Sialon based composite and method of manufacturing the same

BACKGROUND OF THE INVENTION
1. Field of the Invention
The present invention relates to a sialon based composite having excellent mechanical strength and fracture toughness and a method of manufacturing the same.
2. Description of the Related Art
Two sialons are generally known: .beta.-sialon which is represented by formula Si.sub.6-z Al.sub.z O.sub.z N.sub.8-z (wherein 0<z.ltoreq.4.2) and is obtained by adding Al.sub.2 O.sub.3, AlN, SiO.sub.2, and the like to Si.sub.3 N.sub.4, and heating the resultant mixture to solid-dissolve these additives in Si.sub.3 N.sub.4 (that is, to make a solid-solution), and .alpha.-sialon which is represented by formula Mx(Si,Al).sub.12 (O,N).sub.16 (wherein 0<x.ltoreq.2; M represents at least one element selected from the group consisting of Li, Na, Ca, Mg, Y, and rare-earth elements) and in which a metal is soliddissolved in the crystal lattice of Si.sub.3 N.sub.4. A sialon sintered body is excellent in heat resistance and oxidation resistance, and its strength is not degraded at high temperatures exceeding 1,300.degree. C. In addition, even if a sialon sintered body is oxidized at a high temperature, its properties are not impaired. Therefore, sialon sintered bodies are expected to be applied as mechanical component materials required for use at high temperatures. A typical example of such a mechanical component is a ceramic gas turbine.
Although a sialon sintered body is excellent in heat resistance and oxidation resistance, it has poor mechanical strength and fracture toughness which lead to a decisive drawback in practical applications. Extensive studies has been made to improve the mechanical strength and fracture toughness of the sialon sintered bodies. Among them all, some of sialon based composite containing SiC fibers in sialons have been developed, as disclosed in Published Unexamined Japanese Patent Application No. 62-12670.
In such a sialon based composite, although the fracture toughness can be improved to some extent, the mechanical strength cannot be sufficiently improved, and improvement on mechanical strength is left unsolved. Strong demand has arisen for further improvements on fracture toughness in practical applications.
Although attempts have been made to improve the mechanical strength and fracture toughness of sialons, a best solution has not yet been found.
SUMMARY OF THE INVENTION
It is an object of the present invention to provide a sialon based composite which has excellent mechanical strength and fracture toughness and can be used in practical applications, and a method of manufacturing the same.
According to an aspect of the present invention, there is provided a sialon based composite consisting essentially of 5 wt % to 40 wt % of SiC fibers, 0.3 wt % to 10 wt % of an Hf component which is calculated in terms of an Hf oxide, and the balance of sialon as a major constituent.
According to another aspect of the present invention, there is provided a method of manufacturing a sialon based composite, comprising the first step of preparing a powder mixture as a starting material consisting of 5 wt % to 40 wt % of SiC fibers, 0.3 wt % to 10 wt % of an Hf component which is calculated in terms of an Hf oxide, and the balance of Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3 as a sialon component, and the second step of sintering the powder mixture.
Additional objects and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objects and advantages of the invention may be realized and obtained by means of the instrumentalities and combinations particularly pointed out in the appended claims.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT
According to the present invention, there is provided a sialon based composite essentially consisting of 5 wt % to 40 wt % of SiC fibers, 0.3 wt % to 10 wt % of an Hf component which is calculated in terms of Hf oxide, and the balance of sialon as a major constituent. That is, the SiC fibers and the Hf component in the above composition ratio are added to the sialon.
The present inventors made extensive studies on additive components capable of increasing the mechanical strength of sialons and found that their mechanical strength was greatly increased upon addition of an Hf component in each sialon material. The addition of the Hf component is assumed to prevent growth of sialon grains to provide uniform fine grains. In addition, Hf itself as an additive component is present in the form of very fine grains of an Hf compound, and these grains are dispersed in a sintered body. Therefore, the grain boundary second phase having a low melting temperature is not formed and it is prevented that heat resistance and oxidation resistance of the composite are decreased by the grain boundary second phase.
