Ceramic sintered bodies and a method of producing the same

BACKGROUND OF THE INVENTION

[0001] 1. Title of the Invention

[0002] The invention relates to ceramic bodies and a method for producing the same.

[0003] 2. Related Art Statement

[0004] An integrated body of porous ceramics and dense ceramics may be produced by various methods, including brazing, adhesion with an inorganic adhesive and co-sintering (“Metal Handbook” Sixth revision, Pages 1036 to 1037; MARUZEN CO., LTD.).

SUMMARY OF THE INVENTION

[0005] The present inventors has tried to join a dense sintered body and a porous sintered body both made of, for example, silicon carbide. Although a porous ceramic body and a dense ceramic body might be joined with each other by brazing, few brazing materials may provide an adequate strength to the surface of each ceramic body. When the porous ceramic body has a high porosity and relatively large open pores, a brazing material may flow into the open pores to react with the ceramics and denature it. Such brazing material in the pores tends to further reduce the adhesive strength of the brazing material to the surface of the porous ceramics. Further, it is necessary to heat the brazing material to a temperature high enough for melting the material for bonding the porous and dense ceramic bodies. The subsequent cooling step of the molten brazing material may induce a residual stress so that the bonding strength is reduced or fluctuated. These problems may be also induced when bonding porous ceramic and dense ceramic bodies with a glass adhesive.

[0006] It is an object of the invention to integrate porous ceramics and dense ceramics with an adequately high bonding strength.

[0007] The invention provides a ceramic sintered body comprising a dense portion and a porous portion. The dense portion is formed with sintered ceramic fine particles and the porous portion is formed with sintered ceramic coarse particles. The fine particles and coarse particles are subjected simultaneously to pressure sintering to form the dense portion and porous portion.

[0008] The invention also provides a method of producing a ceramic sintered body having a dense portion and a porous portion by subjecting ceramic fine particles and ceramic coarse particles simultaneously to pressure sintering.

[0009] The inventors have modified a so called pressure sintering process and successfully sintered ceramic fine particles and ceramic coarse particles simultaneously to obtain an integrated sintered body with dense and porous portions. Such pressure sintering process was performed under temperature and pressure conditions adapted for producing a highly sintered dense body of the fine particles and for simultaneously producing a porous body of the coarse particles.

[0010] Ceramic particles may be sintered by pressure sintering processes including hot pressing and hot isostatic press sintering. For example, various ceramic materials, such as silicon nitride, silicon carbide and aluminum nitride, have been manufactured by hot pressing.

[0011] According to the invention, ceramic fine particles are used which may provide a dense sintered body with a pressure sintering process. The fine particles are subjected to a pressure sintering process simultaneously with ceramic coarse particles. The coarse particles are selected so as to produce a porous body under temperature and pressure conditions sufficient for producing a dense body of the ceramic fine particles. Consequently, the invention provides an integrated sintered body having a dense portion made from the fine particles and a porous portion made from the coarse particles, by a pressure sintering process.

[0012] In such a sintered body, the dense and porous portions are bonded and integrated strongly along an interface extending continuously when observed microscopically. Since the ceramic fine and coarse particles are subjected to a sintering process simultaneously in the dense and porous portions, a residual stress along the interface of the dense and porous portions is relatively small. The bonding strength of the porous and dense portions is thus high or stabilized, causing very few bonding defects.

[0013] The invention may be generally applied to ceramics. Such ceramics includes an oxide ceramics, such as alumina, zirconia, titania, silica, magnesia, ferrite, cordierite, and the oxides of rare earth elements such as yttria; a complex oxide such as barium titanate, strontium titanate, lead titanate zirconate, manganites of rare earth elements and chromites of rare earth elements; nitride ceramics such as aluminum nitride, silicon nitride and sialon; and carbide ceramics such as silicon carbide, boron carbide and tungsten carbide.

[0014] The average particle diameter of ceramic fine particles is not particularly limited, as far as the fine particles may be sintered to produce a sintered body with a desired porosity under predetermined temperature and pressure conditions during a pressure sintering. The average diameter of the fine particles, however, may preferably be not larger than 5 μm and more preferably be not larger than 1 μm.

