JP2001192791A - Fiber-reinforced metal, composite material using the same, and manufacturing method - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a fiber-reinforced metal for plastic working, including a roll excellent in resistance to wear, seizure and crack at hot working and cold working, and a composite material using the fiber-reinforced metal. SOLUTION: The composite material is manufactured by preparing a lamina formed by using an iron-base alloy powder consisting of Fe, C, Cr, Mo, W, Co and one or more elements among V, Nb, Ti, Ta, Zr and Hf, alternately laminating the above lamina and oxide- or nitride-ceramics long fiber and long fiber yarn, and subjecting the resultant laminated materials to pressure sintering. By optimizing the volume fraction and fiber-to-fiber distance of the ceramic long fiber and specifying the particle size of the powder, an excellent wear-, seizure-, and crack-resisting effect can be provided.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to a composite fiber metal for hot and cold working used in rolls, plugs for seamless rolling, extrusion, forging, cutting, etc., guide shoes, dies, guides, cutting tools and the like. More particularly, the present invention relates to a composite material having excellent wear resistance, seizure resistance, and crack resistance, and a method for producing the same.

[0002]

2. Description of the Related Art As shown in FIGS. 6 (a) and 6 (b), a conventional fiber-reinforced metal or composite material for hot and cold working, particularly a roll material, is made of a steel roll shaft 4 or a roll body. A large number of composite rolls in which high carbon high vanadium cast iron having excellent wear resistance is welded as outer layer 6 around 5 are used as steel material rolls.

[0003] The structure of the outer layer portion of this roll is formed by adding MC carbide such as VC, Mo, Cr, or the like to a base structure of a so-called high-speed steel.
It is called high-sroll because it has a structure in which the composite carbide of W is dispersed. Although this roll has extremely excellent wear resistance, it has a problem in crack resistance, and the life of the roll is almost determined by the progress of the crack. At the same time, improvement in seizure resistance is also desired. In order to extend the roll life, there is a problem how to suppress the progress of cracks without sacrificing wear resistance. Similarly, improvement of wear resistance, improvement of toughness and seizure resistance are desired for plugs, guide shoes, dies and mandrels for hot pressing, dies and guides for forging in seamless rolling.

[0004]

SUMMARY OF THE INVENTION The present invention has been made in view of the above-mentioned problems, and a new fiber reinforcement having an effect of further improving abrasion resistance and seizure resistance and suppressing the progress of cracks. An object of the present invention is to provide a composite material for hot and cold working, including a metal and a roll material.

[0005]

SUMMARY OF THE INVENTION The present invention has been made to achieve the above object, and the gist thereof is as follows. (1) In mass%, C: 0.7 to 3.5%, Cr: 2 to 7
%, One or two of Mo and W are 2% ≦ 2Mo + W
≦ 20%, one or two prepared from an iron-based alloy powder containing 3 to 15% of one or more selected from V, Nb, Ti, Ta, Zr, and Hf and the balance substantially consisting of Fe
A fiber-reinforced metal comprising at least one thin sheet and a plurality of long fiber yarns composed of oxide or nitride ceramic long fiber filaments, which are alternately laminated.

(2) C: 0.7-3.5% by mass%
Cr: 2 to 7%, 2% of one or two of Mo and W
≦ 2Mo + W ≦ 20%, V, Nb, Ti, Ta, Zr,
3 to 15% of one or more selected from Hf, C
o: composed of one or more thin sheets containing 10% or less, the balance being substantially made of iron-based alloy powder composed of Fe, and a plurality of oxide or nitride ceramic filament fibers. A fiber-reinforced metal comprising long fiber yarns alternately laminated.

(3) The iron-based alloy powder has a particle size of 1-2.
The fiber-reinforced metal according to (1) or (2), which has a thickness of 5 μm. (4) The content of the ceramic long fiber filament is 1
The fiber reinforced metal according to any one of (1) to (3), wherein the fiber length is 0 to 90 vol% and the average distance between the ceramic long fiber filaments is 1 to 500 μm.

