosphere of 1700° C. or more, thereby manufacturing the aluminum nitride sintered body.
A feature of a method of manufacturing an aluminum nitride sintered body according to a fourth aspect of the present invention resides in that the method comprises a step of raising the temperature of an aluminum nitride powder together with a metal oxide powder to a temperature of 2000° C. or more in a carbon-reducing atmosphere, thereby heat-treating the aluminum nitride powder; a step of blending at least a non-heat-treated aluminum nitride powder, a MgO powder, a Sm2O3 powder, a CeO2 powder and an Al2O3 powder with the heat-treated aluminum nitride powder to obtain a powder mixture and forming the powder mixture into a product; and a step of subjecting the formed product to hot press sintering in a nitrogen atmosphere of 1700° C. or more, thereby manufacturing the aluminum nitride sintered body.
The molar ratio Sm/Ce (Sm content to Ce content) in the aluminum nitride sintered body desirably falls within the range of more than 0.05 to less than 0.3. The ratio of volume resistivity A at 100° C. to volume resistivity A′ at 300° C., that is, log (A/A′), in the aluminum nitride sintered body desirably falls within the range of more than 1.5 to less than 2.2. The volume resistivity of the aluminum nitride sintered body at 300° C. desirably falls within the range of more than 1×109 Ω·cm to less than 2×1012 Ω·cm. The volume resistivity of the aluminum nitride sintered body at 500° C. desirably falls within the range of 1×108 Ω·cm to 1×1011 Ω·cm.
The brightness of the aluminum nitride sintered body based on JIS Z8721 is desirably N4 or less. The aluminum nitride sintered body desirably contains at least one type of transition metal element selected from the group consisting of the IVA family, VA family, VIA family, VIIA family and VIIIA family of the periodical table within the range of more than 0.01 wt % to less than 1.0 wt %.
According to the aluminum nitride powder and the method of manufacturing the same, it is possible to provide an aluminum nitride sintered body that exhibits suitable volume resistivity when it is used in a substrate material for an electrostatic chuck in a high temperature atmosphere of 300° C. or more, and which has a volume resistivity with a low temperature dependency.
Exemplary embodiments of the invention will become more fully apparent from the following description and appended claims, taken in conjunction with the accompanying drawings. Understanding that these drawings depict only exemplary embodiments and are, therefore, not to be considered limiting of the invention's scope, the exemplary embodiments of the invention will be described with additional specificity and detail through use of the accompanying drawings in which:
As a result of intensive researches conducted by the present inventors, they have found that, as shown in
The present invention will be explained below based on Examples.
In Example 1, first, a commercially available AlN powder (oxygen content: 0.9 wt %, average particle diameter: about 1 μm) manufactured by a reductive nitriding process, a commercially available MgO powder (purity: 99% or more, average particle diameter: about 1 μm) and a (Sm, Ce)Al11O18 powder were weighed so as to satisfy a weight ratio of 34.1:1.7:64.2 (wt %) . After that, they were subjected to wet blending using an IPA (isopropyl alcohol) as a solvent, nylon balls and nylon pot for 4 hours.
The process for manufacturing the AlN powder is not limited to a reductive nitriding process, and a vapor phase synthetic method, a direct nitriding process and other processes can be employed. Furthermore, the (Sm, Ce)Al11O18 powder was prepared by: (1) blending Sm2O3, CeO2 and Al2O3 (each had a purity of 99% or more, an average particle diameter of about 1 μm) using an IPA as a solvent, nylon balls and nylon pot so as to satisfy a molar ratio of Sm:Ce:Al of 0.1:0.9:11; (2) drying the powder mixture and subjecting it to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm; (3) applying heat treatment to the disk-shaped product in a nitrogen atmosphere at 1600° C. for 12 hours; and (4) pulverizing the resultant sintered body by a ball mill using alumina balls, followed by a jet mill until particles having an average diameter of 1 μm or less were obtained.