[0015] The average particle diameter of the ceramic coarse particles is not particularly limited, as far as the coarse particles may be sintered to produce a sintered body with a desired porosity under predetermined temperature and pressure conditions during the pressure sintering. Moreover, preferred average diameter of the ceramic coarse particles may be varied depending on a desired porosity. Generally the average diameter of the coarse particles may preferably be not smaller than 40 μm and more preferably be not smaller than 50 μm. The average diameter may preferably be not larger than 400 μm and more preferably be not larger than 100 μm, for preventing the reduction of strength of a porous portion. The ratio of the porosity of a dense portion divided by the porosity of a porous portion may preferably be not higher than 0.3 and more preferably be not higher than 0.01.

[0016] In a preferred embodiment, ceramic coarse particles are grindstones or abrasive grains used for grinding or polishing. It has not been known to subject these materials to pressure sintering simultaneously with fine particles. Alternatively, a ceramic sintered body may be coarsely ground to produce coarse particles, which are then passed through a mesh for regulating the particle size. The resultant coarse particles with the regulated particle size may preferably be used as the above ceramic coarse particles to be subjected to pressure sintering.

[0017] Ceramic fine particles and coarse particles may be granules containing a binder, or may be ceramic powder containing substantially no binder. It is possible to add a pore forming material to ceramic coarse particles. However, the pressure sintering is normally carried out under sealed or closed condition. It is therefore preferred to substantially avoid the addition of a pore forming material, which may adversely affect the sintering process under the sealed or closed condition. In the invention, the ceramic coarse particles with relatively large diameters are subjected to a high pressure under a high temperature to strongly bond the coarse particles with each other and leaving pores, to a some extent, between the coarse particles.

[0018] The porosity of the dense portion may preferably be not higher than 10 percent and more preferably be not higher than 5 percent, for improving the strength of the inventive sintered body. The lower limit of the porosity is not particularly limited and may be 0 percent.

[0019] The porosity of the porous portion may preferably be not lower than 10 percent, more preferably be not lower than 15 percent, and most preferably be not lower than 20 percent, to utilize the inventive sintered body for a wide variety of applications. The porous portion having a porosity of not lower than 15 percent is particularly preferable, because such portion tends to have open pores continuous with each other so as to form a gas passage.

[0020] The porosity of the porous portion may preferably be not higher than 40 percent and more preferably be not higher than 30 percent, for improving the strength of the porous portion.

[0021] A metal part or metal member may be embedded within the inventive sintered body. The shape or kind or function of such metal member is not particularly limited. The metal member may be, for example, a bulky and plate-shaped material made of a metal, or a metal film formed by printing. Such metal member may preferably be made of a metal having a high melting point and stable at a temperature for sintering the ceramics. The metal includes tantalum, tungsten, molybdenum, platinum, rhenium,, hafnium, and the alloys of these metals.

[0022] The bulky material made of a metal constituting the metal member includes, for example, the following materials.

[0023] (1) A plate-shaped bulky material made of a metal.

[0024] (2) A plate-shaped bulky material made of a metal: A number of small spaces are formed in the material.

[0025] The material (2) includes a plate-shaped bulky body having a number of small openings and a wire netting or gauze. The plate-shaped body having a number of small openings includes an etching metal and punching metal.

[0026] A hot pressing system of ceramics includes, basically, a mechanism for applying a pressure and a mechanism for heating. The pressure-applying mechanism ordinarily includes a die and a punch. The following two properties are needed for a material for the pressure-applying mechanism: (1) the material has a mechanical strength sufficiently high for enduring an applied predetermined pressure, and (2) the material does not chemically react with ceramic particles, at a temperature for heating ceramic particles or ceramic shaped body, for example at a temperature from 1000 to 2400° C. Such material includes, for example, graphite.

[0027] In a preferred embodiment, ceramic fine particles and ceramic coarse particles are made of the same kind of ceramic material. The invention may provide an integrated structure having a porous portion and a dense portion which are made of the same kind of ceramic material and bonded strongly with each other. “The same kind of ceramic material” means that the main component of one ceramic material constituting the dense portion is same as that of the other ceramic material constituting the porous portion. The component or components other than the main component, as well as trace components, may be different with each other. Inevitable impurities derived from raw materials may be also contained in each ceramic material. More preferably, not lower than 50 percent of ceramics constituting the porous portion and not lower than 50 percent of ceramics constituting the dense portion are of the same component. Most preferably, not lower than 80 percent of ceramics constituting the porous portion and not lower than 80 percent of ceramics constituting the dense portion are of the same component.

[0028] In a preferred embodiment, a porous portion and a dense portion are laminated in a direction of a pressure applied during pressure sintering. In this case, the interface between the porous portion and dense portion is formed in a direction crossing, or substantially perpendicular to, the direction of the applied pressure. It is thereby possible to improve the bonding strength of the porous and dense portions. The interface of the porous and dense portions may preferably be formed in a direction crossing the direction of the applied pressure at an angle of not lower than 45° and more preferably not lower than 60°. Most preferably, the interface is substantially perpendicular to the direction of the applied pressure.

