JPH11189926A - Amorphous inorganic fiber - Google Patents

Abstract

(57) [Summary] [Problem] It has high tensile strength from room temperature to high temperature, has viscous flow processability, and is suitable for a wide range of other uses such as heat insulating materials, filter materials or reinforcing materials such as plastics, metals, ceramics, concrete, etc. An amorphous inorganic fiber that can be suitably used is provided. SOLUTION: This is composed of A (A is Al or Cr), O and at least one rare earth metal element,
It has a viscous flow processability in a temperature range of 1100 ° C.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an amorphous inorganic fiber used for a wide variety of uses such as a heat insulating material, a filter material or a reinforcing material such as plastic, metal, intermetallic compound, ceramics and concrete. .

[0002]

2. Description of the Related Art Glass fibers are used in a wide variety of applications such as heat insulating materials for houses and the like and reinforcing materials for plastics and concrete. This is due to the fact that the glass fiber has a high strength due to an amorphous structure or the like and is inexpensive. However, glass fibers have a remarkable decrease in strength at high temperatures, and therefore cannot be used as a high-temperature structural member. In addition, glass fibers are mainly composed of SiO ₂ and are generally alkali metal oxides and / or alkaline earth metals. Due to the inclusion of the oxide, for example, as a reinforcing material, only a base material which has a low molding temperature and does not cause a chemical reaction with the above substances at that temperature must be used.

On the other hand, in order to improve the elastic modulus and high-temperature strength of a metal, a method of reinforcing the metal with whiskers, short fibers, continuous fibers, and the like is effective. Manufacturing research is ongoing. Above all in the case of using a continuous fiber as reinforcing fiber, the elastic modulus, since the improvement in strength, etc. is significant, currently, metal matrix composite material using Al ₂ O ₃ system, the continuous fibers of the SiC-based such as reinforcing fibers Has been most actively researched.

[0004] However, these continuous fibers do not have sufficient ductility at any temperature range, and a continuous fiber reinforced metal matrix composite material is replaced with a conventional metal material, a whisker or a short fiber reinforced metal matrix. It is not possible to perform a secondary molding like a composite material. Therefore, the shape of continuous fiber reinforced metal matrix composites is currently limited to relatively simple shapes, and while having a sufficient strength at the highest operating temperature, it can be used for a wide range of applications. However, it is necessary to develop continuous fibers having ductile workability near the molding temperature.

[0005] US Patent No. 5,605,870 discloses that
Ceramic fibers made from a melt having a viscosity of 0 poises or less are disclosed. This fiber is produced by a so-called melt extraction method known per se and is composed of an amorphous phase and / or a crystalline phase. However, there is no description about the relationship between the composition and physical properties of the fiber composed of only the amorphous phase.

[0006]

SUMMARY OF THE INVENTION In view of the above situation, the present inventors have conducted intensive studies to obtain fibers having high strength, almost no deterioration in performance at high temperatures, and ductile workability. And found a novel amorphous inorganic fiber described in the present invention. That is, A (A is Al, Cr, Ti, Zr,
At least one element selected from the group consisting of Hf, Mn, Fe, Ni, Ga and Ge), O and a melt composed of at least one rare earth metal element are contacted with a rotating roll, cooled, and cooled. Amorphous inorganic fibers produced by coagulation into fibers have sufficient strength as reinforcing fibers, and the strength does not decrease even at a high temperature (800 ° C.). It has been found that the fiber has a property which cannot be obtained by the conventional fiber, that is, has viscous flow processability.

An object of the present invention is to have a high tensile strength from room temperature to a high temperature, a viscous flow processability, a heat insulating material, a filter material or a reinforcing material such as a plastic, a metal, an intermetallic compound, a ceramic, a concrete and the like. An object of the present invention is to provide an amorphous inorganic fiber that can be suitably used for a wide range of applications.