The powder mixture was then dried at 110° C. and subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1800° C. to produce an aluminum nitride sintered body according to Example 1. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Example 2, an aluminum nitride sintered body according to Example 2 was produced by performing the same process as in Example 1, except that the AlN powder, the MgO powder and the (Sm, Ce)A11O18 powder were weighed so as to satisfy a weight ratio of 53.0:2.6:44.4 (wt %).
In Example 3, an aluminum nitride sintered body according to Example 3 was produced by performing the same process as in Example 2, except that the sintering temperature was set at 1700° C.
In Example 4, an aluminum nitride sintered body according to Example 4 was produced by performing the same process as in Example 1, except that the AlN powder, the MgO powder and the (Sm, Ce) Al11O18 powder were weighed so as to satisfy a weight ratio of 53.5:1.6:44.9 (wt %).
In Example 5, an aluminum nitride sintered body according to Example 5 was produced by performing the same process as in Example 1, except that the AlN powder, the MgO powder and the (Sm, Ce)Al11O18 powder were weighed so as to satisfy a weight ratio of 52.4:3.7:43.9 (wt %).
In Example 6, an aluminum nitride sintered body according to Example 6 was produced by performing the same process as in Example 2, except that the pressure of the nitrogen atmosphere was set at 0.9 MPa.
In Example 7, an aluminum nitride sintered body according to Example 7 was produced by first weighing an AlN powder, a commercially available B4C powder (purity: 98% or more, average particle diameter: about 1.5 μm) and a (Sm, Ce)Al11O18 powder so as to satisfy a weight ratio of 53.8:1.1:45.1 (wt %), and blending these powders using an IPA as a solvent, nylon balls and nylon pot for 4 hours, followed by performing the same process as in Example 1.
In Example 8, an aluminum nitride sintered body according to Example 8 was produced by performing the same process as in Example 1, except that the AlN powder, the MgO powder and the (Sm, Ce)Al11O18 powder were weighed so as to satisfy a weight ratio of 53.2:2.1:44.6 (wt %).
In Example 9, first, 80 g of an AlN powder and 4.0 g of an aluminum oxide powder (Al2O3) were placed in a graphite crucible 11 and a graphite crucible 12a, 12b (shown in
Next, the heat-treated AlN powder and a (Sm, Ce)Al11O18 powder were weighed so as to satisfy a weight ratio of 76.1:23.9 (wt %). They were then placed in a flask together with camphene and alumina balls and set in a water bath of 75° C. After the camphene was melted and the materials in the flask were formed into slurry, a propeller was rotated to stir the slurry. After the stirring, the water bath was replaced with a container containing iced water and the slurry was cooled with stirring in the same manner. When the camphene was solidified and the rotation of the propeller was decreased, the rotation thereof was stopped. The substance in the flask was transferred to a tray and allowed to be still for 2 days to sublime the camphene. Since blended powder and alumina balls were left in the tray, the powders and the balls were separated by a sieve. The powder mixture was then subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die or sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1900° C. to obtain an aluminum nitride sintered body according to Example 9. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Example 10, first, an AlN powder, a MgO powder, a heat-treated AlN powder and an (Sm, Ce)Al11O18 powder were weighed so as to satisfy a weight ratio of 14.2:0.7:73.1:11.9 (wt %). They were then blended in the same manner as in Example 9.
Next, the powder mixture was subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter of about φ 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1900° C. to obtain an aluminum nitride sintered body according to Example 10. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Example 11, an aluminum nitride sintered body according to Example 11 was produced by performing the same process as in Example 10, except that the AlN powder, the MgO powder, the heat-treated AlN powder and the (Sm, Ce) Al11O18 powder were weighed so as to satisfy a weight ratio of 8.6:0.4:83.7:7.2 (wt %).
In Example 12, first an AlN powder, a MgO powder, a heat-treated AlN powder, a (Sm, Ce)Al11O18 powder and a titanium nitride (TiN) powder were weighed so as to satisfy a weight ratio of 14.2:0.7:72.9:11.9:0.3 (wt %). These powders were then blended in the same manner as in Example 9.