[0029] At least a part of the interface of the porous and dense portions may preferably be substantially parallel with the direction of a pressure applied during pressure sintering. The porous and dense portions tend to shrink differently so as to induce irregularities in the interface between the porous and dense portions. Such irregularities in the interface may be somehow prevented or avoided in the interface substantially parallel with the direction of the applied pressure.

[0030] When hot isostatic pressing process is applied, however, pressure is applied on the ceramic shaped body in every direction surrounding the body. The above embodiment may therefore be applied to a process with a pressure substantially applied in a predetermined direction, such as hot pressing process.

BRIEF DESCRIPTION OF THE DRAWINGS

[0031]
FIG. 1(a) is a cross sectional view schematically showing a sintered body 1 according to the invention,

[0032]
FIG. 1(b) is a perspective view showing the bottom face 1b and side face of a sintered body 1,

[0033]
FIG. 2 is a cross sectional view schematically showing a primary shaped body 7, ceramic particles 8, and a system for shaping them by an uniaxial pressure shaping process,

[0034]
FIG. 3 is a cross sectional view schematically showing a secondary shaped body 10 set in a mold for hot pressing,

[0035]
FIG. 4(a) is a cross sectional view showing a sintered body 1A,

[0036]
FIG. 4(b) is a perspective view showing a sintered body 1A,

[0037]
FIG. 5(a) is a cross sectional view showing a sintered body 1B,

[0038]
FIG. 5(b) is a cross sectional view showing a sintered body 1C,

[0039]
FIG. 6(a) shows a test sample 15 cut from a sintered body 1 for measuring a four-points bending strength,

[0040]
FIG. 6(b) shows a plan view and side view of a sample cut from a sintered body 1 for measuring a surface resistance,

[0041]
FIG. 7 is a photograph showing the microstructure of bonding interface of a porous portion and dense portion according to an example 2, and

[0042]
FIG. 8 is a photograph showing the microstructure of bonding interface of a porous portion and dense portion in a sintered body according to an example 4.

PREFERRED EMBODIMENTS OF THE INVENTION

[0043]
FIG. 1(a) is a cross sectional view schematically showing a sintered body 1 according to one embodiment of the invention, and FIG. 1(b) is a perspective view showing the bottom face 1b and side face of the sintered body 1. 1a is a main face of the sintered body 1. The sintered body 1 is made of a porous portion 3 and a dense portion 2. The porous portion 3 has a shape of a disk. The dense portion 2 is composed of a disk-shaped portion 2a laminated on the porous portion and a ring-shaped portion 2b surrounding the porous portion 3 and laminated portion 2a. The laminated portion 2a and the ring-shaped side wall portion 2b are continuously formed. The interface 20 of the laminated portion 2a and porous portion 3 is substantially perpendicular to a direction “A” of an applied pressure. The interface 21 of the side face of the porous portion 3 and dense portion 2 is substantially parallel with the direction “A”.

[0044] The sintered body 1 may be produced according to a process explained referring to FIGS. 2 and 3. In a preferred embodiment, ceramic coarse particles are subjected to pressure shaping to obtain a primary shaped body 7. Although the shaped body 7 has a shape of a disk in this example, its shape is not particularly limited. The primary shaped body 7 is contained in a mold system for pressure shaping schematically shown in FIG. 2. This mold system has an upper punch 4, a lower punch 5, and a sleeve 9. In the example, the primary shaped body 7 is mounted on the main face 6b of a supporting body 6 to form a laminated body 21.

[0045] The main face 6a of the supporting body 6 is mounted on the shaping face 5A of the lower punch 5. The supporting body 6 has an outer diameter substantially fit with the inner diameter of the sleeve 9. The primary shaped body 7 has a diameter slightly smaller than the inner diameter of the sleeve 9 and the outer diameter of the shaping face 5A. Ceramic fine particles 8 are filled between the side face 7a of the primary shaped body 7 and the sleeve 9, and on the main face 7b of the primary shaped body 7. It is possible to mount a sheet, made of a material which is not reactive with the ceramic fine and coarse particles, on the upper supporting face 6b of the supporting body 6. The sheet is inserted between the supporting body 6 and the fine and coarse particles.