[0008]

Hereinafter, the present invention will be described in detail. The present invention relates to A (A is Al, Cr, Ti,
At least one element selected from the group consisting of Zr, Hf, Mn, Fe, Ni, Ga and Ge), O and at least one rare earth metal element,
The present invention relates to an amorphous inorganic fiber having viscous flow processability in a temperature range of 1100 ° C.

This amorphous inorganic fiber is produced by rapidly cooling a melt of the constituent elements and solidifying it into a fine wire. Here, “viscous flow workability” means the formability using plastic deformation due to viscous flow in the supercooled liquid region. The term “amorphous” means an atomic structure of a material that shows a broad halo pattern by X-ray diffraction.

[0010]

DETAILED DESCRIPTION OF THE INVENTION As A, Al, Cr, Ti,
Examples include at least one element selected from the group consisting of Zr, Hf, Mn, Fe, Ni, Ga, and Ge. Al and Cr are particularly preferred because the high-temperature strength of the obtained amorphous fiber is increased. When A is two or more elements, or in addition to the above elements, Mg, Ca, B
When at least one element selected from the group consisting of a and Si is contained, the resulting fiber is likely to be amorphous.

The rare earth metal elements include Gd, La, S
m, Y, Ce, Pr, Nd, Eu, Dy, Yb, Er,
At least one element selected from the group consisting of Tb, Ho, Tm and Lu is mentioned, and in particular, Gd, La, S
m is preferable because the strength of the obtained amorphous inorganic fiber increases.

The proportion of A in the amorphous inorganic fiber of the present invention is expressed as A ₂ O _{3 in} the case of Al, Cr, Fe, Ga.
Ti, Zr, Hf, in the case of Ge in AO ₂ terms, Mn,
In the case of Ni, it is preferably in the range of 10 to 90 mol% in terms of AO. The shape of the amorphous inorganic fiber of the present invention is not particularly limited, but preferably has a circular or nearly circular cross section. The amorphous inorganic fiber of the present invention can be used as a continuous fiber or a short fiber.

The dimensions of the cross section of the amorphous inorganic fiber are not limited to the cross-sectional shape, but the diameter is preferably 3 to 50 μm, more preferably 5 to 30 μm. The tensile strength of the amorphous inorganic fiber at room temperature, preferably at 800 ° C., is desirably 2.0 GPa or more, preferably 2.5 GPa or more. The amorphous inorganic fiber of the present invention has 850
It is characterized by having a viscous flow processability within a temperature range of up to 1100 ° C., and after forming a material or a molded body reinforced with the amorphous inorganic fiber of the present invention using the viscous flow processability, Also, the amorphous inorganic fiber of the present invention can substantially not lose its strength (room temperature to 800 ° C.).
Therefore, the amorphous inorganic fiber of the present invention is useful as a reinforcing inorganic fiber having secondary formability.

[0014] The amorphous inorganic fiber of the present invention comprises A (A is A
1, Cr, Ti, Zr, Hf, Mn, Fe, Ni, Ga
And at least one element selected from the group consisting of Ge and Ge), O and at least one rare earth metal element are quenched by a method such as contact with a rotating roll, and solidified into a fine wire. It can be manufactured by the following.

As a raw material before melting, an oxide of A and an oxide of a rare earth metal element are generally used.
A carbonate or the like may be used. In addition, as a form of the raw material,
Any of a powder, a molded body, a sintered body, and a solidified body may be used, or a combination of two or more of these may be used.

The method for dissolving the raw material may be any method as long as it can heat at least a portion of the raw material that comes into contact with the rotating roll to a temperature equal to or higher than the melting point thereof. , Laser, electron beam, light, infrared, high frequency and the like can be used. When a high frequency is used, the raw material has little conductivity near room temperature, so it is necessary to store the raw material in a crucible having conductivity and a melting point higher than the melting point of the raw material. For example, crucibles such as Mo, W, Ta, Ir, and Nb are preferably used. Also, when the raw material is a powder, it is necessary to use a crucible or a support base of the above material,
In this case, in addition to the above crucible, a Cu crucible cooled with water or the like, a support, or the like can be used.
Even when the raw material is not a powder, these crucibles, supports, and the like can be suitably used.