A starting material of the Hf component is not limited to any specific one if it contains Hf. Examples of this starting material are Hf compounds (e.g., HfO.sub.2, HfC, HfN, HfB.sub.2, and HfSi.sub.2) and metal Hf. Along these materials, HfO.sub.2, HfC, and HfN are preferable. At least two of these materials may be mixed with each other. That is, the Hf component means Hf itself or an Hf compound. The content of the Hf component falls within the range of 0.3 to 10 wt % and preferably 1.0 wt % to 7.0 wt %. When the content of the Hf component is less than 0.3 wt %, a sufficient addition effect of the Hf component cannot be obtained. However, when the content of the Hf component exceeds 10 wt %, large grains of the Hf compound are undesirably obtained, and a sufficiently high mechanical strength cannot be obtained. In addition, addition in such a large amount results in an economical disadvantage.
Although the addition of an Hf component greatly improves the mechanical strength of sialon, the fracture toughness of the sialon is hardly changed if only the Hf component is added.
When the present inventors added SiC fibers known as an additive component for improving fracture toughness to sialon in addition to the Hf component, the fracture toughness could be greatly improved compared with a conventional sialon composite containing only SiC fibers. That is, the present inventors found that a sialon composite added with both SiC fibers and an Hf component to sialon greatly improves fracture toughness as compared with a sialon composite added with only SiC fibers. This fact is assumed to be based on the following mechanism.
In order to improve the fracture toughness of sialon upon addition of SiC fibers, an adhesive property of an interface between the sialon and the SiC fibers is an important factor. The improvement of the fracture toughness of the sialon upon addition of the SiC fibers to the sialon can be achieved when the SiC fibers dispersed in the sialon can be pulled out with an appropriate force. For this purpose, an appropriate adhesive property must be provided to the interface between the sialon and the SiC fibers. When an adhesion force acting on the interface is excessively large, the pull-out effect cannot be enhanced, and the fracture toughness cannot be improved. When the adhesion force acting on the interface is excessively small, growth of a crack formed in the sialon cannot be suppressed, and in this case too, the fracture toughness cannot be improved.
The Hf component as an additive component in the sialon based composite according to the present invention serves to provide an appropriate adhesive property to the interface between the sialon and the SiC fibers. That is, fine Hf compound grains formed in the sialon are present at the interface between the sialon grains and the SiC fibers and give the appropriate adhesive property described above.
Generally, a sialon material is relatively hard to sinter, and high-temperature sintering is required to consolidate a sialon composite. The SiC fibers as an additive component may be degraded during such hightemperature sintering. When an Hf component is added to the sialon, its sintering temperature can be lowered. Therefore, an addition of an Hf component can minimize degradation of the SiC fibers, and improves the fracture toughness of the sintered body.
The SiC fibers as one of the additive components described above may be single crystalline SiC whisker or polycrystalline SiC, and their length in the longitudinal direction is not limited to a specific value. When the length of the SiC fibers is increased, the fracture toughness of the sintered body can be increased. However, the mechanical strength tends to be decreased. Therefore, the length of the SiC fibers is preferably determined in consideration of environments in which composites are used. For example, when a sintered body is used under a condition wherein fracture toughness is of a primary importance, long fibers such as SiC continuous fibers are preferably used. However, when the mechanical strength is of a primary importance, short SiC whiskers are preferably used.
In addition, the SiC fibers may be composite fibers in which SiC layers are formed around C fibers as core fibers by a CVD method or the like.
The content of the SiC fibers falls within the range of 5 to 40 wt %, and preferably 10 to 30 wt %. When the content is less than 5 wt %, an addition effect of SiC fibers cannot be obtained. However, when the content of the SiC fibers exceeds 40 wt %, it is difficult to densify. In this case the density of the resultant sintered body is undesirably low, thus degrading properties such as mechanical strength.