[0046] The upper punch 4 is then driven downwardly so as to apply a pressure on the body 7 and fine particles 8 in a direction “A” with the shaping face 4A of the upper punch 4 and shaping face 5A of the lower punch 5. A secondary shaped body 10, shown in FIG. 3, is thus obtained. The secondary shaped body 10 has a shaped body 7A made of the coarse particles and a shaped body 11 made of the fine particles. The shaped body 11 covers the main (upper) face and side face of the shaped body 7A.

[0047] In a preferred embodiment, as described above, ceramic coarse particles are shaped to obtain a primary shaped body, which is then subjected to pressure shaping with ceramic fine particles to obtain a secondary shaped body. The secondary shaped body is then subjected to pressure sintering. The above process is advantageous for preventing the irregularities of the interface between the coarse particles and fine particles in a shaped body before the pressure sintering. When the coarse and fine particles are subjected to pressure shaping without preliminary shaping the coarse particles, irregularities may be induced in the interface of the coarse and fine particles in a shaped body.

[0048] The resulting secondary shaped body 10 is then set within a space formed by, for example, a shaping face 13a of an upper punch 13, a shaping face 14a of a lower punch 14 and a sleeve 12 for hot pressing. In this stage, the supporting body 6 may be removed from the secondary shaped body. Alternatively, the secondary shaped body 10 laminated with the supporting body 6 may be subjected to hot pressing without removing the body 6. When hot pressing is performed, the interface 22 of the ceramic fine particles and coarse particles is substantially perpendicular to a direction of a pressure applied during the hot pressing and the interface 23 is substantially parallel with the direction of the applied pressure.

[0049]
FIG. 4(a) is a cross sectional view of a sintered body 1A according to another embodiment, and FIG. 4(b) is a perspective view of the sintered body 1A. The sintered body 1A has a porous portion 3A with a shaped of a disk and a ring-shaped dense portion 2A surrounding the porous portion 3A. In this example, main faces 3a and 3b of the disk-shaped porous portion 3A are exposed. In other words, the porous portion 3A is continuous from one main face la to the other main face 1b of the sintered body 1A. 21 is an interface of the porous portion 3A and dense portion 2A. The interface 2A is substantially parallel with the direction “A” of the applied pressure.

[0050] In the invention, a porous portion may be made from two or more kinds of coarse particles with the different average particle diameters. In this embodiment, the coarse particles constituting a region near the dense portion preferably has an average particle diameter smaller than that of the coarse particles constituting a region distant from the dense portion. The porosity of the region near the dense portion may thereby be reduced compared with that of the region distant from the dense portion.

[0051] For example, in a sintered body 1B shown in FIG. 5(a), its porous portion 3B has a disk-shaped region 26 and a ring-shaped region 25 surrounding the side of disk-shaped region 26. The ring-shaped region 25 is nearer to a dense portion 2A than the disk-shaped region 26. The average particle diameter of coarse particles constituting the ring-shaped region 25 may preferably be smaller than that of coarse particles constituting disk-shaped region 26. The porosity of the ring-shaped region 25 may thereby be made smaller than that of the disk-shaped region 26.

[0052] Further, as shown in a sintered body 1C shown in FIG. 5(b), its porous portion 3C may be divided into three or more regions, for example four regions 27, 28, 29 and 30. In a preferred embodiment, the average particle diameters of coarse particles constituting the regions are reduced in the descending order of the reference numerals 30, 29, 28 and 27. The porosities of the regions are thereby reduced in the descending order of the reference numerals 30, 29, 28 and 27. Further in another embodiment, the porosity of the porous portion may be sloped and continuously changed therein.

[0053] The maximum temperature during the pressure sintering process may be adjusted depending on an applied ceramics and a desired porosity. Generally, the pressure sintering is carried out at a temperature of 1000 to 2400° C. The pressure during the sintering may be variously adjusted, and generally 50 to 400 kg/cm2.

[0054] The material for a supporting body is not particularly limited. When the supporting body is used during a pressure sintering process, the material for the supporting body may preferably be of a melting point not lower than a desired sintering temperature and not reactive with ceramics. Such material may preferably be boron nitride, carbon or the like. Further, the material may preferably be a metal with a high temperature, which does not melt at a sintering temperature, such as molybdenum, tungsten, tantalum, niobium, hafnium or the like. The material may most preferably be carbon.

