JPH11292633A - Silicon nitride-based ceramic part - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide the mechanical strength comparable to that of a silicon nitride-based ceramic sintered compact sintered by a hot pressing and further readily form a complicated shape by including a glass phase in a silicon nitride- based ceramic sintered compact obtained according to sintering under atmospheric pressure. SOLUTION: A glass phase present in a silicon nitride-based sintered ceramic part is derived from a preadded sintering assistant and one or more kinds selected from yttrium oxide, aluminum oxide and aluminum nitride are used as the sintering assistant. The silicon nitride-based ceramic part is obtained by cutting a silicon nitride-based ceramic sintered compact prepared by sintering under atmospheric pressure into a prescribed shape and heat-treating the cut compact at a lower temperature than the sintering temperature of the silicon nitride-based ceramic sintered compact and a higher temperature than the softening temperature of the glass phase.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to a silicon nitride ceramic part, and more particularly, to a silicon nitride ceramic part obtained by normal pressure sintering having excellent mechanical strength.

[0002]

2. Description of the Related Art Conventionally, when a product requiring high precision, such as a bearing or a ball bearing, is manufactured using a ceramic sintered body, a product having a size larger than a final dimension is manufactured with relatively low precision. Molding and firing have been performed, and the ceramic sintered body thus obtained has been subjected to cutting to obtain a final shape.

[0003]

However, in a ceramic part manufactured by such a method, micro sharp notches are formed in the cutting process, and the mechanical strength is reduced to obtain desired characteristics. There was a problem that it was not possible.

[0004] In particular, when a component made of a silicon nitride-based ceramics sintered body is used as a ceramic component requiring high mechanical strength as described above, a sintered structure having a dense structure and a density close to an ideal density is obtained. A hot press was used as a bonding method.

[0005] However, a silicon nitride ceramic sintered body sintered by hot pressing has high mechanical strength, but it is difficult to form a complicated shape. In addition, a hot press performed under high temperature and high pressure requires a special furnace for equipment and the like, so that the cost is high and a better method has been desired.

On the other hand, a silicon nitride ceramic sintered body sintered by normal pressure sintering can be easily formed into a complicated shape, but has a mechanical strength of less than 100 kg / mm ² .

The present invention has been made in view of such conventional disadvantages, and has a mechanical strength equivalent to that of a silicon nitride-based ceramic sintered body sintered by hot pressing, and is easily formed into a complicated shape. It is an object of the present invention to provide a ceramic component made of a silicon nitride-based ceramic sintered body sintered by normal pressure sintering, which can reduce the cost.

[0008]

According to a first aspect of the present invention, there is provided a silicon nitride ceramic part obtained by normal pressure sintering, wherein the sintered body contains a glass phase. Silicon nitride ceramic parts.

According to a second aspect, the glass phase present in the silicon nitride-based ceramic part is a glass phase comprising a sintering additive added in advance.
The silicon nitride-based ceramic part according to the above.

According to a third aspect of the present invention, the sintering aid is at least one selected from the group consisting of yttrium oxide, aluminum oxide and aluminum nitride.

Further, the silicon nitride-based ceramic part of the present invention is obtained by cutting a silicon nitride-based ceramic sintered body obtained by normal pressure sintering into a predetermined shape, and sintering temperature of the silicon nitride-based ceramic sintered body. At lower temperatures than
Further, it is a silicon nitride-based ceramic part obtained by heat treatment at a temperature higher than the softening point temperature of the glass phase.

The heat treatment temperature in the present invention needs to be 800 ° C. or more, which is the softening point of the glass phase of yttrium oxide, aluminum oxide, and aluminum nitride of the silicon nitride-based ceramics sintered body. Further, even in the presence of oxygen, such as in the atmosphere, the temperature at which oxidation of the silicon nitride-based ceramics sintered body hardly proceeds must be 1100 ° C. or less.

The heat treatment time is suitably 1 to 24 hours, but when the heat treatment temperature is low, the heat treatment time is long, and when the heat treatment temperature is high, the heat treatment time tends to be short. There is. In general, the quality of a product is better when the heat treatment temperature is lower and the heat treatment time is longer than when the heat treatment temperature is higher and the heat treatment time is shorter.