In the sialon based composite according to the present invention, the sialon as the major constituent may be .beta.-sialon or .alpha.-sialon. The .beta.-sialon is better than the .alpha.-sialon to obtain a sialon based composite having better fracture toughness. .beta.-sialon is a sintered body having a composition defined by the following formula:
Si.sub.6-z Al.sub.z N.sub.8-z
(wherein 0<z.ltoreq.4.2) and can be generally obtained by sintering a mixture of Si.sub.3 N.sub.4, Al.sub.2 O.sub.3, AlN, SiO.sub.2, and the like. .alpha.-sialon is a sintered body having a composition defined by the following formula:
Mx(Si,Al).sub.12 (O,N).sub.16
(wherein 0<x.ltoreq.2; M represents at least one element selected from the group consisting of Li, Na, Ca, Mg, Y, and rare-earth elements) and can be generally obtained by sintering a mixture of Si.sub.3 N.sub.4, AlN, Y.sub.2 O.sub.3, and the like. According to the present invention, impurities and additives may be contained in the sialon as the major constituent in amounts small enough not to impair the effect of the present invention.
A method of manufacturing a sialon based composite according to the present invention will be described below. This method of manufacturing a sialon based composite, comprises the first step of preparing a powder mixture as a starting material consisting essentially of 5 wt % to 40 wt % of SiC fibers, 0.3 wt % to 10 wt % of an Hf component which is calculated in terms of Hf oxide, and the balance of Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3 as a sialon component, and the second step of sintering the powder mixture. The sialon based composite manufactured as described above contains .beta.-sialon as a major constituent. That is, the method according to the present invention is characterized in that two components, namely, Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3 are used as materials for obtaining the .beta.-sialon as the major constituent.
The .beta.-sialon represented by formula Si.sub.6-z Al.sub.z N.sub.8-z (wherein 0<z.ltoreq.4.2) has a crystal structure in which Al.sub.2 O.sub.3 is solid-dissolved in Si.sub.3 N.sub.4. When the two components, i.e., Si3N.sub.4 and Al.sub.2 O.sub.3 are used, the .beta.-sialon can be ideally prepared. In practice, however, it is difficult to sinter only Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3, and other components such as AlN and SiO.sub.2 described above are also used. These other components are left as grain boundary phases in the sialon sintered body and degrade resistance to oxidation of the sintered body. Therefore, use of these components is not preferable.
The method of the present invention has been made in consideration of the above situation, and the .beta.-sialon as the major constituent is obtained by using two components, i.e., Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3.
According to the present invention, the Hf component as an additive component can improve mechanical strength and fracture toughness of the sialon, decreases its sintering temperature, and enhances solid dissolving of Al.sub.2 O.sub.3 in Si.sub.3 N.sub.4. It is thus possible to constitute the sialon as the major constituent by Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3. In this case, degradation of resistance to oxidation caused by a grain boundary phase left in the sintered body does not occur. According to the manufacturing method of the present invention, in the first step, a powder mixture of a starting material consisting of SiC fibers, an Hf component, Si.sub.3 N.sub.4, and Al.sub.2 O.sub.3 is prepared. At this time, in order to obtain a sialon based composite having excellent mechanical strength and excellent fracture toughness, the content of the SiC fibers falls within the range of 5 to 40 wt %, preferably 10 to 30 wt %, and the content of the Hf component falls within the range of 0.3 to 15 wt %, preferably 1.0 wt % to 7.0 wt %, when this content is calculated in terms of its oxide. In addition, the content of the Al.sub.2 O.sub.3 preferably falls within the range of 5 to 30 wt %, and the balance is preferably Si.sub.3 N.sub.4.
In the second step, the powder mixture prepared in the first step is sintered. A hot-pressing or a normal pressure sintering method may be used in this sintering. The density of the resultant sintered body formed by the hot-pressing is higher than the density of the resultant sintered body formed by the normal pressure sintering.
According to the method of the present invention, as compared with a conventional method in which other components such as AlN and SiO.sub.2 are used together with the two components, i.e., Si.sub.3 N.sub.4 and Al.sub.2 O.sub.3, a sialon based composite having excellent properties such as resistance to oxidation can be easily obtained.
EXAMPLES
The present invention will be described in detail by way of its examples.
EXAMPLE 1
Powders of Hf compounds and sialon components which had composition ratios, shown in Table 1, were mixed with a plastic ball mill for about 12 hours to prepare each powder mixture. The sialon component powder was prepared in advance as follows.