[0055] The surface of a sintered body according to the invention may be coated with another material, preferably a ceramic material. Particularly when a porous portion is made of grindstones or abrasive particles, the purity of the porous portion may be lower than that of a dense portion utilizing a powdery raw material for a fine ceramic application. In this embodiment, the surface region of the sintered body, or at least the surface region of the porous portion, may be coated with a ceramic film so as to improve the purity of the surface region. A high purity is required for at least the surface portion of the sintered body, for example, in an application of a system for manufacturing semiconductors. In such applications, it is particularly preferred to cover the surface region of the sintered body, or at least the surface region of the porous portion, may be covered with the above ceramic film with a high purity.

[0056] Although the material for the coated ceramic film is not particularly limited, such material may preferably be the same kind as the ceramic material constituting the sintered body. The coated film may be formed by processes, not particularly limited, including chemical vapor deposition, physical vapor deposition, sputtering or the like.

EXAMPLES

(Example “A”)

[0057] A sintered body shown in FIG. 1 was produced according to the process described above referring to FIGS. 2 and 3. Silicon carbide coarse particles (GC abrasive grains), with properties shown in table 1, were prepared.

1TABLE 1ExampleExampleExampleExampleExample12345Silicon carbideNG36NG60NG100NG220#240coarse particleMaximum particle850˜600425˜300212˜150106˜75123diameter (μm)Average particle4002501207557Diameter (μm)Minimum particle355180754540Diameter (μm)SiC (weight %)99.299.299.499.296.0Free carbon0.100.100.040.080.50(weight %)Total iron content0.070.060.050.080.30(weight %)ApplicationGrindGrindGrindGrindAbrasiveStonestonestonestonegrain

[0058] The GC abrasive grains were mixed with a solution containing 5 percent of polyvinyl alcohol to obtain paste, which was then filled into a mold (cercle), removed from the mold, and dried at 110° C. for two hours to obtain a primary shaped body 7. The primary shaped body 7 was set in a metal mold. Ceramic fine particles 8 of silicon carbide were mixed with B4C and carbon powder as sintering aids, and then filled in the metal mold to cover the side face and upper main face of the primary shaped body 7. The fine particles and primary shaped body were pressed at a compacting pressure of 200 kg/cm2 to obtain a secondary shaped body 10. The secondary shaped body 10 was subjected to hot press sintering with its maximum temperature during the sintering of 2200° C. and the holding time period at 2200° C. of 2 hours. The temperature rising rate and cooling rate were 100° C. per hour. The sintering was carried out in 100 percent argon.

[0059] The resulting sintered bodies 1 were cut to obtain rod-shaped samples 15 as shown in FIG. 6. 15a is its porous portion and 15b is its dense portion. The mechanical strength of each sample 15 was measured according to a four point bending method defined in “JIS R1601”. The results were shown in table 2. Moreover, the porosity of each of the porous and dense portions was measured by Archimedes method, and the results were shown in table 2. The microstructure of each interface between the dense and porous portions of each of sintered bodies according to the examples 2 and 4 was shown in FIGS. 2 and 4, respectively. The photographs were taken using a scanning electron microscope with a magnitude of 50.

2TABLE 2ExampleExampleExampleExampleExample12345Silicon carbideNG36NG60NG100NG220#240Coarse particleAverage particle400 μm250 μm120 μm75 μm57 μmdiameter of siliconcarbide coarse particleAverage particle 1.6 μm 1.6 μm 1.6 μm 1.6 μm 1.6 μm diameter of siliconcarbide fine particleMaximum22002200220022002200Temperature duringSintering (° C.)Pressure for200200200200200Sintering kg/cm2Atmosphere forArgonArgonArgonArgonArgonSinteringPorosity of porous2424262727Portion (%)Porosity of dense0.180.100.060.070.06Portion (%)Four point bending110130200240300Strength (MPa)

[0060] As can be seen from the results, the porous and dense portions were made of the same kind of material and had porosities considerably different from each other. The dense portion was substantially densified to a considerably small porosity of not higher than 0.2 percent. At the same time, the porous portion had a sufficiently high porosity of 20 to 30 percent. The bonding strength of the dense and porous portions was relatively large.

[0061] Each sample 16, with a shape and dimensions shown in FIG. 6(b), was then cut from each sintered body. The sample 16 has a cross sectional shape of a fan with an angle of 90°. The sample has a porous portion 3 with a shape of a fan including the center “O” of the fan 16 and an arc-shaped dense portion 2 formed along the peripheral part of the porous portion 3. The porous portion 3 has a radius of 35 mm and a thickness of 4 mm. The sample 16 has a radius of 50 mm and a thickness of 8 mm. The dense portion 2 has a width of 15 mm.