The raw material may be dissolved in any atmosphere such as the atmosphere, an inert gas, a reducing gas, a hydrocarbon gas, or a vacuum, but it is easily oxidized at a temperature lower than the melting point of the raw material. When a crucible or the like is used, the melting is preferably performed in an atmosphere of an inert gas such as an argon gas or a helium gas or in a vacuum. When the raw material is melted by the arc, it is necessary that the atmosphere contains an argon gas or the like sufficient to generate the arc.

The material of the rotating roll is not particularly limited,
A material having a high thermal conductivity or a metal having a high melting point is preferred from the viewpoint of the life of the roll and the stability of the quality of the obtained fiber. Specifically, Cu, Cu alloy, Mo, Ta, W, Ir and the like can be suitably used.

The contact between the rotating roll and the melt can be, for example,
Either a mode in which the tip of the rotary roll is brought into rotary contact with the melt or a mode in which the melt is dropped on the rotary roll may be used. However, the tip of the rotating roll is brought into rotary contact with the melt, and the shape of the rotating roll, whose tip can contact the melt with a small area, is required to make the cross-sectional shape of the resulting fiber uniform. For example, as shown in FIG. 1, a rotating roll having a V-shaped protrusion at the tip can be suitably used.

It is desirable that the peripheral speed of the rotating roll when the rotating roll is brought into contact with the melt is 10 m / sec or less. If the peripheral speed is faster than 10m / sec,
This is because it may be difficult to obtain a fiber having a constant cross-sectional area.

As an apparatus for producing the amorphous fiber of the present invention, for example, an apparatus having a mechanism as shown in FIG. 2 can be used. Melt composed of A (A is Al or Cr), O, and rare earth metal element dissolved by an arc (3) generated between a W electrode (1) and a water-cooled Cu crucible (2) The amorphous inorganic fiber (6) is obtained by moving the liquid (4) in a horizontal direction through a Cu crucible to contact a roll (5) rotating in the direction of the arrow and solidifying it in a fine line shape.

In addition, a known production method and production apparatus can be used as a method for producing an amorphous metal. In short, what is necessary is just to be able to produce under the condition that the amorphous inorganic fiber having the characteristics of the present invention can be obtained.

[0023]

The present invention will be described more specifically below with reference to examples and comparative examples. Example 1 α-Al ₂ O ₃ powder and Y ₂ O ₃ powder were used as raw materials.
α-Al ₂ O ₃ powder and Y ₂ O ₃ powder in molar ratio of 8
2. The latter was mixed at a ratio of 18 by a wet ball mill using ethanol, and ethanol was removed from the obtained slurry using a rotary evaporator.

The obtained mixed powder is formed into a cylindrical shape having a diameter of 10 mm and a height of 10 mm by a uniaxial press using a stainless steel die, and then the cylindrical formed body is melted by an arc to obtain a button-shaped solidified body. Was. This button-shaped solidified body is housed in a water-cooled Cu crucible (2) shown in FIG. 2, and then the system in which the mechanism of FIG. 2 is housed is set to an argon gas atmosphere of -0.04 MPa, and the W electrode and An arc was generated between the Cu crucibles. The button-shaped solidified body is melted by an arc, and while maintaining this melted state, the Cu crucible is moved to rotate the Cu crucible at a peripheral speed of 2 m / sec. This was brought into contact with a production roll to obtain continuous fibers having an average diameter of 15 μm.

The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα ray. The tensile test of this fiber was performed at room temperature at a load speed of 2 mm / min.
In the case of air at 800 ° C. and 1000 ° C. under the conditions of a span of 25 mm, the loading speed was 2 mm / min, and the span was 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C.