As for an .alpha.-sialon component, 63.0 mol % of an Si.sub.3 N.sub.4 powder having an average grain size of 0.7 .mu.m, 33.3 mol % of an AlN powder having an average grain size of 0.8 .mu.m, and 3.7 mol % of a Y.sub.2 O.sub.3 powder having an average grain size of 0.9 .mu.m were mixed to prepare a powder represented by formula Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16.
As for a .beta.-sialon component, a powder represented by a composition of Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 and a powder represented by a composition of Si.sub.5 AlON.sub.7 were used. The Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 powder was obtained by using a synthetic .beta.-sialon powder SZ-2 (tradename) available from Ube, Industries, Ltd. or by mixing an Si.sub.3 N.sub.4 powder having an average grain size of 0.7 .mu.m, an AlN powder having an average grain size of 0.8 .mu.m, and an Al.sub.2 O.sub.3 powder having an average gain size of 0.9 .mu.m. The Si.sub.5 AlON.sub.7 powder was prepared by mixing the above powders.
SiC continuous fibers were aligned in one direction in each amount shown in Table 1 in each powder mixture, and were pressed at a pressure of about 1,000 kg/cm.sup.2, thereby obtaining each green body having a length of 50 mm, a width of 50 mm, and a thickness of 7 mm. Each green body was charged in a carbon mold and was hot-pressed in a nitrogen gas atmosphere at a temperature of 1,700.degree. C. and a pressure of 300 kg/cm.sup.2 for 30 minutes, thereby preparing sialon based composites represented by sample Nos. 1 to 20. These samples have compositions falling within the range of the present invention.
Each resultant sample was worked into a test piece having a size of 4 mm.times.3 mm.times.40 mm, and the strength of each sample was measured at room temperature and 1,300.degree. C. in accordance with a three-point bending test complying with the JIS (Japanese Industrial Standards). The fracture toughness of each sample was measured by an SENB method (Single Edge Notched Beam Method) at room temperature by forming a notch having a width of 0.1 mm and a depth of 0.75 mm in each sample. In the strength and fracture toughness measurements, a tensile stress acted in the same direction as the alignment direction of the SiC continuous fibers. The test results are summarized in Table 1.
As is apparent from Table 1, the resultant sialon based composites were not degraded at high temperatures and had excellent fracture toughness and excellent mechanical strength.
COMPARATIVE EXAMPLE 1
Following the same procedures as in Example 1, sialon based composite represented by sample Nos. 21 to 29 having compositions falling outside the range of the present invention were prepared using the additive components shown in Table 2 and powders of sialon components shown in Table 2 as starting materials.
The same tests as in Example 1 were performed for the resultant samples, and test results are summarized in Table 2. As is apparent from Table 2, the sialon based composites thus obtained had poorer mechanical strength and fracture toughness than those of the sintered bodies obtained in Example 1.
TABLE 1__________________________________________________________________________ Mechanical Mechanical Additive Component Strength Strength FractureSample HfO.sub.2 HfC HfN HfB.sub.2 HfSi.sub.2 SiC Continuous (1300.degree. C.) (1300.degree. C.) ToughnessNo. Sialon Component (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________ 1 Si.sub.5 AlON.sub.7 0.3 0 0 0 0 30 88.1 83.5 18.6 2 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 30 95.2 84.0 19.8 3 Si.sub.5 AlON.sub.7 5.0 0 0 0 0 30 91.1 83.1 19.0 4 Si.sub.5 AlON.sub.7 7.0 0 0 0 0 30 87.3 78.6 19.0 5 Si.sub.5 AlON.sub.7 10.0 0 0 0 0 30 83.4 75.5 18.8 6 Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 