[0062] The sample 16 was measured using a tester to obtain a surface resistance of 5 to 30 M Ω between points “A” and “B” and a surface resistance of 0.10 to 0.11 M Ω between points “C” and “D”. The surface resistances of the porous and dense portions were different from each other by two-digit order. The surface resistance between points “A” and “D” was 2 to 16 M Ω, which was slightly lower than that of the porous portion alone. Such results are conformity with a relatively low surface resistance of the dense portion.

[0063] (Experiment “B”)

[0064] A sintered body 1A shown in FIG. 4 was produced according to the same process as the experiment “A”. Alumina or aluminum nitride coarse particles, with properties shown in table 3, were prepared.

3TABLE 3ExampleExampleExample678Raw materialAl2O3Al2O3AlNCoarse particleWA60WA100No. 1Maximum particle300150600Diameter (μm)Average particle250115400Diameter (μm)Minimum particle210105350Diameter (μm)Al2O3 (weight %)99.999.9—AlN (weight %)——99.9Free carbon (weight %)———SiO2 (weight %)0.010.010.003Total iron content0.010.010.001(weight %)ApplicationAbrasive grainAbrasive grain—

[0065] The coarse particles were mixed with a solution containing 5 percent of polyvinyl alcohol to obtain paste, which was then filled into a mold (cercle), removed from the mold, and dried at 110° C. for two hours to obtain a disk-shaped primary shaped body 7. The primary shaped body 7 was set in a metal mold. Ceramic fine particles 8 of alumina and aluminum nitride both with a purity of 99.9 percent and average particle diameters shown in table 4 were filled in the metal mold to cover the side face of the primary shaped body 7. The fine particles and primary shaped body were pressed at a compacting pressure of 200 kg/cm2 to obtain a secondary shaped body. The secondary shaped body was subjected to hot press sintering. The maximum temperature during the sintering was changed as shown in table 4. The holding time period at the maximum temperature was 2 hours. The temperature rising rate and cooling rate were 100° C. per hour. The sintering was carried out in 100 percent nitrogen.

[0066] The sintered body 1A as shown in FIGS. 4(a) and 4(b) was finally obtained. The porosity and four-point bending strength of each sintered body 1A were measured as described in the experiment “A”, and the results were shown in table 4.

4TABLE 4ExampleExampleExample678Raw materialAl2O3Al2O3AlNRaw coarse particleWA60WA100No. 1Maximum particle250115400diameter of raw coarseparticle (μm)Average particle0.50.51diameter of raw fineparticle (μm)Maximum temperature160016001850during sintering (° C.)Pressure during200200200sintering (kg/cm2)Atmosphere forN2N2N2sinteringPorosity of porous272128portion (%)Porosity of dense000portionFour point bending250270230Strength (MPa)

[0067] As can be seen from the results, the porous and dense portion of the inventive sintered body were integrated with a high strength.

[0068] The microstructure of the interface between the porous and dense portions of each sintered body according to the example 6, 7 or 8 was observed using photographs taken by a scanning electron microscope. The results of the observation were substantially same as the examples 2 and 4 described above.

[0069] Next, the dense portion 2A of each sintered body 1A according to the example 6, 7 or 8 was sealed at its end face using an O-ring. One space facing the main face la was thus separated from the other space facing the bottom face 1b by the O-ring. The pressure of helium gas was adjusted at 2 atm in the former space facing the main face 1a and was adjusted at 1 atm in the latter space facing the bottom face 1b, so as to measure the leakage of helium gas. As a result, the gas leakage did not observed through the dense portion 2A. It was thus confirmed that gas passes through the disk-shaped porous portion 3A from the main face 3a to the bottom face 3b.

[0070] As described above, a porous ceramic material and a dense ceramic material may be integrated with a sufficiently high strength according to the invention.

[0071] Moreover, it is not necessary to use solders or adhesives for bonding the porous and dense ceramic materials.

[0072] When applying a raw ceramic material with a high purity for producing a porous portion and/or dense portion in the inventive sintered body, such sintered body has the following three features. That is, the body has the porous and dense portions integrated with a sufficiently high strength, the body has at least one portion with a high purity, and the body does not need a solder or adhesive. Such sintered body may be useful and advantageous as a member or an article for a semiconductor producing system (for example, a shower plate) or a filter.

Number	Date	Country	Kind
P2001-071,891	Mar 2001	JP
P2001-379,962	Dec 2001	JP

Ceramic sintered bodies and a method of producing the same

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