(5) A composite material for a roll for hot or cold working or a tool, comprising the fiber-reinforced metal according to any one of (1) to (4) in a surface layer portion. (6) In mass%, C: 0.7 to 3.5%, Cr: 2 to 7
%, One or two of Mo and W are 2% ≦ 2Mo + W
≦ 20%, one or two prepared from an iron-based alloy powder containing 3 to 15% of one or more selected from V, Nb, Ti, Ta, Zr, and Hf and the balance substantially consisting of Fe
A method for producing a fiber reinforced metal, comprising alternately laminating at least one thin sheet and long fiber yarns composed of a plurality of oxide or nitride ceramic long fiber filaments, and then sintering under pressure. .

(7) C: 0.7-3.5% by mass%
Cr: 2 to 7%, 2% of one or two of Mo and W
≦ 2Mo + W ≦ 20%, V, Nb, Ti, Ta, Zr,
3 to 15% of one or more selected from Hf, C
o: composed of one or more thin sheets containing 10% or less, the balance being substantially made of iron-based alloy powder composed of Fe, and a plurality of oxide or nitride ceramic filament fibers. Long fiber yarns are alternately laminated,
Then, pressure sintering is carried out.

(8) Melting and cooling the iron-based alloy to crystallize carbides may be pulverized and pulverized, or the molten iron-based alloy may be atomized and pulverized. The method for producing a fiber-reinforced metal according to (6) or (7), wherein an iron-based alloy powder having a diameter of 1 to 25 μm is prepared. (9) After laminating the one or two or more thin sheets and the ceramic long fiber yarn, when performing pressure sintering, perform a pretreatment of heating at 1100 to 1400 ° C. under pressure before main sintering, Then, pressure sintering is performed (6)-
(8) The method for producing a fiber-reinforced metal according to any one of the above (8).

(10) When the iron-based alloy is melted and carbide is crystallized and solidified, and then pulverized into powder, the diameter is 10 to 10.
The method for producing a fiber-reinforced metal according to (8) or (9), wherein a 50 mm grinding ball is used in combination with at least two or more kinds of grinding balls having different diameters. (11) The powder according to any one of (8) to (10), wherein the iron-based alloy is pulverized, wet-milled, and further dry-milled in an inert gas atmosphere to produce a powder. Manufacturing method of fiber reinforced metal.

(12) The fiber-reinforced metal according to any one of (6) to (11) is alternately laminated and stuck to a hot or cold working roll shaft or a tool surface, and then dried and then subjected to a capsule treatment. And producing a pressure-sintered laminated surface layer.

[0013]

BEST MODE FOR CARRYING OUT THE INVENTION According to the present invention, at least the surface layer of the outer layer comprises at least one carbide of W and Mo;
Abrasion resistance and seizure resistance by using a fiber-reinforced metal composed of an iron-based alloy containing a carbide of one or more of V, Nb, Ti, Ta, Zr, and Hf and a ceramic long fiber The fiber-reinforced metal is a base made of an iron-based alloy, and has an aspect ratio (fiber length / fiber diameter) of a bundle of 500 to 1,000 ceramic filament fibers having a length of 1,000 or more. By alternately laminating and infiltrating the iron-based alloy powder between every fiber filament constituting the final yarn, a roll or tool for hot or cold working having a structure in which long fibers are dispersed is used. A composite material is provided. The fiber reinforced metal described above can be achieved for the purpose of the present invention by laminating at least the usable dimensions of the composite material used for a roll material or a tool.

At least one or more carbides of W and Mo and one or two of V, Nb, Ti, Ta, Zr and Hf
In order to obtain a base of an iron-based alloy containing carbides composed of more than one kind, generally, an iron-based alloy containing these elements and carbon is melted, cooled, and the crystallized carbide is pulverized into powder. Alternatively, the powder can be obtained by atomizing a molten metal and pulverizing the powder to obtain a powder. On the other hand, as a method of obtaining a fiber reinforced metal consisting of ceramic long fibers, by filling the iron-based alloy powder into a pre-oriented ceramic long fiber yarn consisting of a plurality of long fiber filaments and sintering under pressure. Although it can be obtained, it becomes very difficult to fill the powder, especially between the filament fibers. In the present invention, FIG.
As shown in (b), after the above-mentioned iron-based alloy powder is made into a slurry, a plurality of ceramic long fiber yarns 2 composed of a plurality of long fiber filaments are formed on a thin sheet 1 formed by a doctor blade method or the like. Are prepared, and a plurality of the composite sheets are laminated and pressure-sintered to obtain a composite sheet. In this case, hot pressing or hot isostatic pressing (hip) may be used as the pressure sintering method.