In a tensile test at 1000 ° C., the fiber exhibited a 150% elongation under low stress. In other words, although this fiber has sufficient strength equivalent to room temperature at a temperature not lower than the substantially maximum use temperature (600 ° C. or more in the case of Ti base) of the fiber-reinforced metal matrix composite material, it has a temperature higher than that temperature. It was shown that at a temperature at which the metal material of Example 1 can be formed, it has viscous flow processability.

Example 2 Continuous fibers were produced in the same manner as in Example 1 except that α-Al ₂ O ₃ powder and Gd ₂ O ₃ powder were used as raw material powders and the mixing ratio was 78:22 in molar ratio. Obtained. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 220% elongation under low stress.

Example 3 α-Al ₂ O ₃ powder and La ₂ O ₃ powder were used as raw material powders, the mixing ratio was 77.5: 22.5 in molar ratio, and the peripheral speed of the rotating roll was 1 m / Continuous fibers were obtained in the same manner as in Example 1 except that sec was set. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was performed at a load speed of 2 mm / min and a span of 25 mm at room temperature.
In the case of air at 900 ° C. and 900 ° C., the test was performed under the conditions of a load speed of 2 mm / min and a span of 100 mm. Measured room temperature and 8
Table 1 shows the average value of the tensile strength at 00 ° C. In a tensile test at 900 ° C., the fiber exhibited 230% elongation under low stress.

Example 4 The same method as in Example 1 except that α-Al ₂ O ₃ powder and Pr ₆ O ₁₁ powder were used as raw material powders, and the mixing ratio was 78.8: 21.2 in molar ratio. To obtain a continuous fiber. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out at room temperature under a load speed of 2 mm / min and a span of 25 mm.
In the case of air at 900 ° C. and 900 ° C., the test was performed under the conditions of a load speed of 2 mm / min and a span of 100 mm. Measured room temperature and 8
Table 1 shows the average value of the tensile strength at 00 ° C. In tensile testing at 900 ° C., the fiber exhibited 160% elongation under low stress.

Example 5 The same method as in Example 1 except that α-Al ₂ O ₃ powder and Nd ₂ O ₃ powder were used as raw material powders and the mixing ratio was 80.3: 19.7 in molar ratio. To obtain a continuous fiber. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out under the conditions of a load speed of 2 mm / min and a span of 25 mm at room temperature.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 170% elongation under low stress.

Example 6 Continuous fibers were produced in the same manner as in Example 1 except that α-Al ₂ O ₃ powder and Sm ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 69:31 in molar ratio. Obtained. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of this fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 220% elongation under low stress.

Example 7 The same method as in Example 1 except that α-Al ₂ O ₃ powder and Eu ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 71.7: 28.3 in molar ratio. To obtain a continuous fiber. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

Further, the tensile test of this fiber was carried out under the conditions of a load speed of 2 mm / min and a span of 25 mm at room temperature.
In the case of air at 900 ° C. and 900 ° C., the test was performed under the conditions of a load speed of 2 mm / min and a span of 100 mm. Measured room temperature and 8
Table 1 shows the average value of the tensile strength at 00 ° C. In a tensile test at 900 ° C., the fiber exhibited 170% elongation under low stress.

Example 8 The same method as in Example 1 except that α-Al ₂ O ₃ powder and Dy ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 78.9: 21.1 in molar ratio. To obtain a continuous fiber. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 160% elongation under low stress.

Example 9 The same method as in Example 1 except that α-Al ₂ O ₃ powder and Yb ₂ O ₃ powder were used as raw material powders and the mixing ratio was 83.7: 16.3 in molar ratio. To obtain a continuous fiber. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out at room temperature under a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 180% elongation under low stress.

Example 10 The same method as in Example 1 except that α-Al ₂ O ₃ powder and Er ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 81.1: 18.9 in molar ratio. To obtain a continuous fiber. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 170% elongation under low stress.

Example 11 Continuous fibers were obtained in the same manner as in Example 1 except that Cr ₂ O ₃ powder and Gd ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 80:20 in molar ratio. . The structure of the obtained fiber is
X-ray diffraction using Cu-Kα rays showed a broad halo pattern, indicating that it was amorphous.