According to the present invention, the microscopic notch formed at the time of cutting is rounded by heat treatment. On the surface of the silicon nitride-based ceramic component obtained by normal-pressure sintering, an extremely thin oxide film layer of sub-micron made of silicon dioxide is formed to protect the surface of the silicon nitride-based ceramic component. Due to these interactions,
The mechanical strength of the silicon nitride-based ceramic part is further improved, and a silicon nitride-based ceramic part having the same mechanical strength as the silicon nitride-based ceramic part obtained by conventional hot pressing can be obtained.

[0015]

Embodiments of the present invention will be described below. Example 1 100 parts by weight of Si ₃ N ₄ 5 parts by weight of Y ₂ O _{3 3} parts by weight of AlN 3 parts by weight of Al ₂ O _{3 The} binder was added to the above mixed powder, pressed into a flat plate, and pressed at 700 ° C. After degreasing for 1 hour, 1750 ° C at normal pressure
For 3 hours to obtain a flat silicon nitride ceramic sintered body of 100 mm × 100 mm × 12 mm.

Next, as a final finish of the flat silicon nitride ceramic sintered body, a diamond rod having a grain size of # 400 was cut into a piece of 3 mm × 4 mm × 40 mm to prepare a square rod-shaped test sample. The bending strength was measured by three-point bending at a distance of 20 mm between the gauges as it was (Comparative Example 1), and the remaining 25 samples were measured in air at 1000
After heat treatment at 2 ° C. for 2 hours, bending strength was measured under the same conditions (Example 1). The results are shown in Table 1.

[0017]

[Table 1]

The Weibull distribution was as shown in FIG. 1 (Example 1) and FIG. 2 (Comparative Example 2). - Example 2 Si ₃ by adding N4 100 parts by weight of Y ₂ O ₃ 5 parts by weight Al ₂ O ₃ 3 parts by weight of the binder in the mixed powder of the pressure-molding into a flat plate, was degreased 3 hours at 700 ° C., 1750 ° C at normal pressure
For 3 hours to obtain a flat silicon nitride ceramic sintered body of 100 mm × 100 mm × 12 mm.

Next, as a final finish of the flat silicon nitride ceramic sintered body, a square rod-shaped test sample was prepared by cutting the sample into 3 mm × 4 mm × 40 mm using a diamond disk having a grain size of # 600. The flexural strength was measured by three-point bending at a distance between the gauge points of 20 mm (Comparative Example 2).
After the heat treatment at 2 ° C. for 2 hours, the transverse rupture strength was measured under the same conditions (Example 2). Table 2 shows the results.

[0020]

[Table 2] The Weibull distribution was as shown in FIG. 3 (Example 2) and FIG. 4 (Comparative Example 2).

[0021]

As is apparent from the above description, the silicon nitride-based ceramic part obtained by the normal pressure sintering of the present invention has a very high mechanical strength despite being subjected to grinding, and has a large bearing strength. It can be used advantageously for structural components such as bearings and bearings.

In addition, since it is not necessary to perform the heat treatment in a non-oxidizing atmosphere (such as a nitrogen atmosphere or an inert atmosphere) as in the prior art, the heat treatment is easy, and the use of air reduces the cost.

Further, since the sintered body used for the silicon nitride-based ceramic part is sintered by normal pressure sintering, equipment such as a furnace can be simpler than when sintering by hot pressing, and the cost can be reduced. And maintenance became easier.

[Brief description of the drawings]

FIG. 1 is a graph showing a Weibull distribution according to Example 1 of the present invention.

FIG. 2 is a graph showing a Weibull distribution of Comparative Example 1 of the present invention.

FIG. 3 is a graph showing a Weibull distribution according to a second embodiment of the present invention.

FIG. 4 is a graph showing a Weibull distribution of Comparative Example 2 of the present invention.

Claims (3)

[Claims] 1. A silicon nitride ceramic part obtained by normal pressure sintering, wherein the sintered body contains a glass phase. 2. The silicon nitride-based ceramic part according to claim 1, wherein the glass phase present in the silicon nitride-based ceramic part is a glass phase comprising a sintering agent added in advance. 3. The silicon nitride-based ceramic part according to claim 2, wherein the sintering aid is at least one selected from yttrium oxide, aluminum oxide and aluminum nitride.