The types of ceramic long fibers are Al ₂ O ₃ ,
SiO ₂ , ZrO ₂ , mullite (Al ₂ O ₃ + SiO
Any of oxides such as ₂ ) and nitrides such as Si ₃ N ₄ and BN can be used. The filament constituting the ceramic long fiber yarn 2 may have a diameter of 3 μm to 30 μm. When a long fiber yarn is used, the binder used to bundle the fibers may be removed by low-temperature heating or the like before use.

The particle size of the iron-based alloy powder used to form the thin sheet 1 is as follows. When ceramic long fibers are combined in a yarn state, the iron-based alloy powder is interposed between the long fiber filaments constituting the yarn during pressure sintering. It was found that it was necessary to use an iron-based alloy having a particle size of 1 to 25 μm. The reason why the lower limit of the particle diameter of the iron-based alloy powder when the long fiber yarn is used is set to 1 μm is that the smaller the particle diameter is, the easier the powder enters between the long fiber filaments. It is extremely difficult to obtain a powder having a size of 1 μm or less, and the lower limit was set at 1 μm which can be industrially produced. If the particle diameter of the iron-based alloy powder is 25 μm or more, interference occurs between the iron-based alloy powder and the filament, and the strength as a composite material cannot be obtained. After adding an organic solvent and a binder to the powder to form a slurry, a thin sheet may be manufactured by a doctor blade method or the like. It is preferable to use toluene, ethylene glycol or polyethylene glycol as the organic solvent, and to use methyl cellulose, nitrocellulose, acrylate, starch or the like as the binder.

The thin sheet can be obtained as a flexible sheet having a thickness of 50 to 1000 μm by adding a plasticizer or the like to the slurry, and can be wound into a coil. In order to allow the iron-based alloy powder to penetrate between the long fiber filaments in the ceramic long fiber yarn during pressure sintering, a particle size of 25 μm or less is required as described above. If this is not possible, it can be used, but if that is not possible, it is necessary to reduce the particle size with a crusher such as a ball mill or attritor. The present inventors have studied a method of refining an iron-based alloy powder, and when using two or more types of ball diameters rather than performing one type of ball diameter in a crusher such as a ball mill or an attritor. Was found to be finer in a shorter time. Special steel, alumina, SiC, etc. may be used as the ball material for grinding, and it is said that the larger the particle size, the higher the grinding energy. In the case of alloy high-speed steel powder, it is effective to use two or more types of pulverized balls having diameters of 10 to 50 mm and different diameters. If the diameter is less than 10 mm, the pulverizing energy is insufficient, and if it exceeds 50 mm, the particle size can be reduced to a certain level, but it is difficult to pulverize the powder to a final particle size of 25 μm or less.

Further, aiming at shortening the milling time,
After examining the effect of the milling atmosphere, wet milling using ethanol is effective for finer particles when the particle size is large, but when the particle size is small, the surface area of the powder increases and the surface is oxidized. Therefore, it was found that a sufficient sintering reaction could not be obtained during pressure sintering. To prevent this, dry milling in an inert gas atmosphere such as argon is required. However, since dry milling from the beginning takes a long time to achieve fineness, it is effective to perform wet milling at least up to a particle size of about 30 μm and then dry milling in an inert gas atmosphere. .

The present inventors further studied a method of easily injecting an iron-based alloy powder (iron-based alloy high-speed steel powder) between long fiber filaments in a long fiber yarn during sintering. As a result, prior to sintering, a method of performing pretreatment in a temperature range of 1100 to 1400 ° C., that is, employing a sintering pattern of at least two or more stages, allows the iron-based alloy high-speed powder to be easily interposed between the filament fibers. It turned out that it could be penetrated. In this case, the pressure is 10 to 8
The pressure may be about 0 MPa, but the higher the processing temperature, the higher the pressure, while the higher the temperature, the lower the pressure. When the temperature is 1
If the temperature is lower than 100 ° C., the effect is not sufficient, and 1400 ° C.
If it exceeds, the fiber itself is deteriorated and cannot be applied. In addition, processing time within one hour is sufficient. After this pretreatment, the iron-based alloy high-speed steel powder is subjected to pressure sintering in a temperature range of 950 to 1100 ° C.