Further, the tensile test of this fiber was carried out at room temperature under a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 200% elongation under low stress.

Example 12 Continuous fibers were obtained in the same manner as in Example 1 except that Cr ₂ O ₃ powder and Er ₂ O ₃ powder were used as raw material powders, and the molar ratio was 78:22. . The structure of the obtained fiber is
X-ray diffraction using Cu-Kα rays showed a broad halo pattern, indicating that it was amorphous.

Further, the tensile test of the fiber was performed at a load speed of 2 mm / min and a span of 25 mm at room temperature.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 160% elongation under low stress.

Example 13 Continuous fibers were obtained in the same manner as in Example 1 except that ZrO ₂ powder and La ₂ O ₃ powder were used as raw material powders and the mixing ratio was 65:35 in molar ratio. The structure of the obtained fiber is C
X-ray diffraction using u-Kα rays showed a broad halo pattern, indicating that it was amorphous.

The tensile test of this fiber was carried out at room temperature under a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 160% elongation under low stress.

Example 14 Example 1 was the same as Example 1 except that MnO powder and Gd ₂ O ₃ powder were used as raw material powders, the mixing ratio was 27:73 in molar ratio, and the peripheral speed of the rotating roll was 1 m / sec. Continuous fibers were obtained in the same manner. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of the fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 170% elongation under low stress.

Example 15 Continuous operation was performed in the same manner as in Example 1 except that Fe ₂ O ₃ powder and Sm ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 16.8: 83.2 in molar ratio. Fiber was obtained. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

Further, the tensile test of this fiber was carried out under the conditions of a load speed of 2 mm / min and a span of 25 mm at room temperature.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 180% elongation under low stress.

Example 16 A continuous method was performed in the same manner as in Example 1 except that Ga ₂ O ₃ powder and Gd ₂ O ₃ powder were used as raw material powders, and the mixing ratio was 69.2: 30.8 in molar ratio. Fiber was obtained. The structure of the obtained fiber was found to be amorphous by showing a broad halo pattern by X-ray diffraction using Cu-Kα radiation.

The tensile test of this fiber was carried out under the conditions of a load speed of 2 mm / min and a span of 25 mm at room temperature.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited a 170% elongation under low stress.

Example 17 GeO ₂ powder and La ₂ O ₃ powder were used as raw material powders, the mixing ratio was 45.5: 54.5 in molar ratio, and the peripheral speed of the rotating roll was 1.5 m / sec. A continuous fiber was obtained in the same manner as in Example 1 except that the procedure was repeated. The structure of the obtained fiber is
X-ray diffraction using Cu-Kα rays showed a broad halo pattern, indicating that it was amorphous.

The tensile test of the fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 160% elongation under low stress.

Example 18 α-Al ₂ O ₃ powder, Y ₂ O ₃ powder and Mg
O powder was used, and the mixing ratio was 66.3: 32.
Continuous fibers were obtained in the same manner as in Example 1 except that the ratio was 7: 1. The structure of the obtained fiber was X-ray using Cu-Kα ray.
A broad halo pattern was shown by line diffraction, indicating that it was amorphous.

The tensile test of the fiber was carried out at room temperature at a load speed of 2 mm / min and a span of 25 mm.
℃, 1000 ℃ in the case of air load speed 2mm / min,
The test was performed under the condition of a span of 100 mm. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. 1000
In tensile tests at 0 ° C., the fiber exhibited 190% elongation under low stress.

Comparative Example 1 α-Al ₂ O ₃ powder and ZrO ₂ powder were used as raw materials, the mixing ratio of which was 62 in the former and 38 in the latter, and the peripheral speed of the rotating roll was 0.5 m / sec. A continuous fiber having an average diameter of 15 μm was obtained in the same manner as in Example 1 except that the above procedure was repeated.
The structure of the obtained fiber showed a broad halo pattern and a sharp peak by X-ray diffraction using Cu-Kα radiation, indicating that an amorphous phase and a crystalline phase were mixed. Was.