3.0 0 0 0 0 30 84.6 73.7 19.5 7 Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 (SZ-2) 3.0 0 0 0 0 30 83.8 71.5 19.3 8 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 3.0 0 0 0 0 30 80.6 70.6 18.0 9 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 5 85.0 81.6 15.410 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 10 86.1 81.8 16.811 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 15 93.6 82.0 17.912 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 25 90.3 80.1 19.213 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 40 81.4 74.2 17.414 Si.sub.5 AlON.sub.7 0 3.0 0 0 0 30 90.2 78.6 19.315 Si.sub.5 AlON.sub.7 0 0 3.0 0 0 30 88.2 80.2 19.216 Si.sub.5 AlON.sub.7 0 0 0 3.0 0 30 83.6 74.4 18.117 Si.sub.5 AlON.sub.7 0 0 0 0 3.0 30 82.7 73.1 17.918 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 0.3 0 0 0 0 30 75.2 70.6 17.819 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 7.0 0 0 0 0 30 78.2 68.4 17.920 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 10.0 0 0 0 0 30 76.7 67.9 17.6__________________________________________________________________________
TABLE 2__________________________________________________________________________ Mechanical Mechanical Additive Component Strength Strength FractureSample HfO.sub.2 HfC HfN HfB.sub.2 HfSi.sub.2 SiC Continuous (1300.degree. C.) (1300.degree. C.) ToughnessNo. Sialon Component (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________21 Si.sub.5 AlON.sub.7 0 0 0 0 0 0 52.1 53.0 3.322 Si.sub.5 AlON.sub.7 0 0 0 0 0 30 48.7 48.5 5.623 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 0 76.4 73.2 3.024 Si.sub.5 AlON.sub.7 0.1 0 0 0 0 30 44.2 42.1 5.825 Si.sub.5 AlON.sub.7 15.0 0 0 0 0 30 58.6 57.4 5.526 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 3 74.7 70.9 3.227 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 45 41.8 39.0 2.928 Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 0 0 0 0 0 0 48.8 47.2 2.829 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 0 0 0 0 0 0 45.5 42.4 2.8__________________________________________________________________________
EXAMPLE 2
Powders of additive components and sialon components which had composition ratios shown in Table 3 were mixed with a plastic ball mill for about 12 hours to prepare starting powder. The sialon component powders were prepared following the same procedures as in Example 1.
Sintering was performed by a hot-pressing. That is, each powder was cold-pressed at a pressure of about 1,000 kg/cm.sup.2 to obtain a green body. Each green body was charged in a carbon mold and sintered in a nitrogen gas atmosphere at a temperature of 1,750.degree. C. and a pressure of 300 kg/cm.sup.2 for 30 minutes, thereby preparing sialon based composite represented by sample Nos. 30 to 49. These samples have compositions falling within the range of the present invention.
The same tests as in Example 1 were performed for the resultant samples, and test results are shown in Table 3. As is apparent from Table 3, the sialon based composites thus obtained were not so degraded at high temperatures and had excellent mechanical strength and excellent fracture toughness.
COMPARATIVE EXAMPLE 2
Following the same procedures as in Example 2, sialon based composites represented by sample Nos. 50 to 57 having compositions falling outside the range of the present invention were prepared using additive and sialon components having the composition ratios shown in Table 4 as starting materials.
The same tests as in Example 2 were performed for the resultant samples, and test results are shown in Table 4. As is apparent from Table 4, the sialon based composites thus obtained had poorer mechanical strength and fracture toughness than those of the sintered bodies obtained in Example 2.