Next, the powder mixture was subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter of about φ 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1875° C. to obtain an aluminum nitride sintered body according to Example 12. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Example 13, an aluminum nitride sintered body according to Example 13 was produced by performing the same process as in Example 12, except that the (Sm, Ce)Al11O18 powder was produced by blending Sm2O3, CeO2 and Al2O3 in a IPA as a solvent so as to satisfy a molar ratio of Sm:Ce:Al of 0.15:0.85:11.
In Example 14, first an AlN powder, a MgO powder, a heat-treated AlN powder, a (Sm, Ce)Al11O18 powder and a TiN powder were weighed so as to satisfy a weight ratio of 8.6:0.4:83.4:7.2:0.3 (wt %). These powders were then blended in the same manner as in Example 9.
Next, the powder mixture was subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1900° C. to obtain an aluminum nitride sintered body according to Example 14. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Example 15, an aluminum nitride sintered body according to Example 15 was produced by performing the same process as in Example 14, except that the (Sm, Ce)A11O18 powder was produced by blending Sm2O3, CeO2 and Al2O3 in a IPA as a solvent so as to satisfy a molar ratio of Sm:Ce:Al of 0.2:0.8:11.
In Example 16, an aluminum nitride sintered body according to Example 16 was produced by performing the same process as in Example 9, except that the (Sm, Ce)Al11O18 powder was produced by blending Sm2O3, CeO2 and Al2O3 in a IPA as a solvent so as to satisfy a molar ratio of Sm:Ce:Al of 0.15:0.85:11.
In Example 17, an aluminum nitride sintered body according to Example 17 was produced by performing the same process as in Example 9, except that the (Sm, Ce)Al11O8 powder was produced by blending Sm2O3, CeO2 and Al2O3 in a IPA as a solvent so as to satisfy a molar ratio of Sm:Ce:Al of 0.2:0.8:11.
In Example 18, an AlN powder treated with heat, Sm2O3, CeO2 and Al2O3 were weighed so as to satisfy a weight ratio of 76.1:0.6:5.1:18.3 (wt %). These powders were then blended in the same manner as in Example 9.
Next, the powder mixture was subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1900° C. to obtain an aluminum nitride sintered body according to Example 18. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Comparative Example 1, first, an AlN powder was subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Next, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1900° C. to obtain an aluminum nitride sintered body according to Comparative Example 1. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Comparative Example 2, first, an AlN powder and a MgO powder were weighed so as to satisfy a weight ratio of 99.0:1.0 (wt %). These powders were blended using an IPA as a solvent, nylon balls and nylon pot for 4 hours. Next, the powder mixture was dried at 110° C. and subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1900° C. to produce the aluminum nitride sintered body according to Comparative Example 2. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Comparative Example 3, first, an AlN powder and a B4C powder were weighed so as to satisfy a weight ratio of 96.7:3.3 (wt %). These powders were blended using an IPA as a solvent, nylon balls and nylon pot for 4 hours. Next, the powder mixture was dried at 110° C. and subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 2000° C. to produce the aluminum nitride sintered body according to Comparative Example 3. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Comparative Example 4, first, the AlN powder heat-treated in the same step as in Example 9 was subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. The disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 2000° C. to produce the aluminum nitride sintered body according to Comparative Example 4. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Comparative Example 5, first, an AlN powder, a Sm2O3 powder and a CeO2 powder were weighed so as to satisfy a weight ratio of 98.0:1.0:1.0 (wt %). These powders were then blended using an IPA as a solvent, nylon balls and nylon pot for 4 hours. Next, the powder mixture was dried at 110° C. and subjected to uniaxial pressing at a pressure of 200 kgf/cm2 to form a disk-shaped product having a diameter (φ) of about 50 mm and a thickness of about 20 mm. Finally, the disk-shaped product was housed in a graphite die for sintering and a sintering process was performed at a press pressure of 200 kgf/cm2 and a sintering temperature of 1800° C. to produce the aluminum nitride sintered body according to Comparative Example 5. The sintering process was carried out in a vacuum from room temperature to 1000° C., and in a nitrogen atmosphere of 0.15 MPa from 1000° C. to the sintering temperature.
In Comparative Example 6, an aluminum nitride sintered body according to Comparative Example 6 was produced by performing the same process as in Example 12, except that the sintering temperature was set at 1850° C.