The long fiber content of the composite structure of the fiber-reinforced metal after pressure sintering is preferably in the range of 10 to 90% by volume. It is desirable that the sintered density after sintering be at least 99% of the theoretical density.
Almost this sintering density can be secured. If it is less than 10%, the improvement in wear resistance and toughness is insufficient, and if it exceeds 90%, a sufficient sintered density cannot be obtained. In addition, the distance between the fiber filaments in the composite structure is 1 to the average value of the distance between the fibers in a certain cross section when observing the microstructure.
500 μm is preferred. The distance between the fiber filaments is particularly problematic when used while being oriented perpendicular to the rolled surface during hot and cold working. If the distance between the fibers is 1 μm or less, the bondability between the fiber and the base high-speed steel is not sufficient. , 500μ
If it exceeds m, the seizure resistance deteriorates, and the effect of the ceramic fiber cannot be sufficiently exhibited.

The ceramic long fiber yarn to be laminated on the thin sheet is shown in FIGS. 1 (a) and 1 (b) and FIGS. 2 (a) and 2 (b).
As illustrated in (c), one or two or more thin sheets are arranged in one direction and fixed with a binder, or alternately overlapped in one direction and a direction at an angle to the direction and fixed with a binder. Alternatively, one or more thin sheets and ceramic long fiber yarns are alternately laminated with the woven yarns fixed with a binder. Also,
The angle of the long fiber yarn at the time of lamination is 1 for one direction.
0-90 degrees is sufficient. In this case, fiber yarns may be alternately laminated on a plurality of thin sheets stacked in accordance with the desired fiber volume ratio.

Particularly, in the case of a composite roll to which fiber-reinforced metal is applied, as shown in FIG.
Flows down to the endless belt 8 and is made into a thin sheet by a doctor blade 9 provided on the endless belt 8,
Next, after drying in a drying furnace 10 covering the endless belt 8, winding and forming into a coil shape while inserting the reinforcing filaments of the plurality of ceramic filament fibers 2 between the thin sheets 1 around the roll shaft 5 is performed. 4 or a composite of the thin sheet 1 and the ceramic long fiber yarn 2 attached around the roll shaft 4 as shown in FIG. In this way, pressure sintering is performed, and finally, capsules can be removed and the surface can be ground by finishing. As shown in FIG. 4, when sticking, the long fibers are oriented perpendicular to the roll surface, the thin sheet is made circular, and the ceramic long fiber yarns are radially oriented thereon and alternately laminated with the thin sheet. To manufacture.

The composition of the iron-based alloy in the thin sheet is
0.7 to 3.5% C, 2 to 7% Cr, Mo, W
Of 2 ≦ 2Mo + W ≦ 20%, V, Nb, Ti, Ta, Z
one or more elements selected from r and Hf
It is preferable to use a composition containing about 15% and the balance substantially consisting of Fe, or a composition further containing 10% or less of Co. In the following description, all the components of the iron-based alloy are mass%.

C is required for carbide formation, and is 0.7%
When the amount is less than the above, the amount of the precipitated carbides is small and the wear resistance is not sufficient. When the amount exceeds 3.5%, the carbides are not uniformly dispersed, so that a problem occurs in terms of toughness and surface roughening resistance. V, Nb,
If the sum of the amounts of one or more elements selected from Ti, Ta, Zr, and Hf is less than 3%, the amount of carbides is small in balance with C, and wear resistance, which is a characteristic of HSS, is reduced. Not enough. On the other hand, if it is 15% or more, a large primary crystal carbide is crystallized and a problem of rough skin occurs. V, N
b, Ti, Ta, Zr, and Hf form MC-based carbides, and these metals are effective in improving the wettability between the iron-based alloy and the ceramic fibers, and are essential elements in the present invention.