TABLE 3__________________________________________________________________________ Mechanical Mechanical Additive Component Strength Strength FractureSample HfO.sub.2 HfC HfN HfB.sub.2 HfSi.sub.2 SiC Whisker (1300.degree. C.) (1300.degree. C.) ToughnessNo. Sialon Component (wt %) (wt %) (wt %) (wt %) (wt %) (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________30 Si.sub.5 AlON.sub.7 0.3 0 0 0 0 20 105 98.0 9.331 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 20 114 101 9.432 Si.sub.5 AlON.sub.7 5.0 0 0 0 0 20 107 96.1 8.933 Si.sub.5 AlON.sub.7 8.0 0 0 0 0 20 102 90.2 8.834 Si.sub.5 AlON.sub.7 10.0 0 0 0 0 20 92.2 87.6 8.535 Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 3.0 0 0 0 0 20 103 94.6 9.036 Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 (SZ-2) 3.0 0 0 0 0 20 112 100 9.237 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 3.0 0 0 0 0 20 90.6 78.6 8.238 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 5 110 102 7.839 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 10 111 107 8.240 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 15 115 107 8.941 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 25 112 98.6 9.242 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 30 109 93.7 9.243 Si.sub.5 AlON.sub.7 0 3.0 0 0 0 20 113 100 9.244 Si.sub.5 AlON.sub.7 0 0 3.0 0 0 20 109 97.4 9.045 Si.sub.5 AlON.sub.7 0 0 0 3.0 0 20 98.6 79.5 8.646 Si.sub.5 AlON.sub.7 0 0 0 0 3.0 20 95.3 78.6 8.547 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 0.3 0 0 0 0 20 88.4 73.1 8.048 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 8.0 0 0 0 0 20 92.8 86.5 8.349 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 10.0 0 0 0 0 20 91.5 85.3 8.1__________________________________________________________________________
TABLE 4__________________________________________________________________________ Mechanical Mechanical Additive Component Strength Strength FractureSample HfO.sub.2 HfC HfN HfB.sub.2 HfSi.sub.2 SiC Whiskers (1300.degree. C.) (1300.degree. C.) ToughnessNo. Sialon Component (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________50 Si.sub.5 AlON.sub.7 0 0 0 0 0 0 52.1 55.0 3.351 Si.sub.5 AlON.sub.7 0 0 0 0 0 20 56.0 55.1 4.252 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 0 76.4 73.2 3.053 Si.sub.5 AlON.sub.7 0.1 0 0 0 0 20 58.8 58.9 4.254 Si.sub.5 AlON.sub.7 15.0 0 0 0 0 20 62.2 60.6 4.155 Si.sub.5 AlON.sub.7 3.0 0 0 0 0 3 80.7 80.4 3.056 Si.sub.4 Al.sub.2 O.sub.2 N.sub.6 0 0 0 0 0 0 48.8 47.2 2.857 Y.sub.0.4 (Si,Al).sub.12 (O,N).sub.16 0 0 0 0 0 0 45.5 42.4 2.6__________________________________________________________________________
EXAMPLE 3
Si.sub.3 N.sub.4 powders having an average grain size of 0.7 .mu.m, Al.sub.2 O.sub.3 powders having an average grain size of 0.9 .mu.m, and HfO.sub.2, HfN or HfC powders having an average grain size of 1 .mu.m were mixed in composition ratios shown in Table 5, and each mixing was performed with a plastic ball mill for about 12 hours to prepare a starting powder. SiC continuous fibers having compositions shown in Table 5 were aligned in one direction in the corresponding material powder as in Example 1, thereby preparing sialon based composites represented by sample Nos. 58 to 69 containing .beta.-sialon components as major constituents. These samples have compositions falling within the range of the present invention.
The same tests as in Example 1 were performed for these samples, and test results are summarized in Table 5. As is apparent from Table 5, the sialon based composites had excellent fracture toughness and sufficient mechanical strength.
COMPARATIVE EXAMPLE 3
Following the same procedures as in Example 3, sialon based composites represented by sample Nos. 70 to 72 having compositions falling outside the range of the present invention were prepared using additive and sialon components having the composition ratios shown in Table 6 as starting materials.
The same tests as in Example 3 were performed for the resultant samples, and test results are shown in Table 6. As is apparent from Table 6, the sialon based composites thus obtained had poorer mechanical strength and fracture toughness than those of the sintered bodies obtained in Example 3.
TABLE 5__________________________________________________________________________Sialon Mechanical MechanicalComponent Additive Component Strength Strength FractureSample Si.sub.3 N.sub.4 Al.sub.2 O.sub.3 HfO.sub.2 HfN HfC SiC Continuous (1300.degree. C.) (1300.degree. C.) ToughnessNo. (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________58 82 10 3 0 0 5 85 81 7.259 77 10 3 0 0 10 86 83 7.460 67 10 3 0 0 20 83 78 7.861 57 10 3 0 0 30 78 77 16.362 47 10 3 0 0 40 77 75 16.863 72 5 3 0 0 20 80 80 14.964 62 15 3 0 0 20 85 82 15.865 57 20 3 0 0 20 84 79 14.266 69 10 1 0 0 20 75 72 14.167 60 10 10 0 0 20 72 70 14.668 65 10 0 5 0 20 82 80 15.269 65 10 0 0 5 20 78 79 15.1__________________________________________________________________________
TABLE 6__________________________________________________________________________Sialon Mechanical MechanicalComponent Additive Component Strength Strength FractureSample Si.sub.3 N.sub.4 Al.sub.2 O.sub.3 HfO.sub.2 HfN HfC SiC Continuous (1300.degree. C.) (1300.degree. C.) ToughnessNo. (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________70 70 10 0 0 0 20 55 53 7.671 90 10 0 0 0 0 55 52 3.972 85 10 5 0 0 0 63 62 4.1__________________________________________________________________________
EXAMPLE 4
Powders of additive and sialon components having composition ratios shown in Table 7 were mixed with a plastic ball mill for about 12 hours to prepare starting powders. Following the same procedures as in Example 2, sialon based composites represented by sample Nos. 73 to 84 having .beta.-sialon components as major constituents were prepared. The samples have compositions falling within the range of the present invention.