Room temperature and 800 ° C., 1000
A tensile test in air at ℃ was performed under the same conditions as in Example 1. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. In a tensile test at 1000 ° C., the fiber broke brittlely and had a tensile strength of 0.3 GPa.

Comparative Example 2 α-Al ₂ O ₃ powder, ZrO ₂ powder, and TiO ₂ were used as raw materials, and the mixing ratio was 44.8, 37.
Continuous fibers having an average diameter of 15 μm were obtained in the same manner as in Comparative Example 1 except that the composition was changed to 9,17.3. The structure of the obtained fiber showed a broad halo pattern and a sharp peak by X-ray diffraction using Cu-Kα radiation, indicating that an amorphous phase and a crystalline phase were mixed. Was.

Room temperature and 800 ° C., 1000
A tensile test in air at ℃ was performed under the same conditions as in Example 1. Table 1 shows the average values of the measured tensile strengths at room temperature and 800 ° C. In a tensile test at 1000 ° C., the fiber broke brittlely and had a tensile strength of 0.1 GPa.

[0065]

[Table 1]

[0066]

According to the present invention, the tensile strength from room temperature to high temperature is high, the material has viscous flow processability, and is used for heat insulating materials, filter materials or reinforcing materials such as plastics, metals, ceramics, concretes, etc. An amorphous inorganic fiber that can be suitably used for an application is provided.

[Brief description of the drawings]

FIG. 1 is a drawing showing an example of the shape of a rotating roll used for producing the amorphous inorganic fiber of the present invention.

FIG. 2 is a drawing showing an example of a mechanism of an apparatus used for producing an amorphous inorganic fiber of the present invention.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 ... W electrode 2 ... Cu crucible 3 ... Arc 4 ... Melt 5 ... Roll 6 ... Amorphous inorganic fiber

 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Yoshiharu Waku, 5-1978 Kogushi, Oji, Ube City, Yamaguchi Prefecture Inside Ube Research Institute, Ltd. Ube Research Institute Co., Ltd. (72) Inventor Hideki Ohtsubo, Ube-shi, Yamaguchi Prefecture, 1978 Kogushi, 5 Ube Kosan Co., Ltd. Inside Ube Research Institute Co., Ltd.

Claims (7)

[Claims] 1. A (A is Al, Cr, Ti, Zr, H
f, Mn, Fe, Ni, at least one element selected from the group consisting of Ga and Ge), O and at least one rare earth metal element,
An amorphous inorganic fiber having a viscous flow processability in a temperature range of ° C. 2. The method according to claim 1, wherein A is Al and / or Cr.
Amorphous inorganic fibers as described. 3. The amorphous inorganic fiber further comprises Mg, Ca,
The amorphous inorganic fiber according to claim 1, which contains at least one element selected from the group consisting of Ba and Si. 4. The amorphous inorganic fiber further comprises Ti, Zr,
Hf, Mn, Fe, Ni, Ga, Ge, Mg, Ca, B
The amorphous inorganic fiber according to claim 2, comprising at least one element selected from the group consisting of a and Si. 5. The amorphous inorganic fiber according to claim 1, wherein the amorphous inorganic fiber is produced by bringing a melt of the constituent elements into contact with a rotating roll, cooling the solid solution, and solidifying it in a thin line shape. Amorphous inorganic fibers as described. 6. The rare earth metal element is Gd, La, Sm,
Y, Ce, Pr, Nd, Eu, Dy, Yb, Er, T
6. At least one element selected from the group consisting of b, Ho, Tm and Lu.
The amorphous inorganic fiber according to any one of the above. 7. The rare earth metal element is selected from the group consisting of Gd, La and Sm.
The amorphous inorganic fiber according to claim 6, which is at least one element selected from the group consisting of: