CA1198610A - Mn-based alloy of nonequilibrium austenite phase - Google Patents
Mn-based alloy of nonequilibrium austenite phaseInfo
- Publication number
- CA1198610A CA1198610A CA000412373A CA412373A CA1198610A CA 1198610 A CA1198610 A CA 1198610A CA 000412373 A CA000412373 A CA 000412373A CA 412373 A CA412373 A CA 412373A CA 1198610 A CA1198610 A CA 1198610A
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- CA
- Canada
- Prior art keywords
- alloy
- atomic
- based alloy
- austenite phase
- nonequilibrium
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C22/00—Alloys based on manganese
Abstract
ABSTRACT OF THE DISCLOSURE
A Mn-based alloy is disclosed. The alloy is com-prised of 4 to 30 atomic % of at least one element selected from the group consisting of Al, Ni, and Cr; 1 to 15 atomic %
of C, 30 atomic % or less of at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr, and the balance of alloy making up 100 atomic % being comprised substantially of Mn. The alloy has a nonequilibrium austenite phase. The alloy disclosed has high ductility and workability. The alloy is capable of being cold worked and has excellent tensile strength. The Mn-based alloy can be produced at substantially the same cost as any Fe-based alloy.
The disclosed alloy is a nonmagnetic alloy which has been found to be very useful for nonmagnetic electromagnetic parts and composite materials.
A Mn-based alloy is disclosed. The alloy is com-prised of 4 to 30 atomic % of at least one element selected from the group consisting of Al, Ni, and Cr; 1 to 15 atomic %
of C, 30 atomic % or less of at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr, and the balance of alloy making up 100 atomic % being comprised substantially of Mn. The alloy has a nonequilibrium austenite phase. The alloy disclosed has high ductility and workability. The alloy is capable of being cold worked and has excellent tensile strength. The Mn-based alloy can be produced at substantially the same cost as any Fe-based alloy.
The disclosed alloy is a nonmagnetic alloy which has been found to be very useful for nonmagnetic electromagnetic parts and composite materials.
Description
Mn-BASED ALLOY OF NONEQUILIBRIUM AUSTENITE PHASE
~IELD OF THE INVENTION
This invention relates to a Mn-based alloy of nonequilibrium austenite phase which possesses excellent tensile strength and high ductility.
BACKCROUND OF THE INVENTION
Conventional Mn-based alloy assumes an A~12 type ~-~ln structure containing 58 atoms in the unit cell at room temperature. Therefore, the alloy is too brittle to be normally worked or formed. Therefore, an inexpensive Mn-Al powder alloy has been found to have a small amount of utility as a material for a magnet. None of the Mn-based alloys existing today possess any appreciable degree of strength, elongation and high ductility.
SUMMARY OF THE INVE~TION
An object of this inven~ion is to provide a ~In-based alloy which is very rich in ductility and workability, capable o being cold worked, and excellent in mechanical properties including tensile strength. Another object of -this invention is to provide a Mn-based alloy which is useful in a great variety of products such as nonmagnetic electro-magnetic parts, composite materials, and textile materials.
As a resul~ of diligen~ efforts to meet the objects described above, the present inventors have found that a Mn-., - 1 - '~
~.9~
based alloy of a specific composition, when solidified by quenching, retains intact (even at room temperature) an austenite phase which is stable only at elevated temperatures.
The Mn-based alloy having a nonequilibrium austenite phase at room temperature is very rich in ductility and workability and capable of being cold worked.
More specifically, the invention is directed to providing a Mn-based alloy having a nonequilibrium austenite phase. The alloy is produced by solidifying by quenching an alloy comprising ~ to 30 a-tomic % o~ at least one element selected from the group consisting of Al, Ni, and Cr, 1 to 15 atomic % of C, not more than 30 atomic % of at least one elemen~ selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr. Ihe balance of the alloy making up 100 atomic % is comprised substantially of Mn. The ~In based alloy of a nonequilibrium austenite phase provided by this invention is very rich in ductility and workability.
Furthermore, the alloy is capable of being cold worked, excellent in mechanical properties including tensile strength, ~0 inexpensive and, therefore, is highly useful in nonmagnetic electromagnetic parts, composite materials, textile materials, etc.
DETAILED DESCRIPTION OF PREFERRED EMBODIMENT
The ~In-based alloy of a nonequilibrium austenite ~5 phase according to this invention is obtained by quenching and solidifying a molten alloy which comprises 4 to 30 atomic % of at least one element selected from the group consisting of Al, Ni, and Cr, 1 to 15 atomic % of C, not more than 30 atomi.c % of at least one element selected from the group consisting of Co, ~lo, W, Ta, Nb, V, Ti, and Zr, and the balance to make up 100 atomic % being comprised substantially of ~In.
The Mn-based alloy of this invention will now be described. It contains at least one element selected from the group consisting of Al, Ni, and Cr in a concentration of 4 to 30 atomic %. The elements and percentage amounts described above represent the metallic elements and the amounts which are essential for the purpose of enabling a Mn-alloy in a molten state to be solidified by quenching into a tough Mn-based alloy, whereby the austenite phase which is stable only at elevated temperatures is supercooled intact to room temperature. If the atomic % amount of these elements is less than ~ atomic %, the alloy produced will have very high bri.ttleness because it can no longer be expected to enjoy the effect described above and further because the alloy suffers precipitation of an ~-Mn phase.
An alloy which does not contain the indicated atomic % amounts of metals cannot be used to produce continuous ribbons and thin wires of fixed shapes. If the concentration exceeds 30 atomic %, the alloy to be produced is rigid and brittle due to the precipitation of an intermetallic compound ~n~ (X denoting Ni, Al, or Cr). Thus, the alloy lacks practicabîlity. The elongation of the alloy material is effected by the amounts of Al, ~i and/or Cr to be present.