If the content of Cr is less than 2%, the hardenability is poor, and 7%
If it exceeds, the amount of Cr-based carbides becomes excessive and the toughness and wear resistance decrease. Mo and W are necessary for obtaining hardenability and high-temperature hardness. Further, the total amount of one or two of them is limited to the range of 2% ≦ 2Mo + W ≦ 20%. 2%
If it is less than 30%, sufficient high-temperature hardness cannot be secured, and if it exceeds 20%, it is not preferable in terms of toughness and resistance to rough skin.

Further, in the present invention, Co may be added for tempering softening resistance and secondary hardening. When Co is added, if it exceeds the upper limit of 10%, hardenability deteriorates. If necessary, 5% or less of Ni may be added. Ni is an element that improves the hardenability, but if it exceeds 5%, retained austenite increases and cracks and roughening during rolling occur, which is not preferable.

After the pressure forming, heat treatment conditions, so as to obtain the hardness and surface roughness required under the use conditions of each tool,
What is necessary is just to select a polishing condition and process. The roll axis in the case of a composite roll in which the present invention is applied only to the surface layer is steel,
Cast steel, forged steel, tough cast iron, etc. can be used. The composite roll of the present invention is a sleeve in which at least the surface layer portion corresponding to the outer layer is a single layer or a multiple layer of the fiber reinforced metal defined in the present invention, and the inner layer is joined by welding, sintering, melting, etc. In addition to the method, it can be joined as a composite roll by shrink fitting, fitting, or the like, and used as a composite roll. In a composite tool other than a roll, the composite material may be applied to at least the surface layer.

[0028]

(Example 1) The powder of the iron-based alloy used in Table 1 was used and the powder of about 150 μm was obtained by the doctor blade method shown in FIG.
A thin sheet having a thickness is prepared, and alumina long fibers having an average fiber diameter of 10 μm are alternately laminated with the thin sheet while being arranged so as to have a volume ratio of about 30%, encapsulated in a capsule, and then subjected to hot isostatic pressing (HIP). ), Pressure sintering was performed at a temperature of 1100 ° C., and the structure and the infiltration state between the long fiber filaments were examined. Table 2 shows the state of carbide crystallization, the state of penetration between fibers,
The sintering density is shown.

[0029]

[Table 1]

[0030]

[Table 2]

As can be seen from Tables 1 and 2, if the average powder particle diameter of the iron-based alloy is 20 μm or less, the space between the fibers is filled, and the sintered density with respect to the theoretical density can be maintained at 99.0% or more. . When the C value is lower than the lower limit of the present invention, carbide is hardly crystallized, which indicates that it is difficult to secure wear resistance equivalent to a high-speed steel material. (Example 2) Powder having an average particle diameter of 10 µm having the same composition as the material of material No. 2 in Table 1 and alumina long fiber having an average fiber filament diameter of 10 µm and Si ₃ N ₄ long fiber having an average fiber diameter of 15 µm were used as ceramic long fibers. A long fiber reinforced metal was prototyped by cutting as appropriate.

The thin sheet was manufactured by the doctor blade method shown in FIG. While variously changing the volume ratio of the thin sheet and the fiber and the average inter-fiber distance, a plurality of long fibers arranged alternately are laminated, and hot-pressed to 105
Pressure sintering was performed at 0 ° C. and 40 MPa. Finally, the hardness was adjusted to 80 to 85 Shore hardness by heat treatment. This sample was embedded in a disk-shaped test piece while changing the fiber direction of the surface, and the wear and seizure were evaluated using a rolling wear tester as shown in FIG.

Abrasion, seizure and crack test conditions (1) Specimen size: outer diameter 80 mm, thickness 10 mm A long fiber reinforced material was embedded in the circumferential width 20 mm of the specimen. (2) Heating piece size: outer diameter 160 mm, thickness 15 mm,
7.5R material S45C for crown wear test, SUS430 for seizure test (3) Wear test conditions: heated piece temperature 900 ° C, slip rate 11
% And a load of 50N were compared by measuring the wear depth before and after the test after 10,000 rotations.

The slip ratio was defined as follows. ｛(Heating piece speed-test piece speed) / test piece speed｝ × 100
(%) (4) Seizure test: The sliding rate at which the seizure occurs (critical slip rate) was compared by increasing the sliding rate at 900 ° C. under heating and a load of 20 N. The higher the value, the better the seizure resistance.

(5) Crack test: The test piece was heated to 600 ° C., then water-cooled, and repeated 2,000 times, and the crack depth was measured with a crack meter. Table 3 shows the specifications of the tested materials, and Table 4 shows the results of the wear, seizure and crack tests. In addition, abrasion resistance, seizure resistance, and crack resistance were simultaneously performed on a cast high-speed steel as a comparative material, and compared with the high-speed steel. That is, abrasion ratio = abrasion depth of test material / abrasion depth of high speed material, seizure resistance = critical slip ratio of test material / critical slip ratio of high speed material, crack length ratio = crack length of test material / high speed Expressed by the crack length of the material.

[0036]

[Table 3]

[0037]

[Table 4]

The material No. 19 has not been tested because it has a low sintered density and does not have sufficient strength. The materials Nos. 9 and 10 cannot sufficiently improve the seizure resistance and cracking resistance as compared with the normal high-speed steel, but the materials Nos. 11 to 18 of the present invention have a significantly improved abrasion resistance of 30% or more. The seizure resistance is about 1.5 to 4 times, and the crack resistance is greatly improved. (Example 3) 100 g of powder having the same composition as the material No. 4 in Table 1 and having an average particle diameter of 75 μm was obtained under the conditions shown in Table 5.
It was pulverized with a ball mill. Also in Table 6 after 50 hours, 1
The powder particle diameters after 00 hours and 150 hours are shown.

By combining two or more kinds of balls having different diameters with a ball diameter of 10 to 50 mm, the time can be greatly reduced as compared with the case of a single diameter. Also,
If the ball diameter is less than 10 mm or more than 50 mm, it is difficult to secure a final powder particle size of 25 μm or less.
The pulverization time was based on the particle size at 100 hours.

[0040]

[Table 5]

[0041]

[Table 6]

[0042]

As described in detail above, the fiber-reinforced metal according to the present invention is excellent in wear resistance, seizure resistance and crack resistance. Application to tool materials and the like becomes possible.

[Brief description of the drawings]

FIG. 1 is a diagram showing, as an example of producing a fiber-reinforced metal according to the present invention, a state in which iron-based alloy thin sheets and ceramic long-fiber yarns are alternately laminated, and FIG. (B) is a figure which shows the state which laminated | stacks two sheets and a ceramic long fiber yarn as a thin sheet | seat plural sheets.

FIG. 2 shows an example in which the direction of a ceramic long fiber yarn is changed when producing a fiber reinforced metal according to the present invention. FIG. 2 (a) shows a case where long fibers are inserted between iron-based alloy thin sheets while intersecting at right angles. Examples (b) and (c) are diagrams showing examples in which the orientation of long fibers between iron-based alloy thin sheets is changed.

FIG. 3 is an example of a case where a composite roll is manufactured by using the fiber-reinforced metal of the present invention. FIG.

FIG. 4 shows a method for producing a composite roll using the fiber-reinforced metal of the present invention, wherein an iron-based alloy thin sheet and a ceramic long fiber yarn or an iron-based alloy thin sheet containing a ceramic long fiber yarn are provided around a roll drum. It is a figure which shows the example which manufactures a composite roll while sticking by a suitable magnitude | size.

FIG. 5 is a diagram showing an outline of equipment of a rolling wear tester.

6 (a) and 6 (b) are views showing a cross-sectional structure of a conventional composite roll.

 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Shuichi Hamazuzu 5-1 Nisone, Kokura Minami-ku, Kitakyushu-shi, Fukuoka Prefecture Machinery Division, Mishima Kosan Co., Ltd. (72) Inventor Yoshihiro Hirata Korimoto, Kagoshima City, Kagoshima Prefecture 1-21-40 Kagoshima University Faculty of Engineering (72) Inventor Shuichi Sueyoshi 1-21-40 Korimoto Kagoshima City Kagoshima Pref. Kagoshima University Faculty of Engineering (72) Inventor Sumihiko Kurita 91 No. 114 (72) Inventor Soichiro Samejima 1-21-40 Gunmoto, Kagoshima City, Kagoshima Prefecture Kagoshima University Faculty of Engineering

Claims (12)

[Claims] 1. A mass% of C: 0.7 to 3.5%, C
r: 2 to 7%, one or two of Mo and W are 2% ≦
2Mo + W ≦ 20%, V, Nb, Ti, Ta, Zr, H
f) contains 3 to 15% of one or more selected from f.
1 made from iron-based alloy powder consisting essentially of Fe
A fiber reinforced metal comprising a plurality of thin sheets and two or more thin sheets and long fiber yarns formed of a plurality of oxide or nitride ceramic long fiber filaments, which are alternately laminated. 2. In mass%, C: 0.7-3.5%, C
r: 2 to 7%, one or two of Mo and W are 2% ≦
2Mo + W ≦ 20%, V, Nb, Ti, Ta, Zr, H
3-15% of one or more selected from f, Co:
One or two or more thin sheets made from an iron-based alloy powder containing 10% or less and the balance substantially consisting of Fe;
A fiber reinforced metal comprising a plurality of long fiber yarns composed of a plurality of oxide or nitride ceramic long fiber filaments alternately laminated. 3. The iron-based alloy powder has a particle size of 1 to 25 μm.
3. The fiber-reinforced metal according to claim 1, wherein m is m. 4. The ceramic filament filament content is 10 to 90 vol%, and the average distance between the ceramic filament filaments is 1 to 500 μm.
The fiber reinforced metal according to any one of claims 1 to 3, wherein m is m. 5. A roll or tool composite for hot and cold working, comprising the fiber reinforced metal according to claim 1 in a surface layer. 6. C: 0.7 to 3.5% by mass, C
r: 2 to 7%, one or two of Mo and W are 2% ≦
2Mo + W ≦ 20%, V, Nb, Ti, Ta, Zr, H
f) contains 3 to 15% of one or more selected from f.
1 made from iron-based alloy powder consisting essentially of Fe
A fiber reinforced metal comprising alternately laminating one or more thin sheets and long fiber yarns composed of a plurality of oxide or nitride ceramic long fiber filaments, and then sintering under pressure. Manufacturing method. 7. C: 0.7 to 3.5% by mass%, C:
r: 2 to 7%, one or two of Mo and W are 2% ≦
2Mo + W ≦ 20%, V, Nb, Ti, Ta, Zr, H
3-15% of one or more selected from f, Co:
One or two or more thin sheets made from an iron-based alloy powder containing 10% or less and the balance substantially consisting of Fe;
A method for producing a fiber reinforced metal, comprising alternately laminating long fiber yarns composed of a plurality of oxide or nitride ceramic long fiber filaments, and then sintering under pressure. 8. A method in which the iron-based alloy is melted and cooled to crystallize carbides and then crushed and powdered, or the molten iron-based alloy is atomized and powdered to obtain a particle size. 8. The method for producing a fiber-reinforced metal according to claim 6, wherein an iron-based alloy powder of 1 to 20 μm is produced. 9. After laminating the one or more thin sheets and the ceramic long-fiber yarn and performing pressure sintering, a pre-treatment of heating at 1100 to 1400 ° C. under pressure before main sintering is performed. 9. The method for producing a fiber reinforced metal according to claim 6, wherein the sintering is performed and then pressure sintering is performed. 10. A method for dissolving the iron-based alloy to crystallize carbides.
After coagulation, when pulverizing by pulverization, the diameter: 10 to 50
The method for producing a fiber-reinforced metal according to claim 8, wherein at least two types of grinding balls having different diameters are used in combination with each other. 11. The powder according to claim 8, wherein the iron-based alloy is pulverized, wet-milled, and further dry-milled in an inert gas atmosphere to produce a powder. Manufacturing method of fiber reinforced metal. 12. The fiber-reinforced metal according to claim 6 is alternately laminated and stuck on a roll shaft for hot and cold working or on the surface of a tool, followed by drying and encapsulation. A method for producing a composite material, comprising forming a laminated surface layer portion subjected to pressure sintering.