The same tests as in Example 1 were performed for the resultant samples, and test results are shown in Table 7. As is apparent from Table 7, the sialon based composites thus obtained were not so degraded at high temperatures and had excellent mechanical strength and excellent fracture toughness.
COMPARATIVE EXAMPLE 4
Following the same procedures as in Example 4, sialon based composites represented by sample Nos. 85 to 87 having compositions falling outside the range of the present invention were prepared using additive and sialon components having the composition ratios shown in Table 8 as starting materials.
The same tests as in Example 4 were performed for the resultant samples, and test results are shown in Table 8. As is apparent from Table 8, the sialon based composites thus obtained had poorer mechanical strength and fracture toughness than those of the sintered bodies obtained in Example 4.
Additional advantages and modifications will readily occur to those skilled in the art. Therefore, the invention in its broader aspects is not limited to the specific details, illustrated examples shown and described. Accordingly, various modifications may be made without departing from the spirit or scope of the general inventive concept as defined by the appended claims and their equivalents.
TABLE 7__________________________________________________________________________Sialon Mechanical MechanicalComponent Additive Component Strength Strength FractureSample Si.sub.3 N.sub.4 Al.sub.2 O.sub.3 HfO.sub.2 HfN HfC SiC Continuous (1300.degree. C.) (1300.degree. C.) ToughnessNo. (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________73 82 10 3 0 0 5 105 104 7.274 77 10 3 0 0 10 106 106 7.475 67 10 3 0 0 20 103 105 7.876 57 10 3 0 0 30 100 98 8.177 47 10 3 0 0 40 98 100 8.378 72 5 3 0 0 20 100 96 7.579 62 15 3 0 0 20 105 107 7.980 57 20 3 0 0 20 106 102 7.481 69 10 1 0 0 20 96 96 7.182 60 10 10 0 0 20 94 98 7.383 65 10 0 5 0 20 102 105 7.784 65 10 0 0 5 20 100 100 7.7__________________________________________________________________________
TABLE 8__________________________________________________________________________Sialon Mechanical MechanicalComponent Additive Component Strength Strength FractureSample Si.sub.3 N.sub.4 Al.sub.2 O.sub.3 HfO.sub.2 HfN HfC SiC Continuous (1300.degree. C.) (1300.degree. C.) ToughnessNo. (wt %) (wt %) (wt %) (wt %) (wt %) Fiber (wt %) (kg/mm.sup.2) (kg/mm.sup.2) (MPam.sup.1/2)__________________________________________________________________________85 70 10 0 0 0 20 58 56 4.486 90 10 0 0 0 0 55 52 3.987 85 10 5 0 0 0 63 62 4.1__________________________________________________________________________

Number	Date	Country	Kind
1-117512	May 1989	JPX
1-329510	Dec 1989	JPX

Number	Name	Date
4547470	Tanase et al.	Oct 1985
4705761	Kosugi	Nov 1987
4801564	Buba	Jan 1989
4946807	Okuno et al.	Aug 1990

Number	Date	Country
202504	Nov 1986	EPX
209320	Jan 1987	EPX
3423911	Jan 1985	DEX
0246269	Dec 1985	JPX
61-291463	Dec 1986	JPX
62-12670	Jan 1987	JPX

Sialon based composite and method of manufacturing the same

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