In Comparative Example 7, an aluminum nitride sintered body according to Comparative Example 7 was produced by performing the same process as in Example 5, except that the AlN powder, the Sm2O3 powder and the CeO2 powder were weighed so as to satisfy a weight ratio of 98.96:0.99:0.05 (wt %).
Aluminum nitride sintered bodies obtained by the processes in Examples and Comparative Examples above were evaluated, and the results are shown in Tables 1 and 2.
[Evaluation Method]
Aluminum nitride sintered bodies of Examples and Comparative Examples were individually measured for the content of a metal component (wt %), carbon amount (wt %), volume resistivity (Ω·cm) at 100, 300 and 500° C., variation of volume resistivity along with temperature increase from 100° C. to 300° C., thermal conductivity (W/mK) and an Sm/Ce molar ratio. In addition, the presence or absence of an (Sm, Ce)Al11O18 phase in aluminum nitride sintered bodies of Examples and Comparative Examples was checked. Each value was determined according to the following methods.
(1) The Content of Metal Component
The content of a metal component was quantified by an ICP emission spectrometric analysis.
(2) Carbon Amount
Carbon amount was quantified by high-frequency heating infrared absorption method.
(3) Volume Resistivity
Volume resistivity was measured according to JIS C2141 in a vacuum at 100, 300 and 500° C. To explain more specifically, test pieces of φ 50 mm×1 mm were prepared. A main electrode having a diameter of 20 mm, a guard electrode having an inner diameter of 30 mm and an outer diameter of 40 mm, and an applying electrode having a diameter of 45 mm each were formed of silver. A voltage of 500 V/mm was applied. One minute after applying the voltage, a current was measured to calculate the volume resistivity.
(4) Variation of Volume Resistivity
Variation of volume resistivity was calculated by substituting a value of volume resistivity A at 100° C. and a value of volume resistivity A′ at 300° C. into the formula of: Log (volume resistivity A at 100° C./Volume resistivity A′ at 300° C.).
(5) Thermal Conductivity
Thermal conductivity was measured by a laser flash method.
(6) Sm/Ce Ratio
Sm/Ce ratio was calculated by substituting an Sm content (wt %) and a Ce content (wt %) into the formula of: Log (Sm content (wt %)/150.36/Ce content (wt %)/140.12).
(7) Presence or Absence of (Sm, Ce)Al11O18 Phase
The presence or absence of a (Sm, Ce)Al11O18phase was determined based on whether an (Sm, Ce)Al11O18 phase was detected by a rotating-anode-type X-ray diffractometer (RINT by Rigaku Corporation). Note that there was no JCPDS card of (Sm, Ce)Al11O18. Instead, the peak of a CeAl11O18 was checked to confirm the presence or absence of an (Sm, Ce)Al11O18 phase. The measurement was performed in the conditions of X-ray source: CuKα beam, 50 kV, 300 mA, and a monochro-angle 2θ: 10 to 70°.
[Evaluation]
Aluminum nitride sintered bodies of Examples 1 to 18 and Comparative Examples 1 to 7 were compared with respect to volume resistivity values at 300° C. and 500° C. As shown in Tables 1 and 2 and
The aluminum nitride sintered bodies of Examples 1 to 18 and Comparative Examples 1 to 7 were then evaluated with respect to difference in composition. As a result, it was found that no (Sm, Ce)Al11O18 phase was present in the aluminum nitride Sintered bodies of Comparative Examples 1 to 4. Even in the cases where a (Sm, Ce)Al11O18 phase was present as was in the cases of Comparative Examples 5 to 7, it was found, in Comparative Example 6, that the (Sm, Ce)Al11O18 phase (white region shown in
In contrast, it was found that an (Sm, Ce)Al11O18 phase was present in the aluminum nitride sintered bodies of Examples 1 to 18 and interconnected as was shown in the SEM photograph of
From the above results, it was apparent that a conductive channel formed of an (Sm, Ce)Al11O18phase was interconnected in the grain boundaries of aluminum nitride particles and aluminum nitride particles form with at least one of C and Mg. Based on these facts, it was found that an aluminum nitride sintered body that exhibits suitable volume resistivity for use in a substrate material for an electrostatic chuck at a high temperature, and which has a volume resistivity with a low temperature dependency, can be provided.
With respect to the above findings, the present inventors think that an (Sm, Ce)Al11O18 phase forms a conductive channel in the grain boundaries of aluminum nitride particles and contributes to reducing temperature dependency of the volume resistivity of an aluminum nitride sintered body. Furthermore, the inventors think that the solid solution of an aluminum nitride particle with at least one of C and Mg maintains the volume resistivity of the aluminum nitride particle at a high value even at a high temperature, and thereby contributes to preventing the conductive channel from moving into the aluminum nitride particle.
The volume resistivity of an (Sm, Ce)Al11O18 phase changes depending upon the molar ratio of Sm/Ce (Sm content/Ce content), as shown in
As is apparent from Table 1, it was found that the aluminum nitride sintered bodies of Examples 1 to 18 has a common feature that log (A/A′), which was a ratio of volume resistivity A at 100° C. to that at 300° C., falls within the range of more than 1.5 to less than 2.2. The volume resistivity at 300° C. was found to fall within the range of more than 1×109 Ω·cm to less than 2×1012 Ω·cm. The volume resistivity at 500° C. was found to fall within the range of more than 1×108 Ω·cm to less than 1×1011 Ω·cm.
Although not shown in Table 1, it was found that the aluminum nitride sintered bodies of Examples 12 to 15 exhibit brightness values (according to JIS Z8721) of N4 or less. In the aluminum nitride sintered bodies of Examples 12 to 15, Ti was contained as a transition metal element. However, the transition metal element of the present invention is not limited to Ti. Any transition metal element can be used as long as it is at least one type of transition metal element selected from the group consisting of the IVA family, VA family, VIA family, VIIA family and VIIIA family of the periodical table. Furthermore, it was found that the content of the transition metal element desirably falls within the range of more than 0.01 wt % to less than 1.0 wt %.
The higher the thermal conductivity of an aluminum nitride sintered body, the more desirable. More specifically, the thermal conductivity thereof is preferably 30 W/mk or more and further preferably 50 W/mk or more. In the aluminum nitride sintered bodies of Examples, as the amount of (Sm, Ce)Al11O18 powder decreases, the thermal conductivity increases. As shown in Table 1, the aluminum nitride sintered bodies of Examples 2 to 7 exhibited higher thermal conductivity values than that of Example 1.
In the aluminum nitride sintered bodies of Examples 9 to 18, the particle diameter of an aluminum nitride powder was set at larger than that of an (Sm, Ce)Al11O18 powder in order to interconnect an (Sm, Ce)Al11O18 phase after sintering even if the amount of (Sm, Ce)Al11O18 powder was low. More specifically, the particle diameter of an aluminum nitride powder was set at 10 to 20 μm, although that of an (Sm, Ce)Al11O18 powder was 1 μm or less. This aluminum nitride powder was heat-treated. More specifically, a solid solution with C was formed, and the particle diameter was increased during the heat treatment at the same time.
The present invention is not limited to the description and the drawings which constitute a part of the disclosure of the present invention according to the embodiment. Specifically, it may be added that, needless to say, other embodiments, examples, operational technologies and the like, which are made by those skilled in the art based on the embodiment, are all included in the scope of the present invention.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2006-076680 | Mar 2006 | JP | national |
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|---|---|---|---|
| 6001760 | Katsuda et al. | Dec 1999 | A |
| 6607836 | Katsuda et al. | Aug 2003 | B2 |
| 6919287 | Teratani et al. | Jul 2005 | B2 |
| 7122490 | Kobayashi et al. | Oct 2006 | B2 |
| 7148166 | Teratani et al. | Dec 2006 | B2 |
| Number | Date | Country |
|---|---|---|
| 09-315867 | Dec 1997 | JP |
| 2003-055052 | Feb 2003 | JP |
| Number | Date | Country | |
|---|---|---|---|
| 20070215840 A1 | Sep 2007 | US |