As the amount of these components increases, the elonga-tion of the alloy decreases. The tensile strength is not affected much by the content of Al and is liable to increase with the content of Ni and/or Cr. The Mn-based alloy of this inven-tion further contains C in a concentration in the range of 1 to 15 atomic %. The carbon must be present in this amount to enable the austenite phase to be cooled down intact to room temperature when the molten ~In-based alloy is solidified by quenching. If the concentration is less than 1 atomic %, the alloy obtained produces the nonequilibrium austenite phase at room temperature with difficulty and shows very high brittleness because the quenchin~ does not easily manifest its effect. If the concentration exceeds 15 atomic %, the produced alloy is brittle due to the precipitation of a carbide ~In23C6.
When at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr is contained in a concentration of not more than 30 atomic %, the ~In in the austenite phase which is stable only at elevated tempera-tures improves the mechanical properties of the alloy such as tensile strength. This improvement is brought about - '1 -without impeding the conversion of the austenite phase, by quenching, into the nonequilibrium austenite phase which is stable even at room temperature. I~owever, if ~he concentra-tion of the elements exceeds 30 atomic %, ~he ~ln-based alloy will be too brittle to be useful due to the precipitation of a MnY (Y denoting Co, Mo, W, Ta, Nb, V, Ti, and/or Zr) type compound. Particularly in the aforementioned alloy composi-tion, an alloy composed of 7 to 26 atomic % of at least one element selected from the group consisting of Al, Ni and Cr, 3 to 10 atomic % of C, not more than 30 atomic % of at least one element selected from the group consisting of Cog Mo, W, Ta, Nb, V, Ti and Zr (providing that Co have concen~ration not exceedin~ 30 atomic %, ~lo and/or W have concentration not exceeding 20 atomic % and the at least one element selected from the group consisting of Ta, Nb, V, Ti and Zr have concentration not exceeding 10 atomic %), and the balance to make up 100 atomic % being comprised substantially of Mn (e.g.~ 25 to 95 atomic % of Mn), when converted from its molten state by quenching into a solid state, assumes a highly tough austenite phase.
The Mn-based alloy of the present invention is hi~hly desirable because uniform ribbons or thin wires of a circular cross section can be manufactured from this alloy.
Moreover~ the Mn-based alloy of this composition is capable of being cold rolled or cold drawn. Particularly with respect 36~ ~
to wire drawin~, it should be noted that the workability such as cold drawing of this alloy can be effected to more than 90% of reduction of area. The alloy is advantageous in that the tensile strength at fracture notably increases proportion-ally with respect to increases in the area of reduction.
The alloy has been found to be highly suitable for economic production of nonferrous and nonmagnetic heavy-duty metal fibers having diameters not exceeding about 150 ~m,preferably 50 ~m or more. The reduction ratio of area is represented by the following equation:
D - d x 100 D
wherein D is a diameter of wire before the wire drawing and d is a diameter of the thin wire after repeatedly wire drawing. That is, it shows the reduction ratio of the cross section of thin wire to be reduced in accordance with sub-jecting to the drawing workability.
An alloy of the present invention may include additional elements such as Si~ B, P, Ge, Cu, and Hf in addition to the essential elements of this invention provided in that thesè additional elements are only present within a range in which the objects and effects of this invention are not impaired by their presence.
The particle diameter of microcrystals in the nonequilibrium austenite phase varys with the alloy composi-6~
tion and cooling speed. }~owever, it should be pointed out that it is the successful formation of the austenite phase and not the magnitude of the particle diameter of the crystals which is important.
The alloy of this invention is produced by preparing a molten alloy in the aforementioned composition and quenching this molten alloy. Various methods are available for effect-ing this quenching. For example, the single roll methodf the double roll method, and the submerged rotary spinning method which are liquid quenching methods are particularly eIfective.
Plates of the alloy may be produced by the piston-anvil method, the splat etching method, etc. The aforementioned liquid quenching methods (single roll method, double room method, or submerged rotary spinning method) have a cooling speed in the range of about 104 to 105C/sec., while the piston-anvil method or the splat etching method has a cooling speed in the range of about 105 to 106C/sec. By using some of these quenching methods, therefore, the quenching of the molten alloy can be efficiently carried out. The term "submerged rotary spinning method" refers to a method as disclosed in Japanese Patent Application (OPI) No. 64948/80 (The term "OPI" as used herein refers to a "published unexamined Japanese patent application.). The "submerged rotary spin-nina method is a method for obtaining a thin wire of a circular cross section by placing wa~er in a rotary drum in motion thereby centrifugally forming a film of water on the inner wall surface of the drum and extruding molten alloy through a spinning nozzle into the water film. To produce a continuous thin wire uniformly by this method, the peripheral speed of the rotary drum is preferably equal to or greater than the speed of the flow of molten alloy being thrown out of the spinning nozzle. Particularly, the peripheral speed of the rotary drum is preferably 5 to 30% high than the speed of the flow o~ molten alloy extruded through the spinning nozzle. The angle formed between the flow of molten metal extruded through the spinning no2zle and the water film formed on the inner wall surface of the rotary drum is prefer-ably greater than 20.
The Mn based alloy of this invention has a wider range of equilibrium austenite phase at elevated temperatures than the Fe-based alloy. It, therefore, acquires the non-equilibrium austenite phase at room temperature over a wide range of alloy compositions. At the same time, it enjoys stability because it is capable of keeping the austenite phase from converting into martensite. Particularly, the alloy acquires-a large thick austenite phase as compared with the Fe-X-C (X denoting Cr, Mo, W, or Al) alloy. This fact is profoundly significant from the industrial point of view.
When the Mn-based alloy incorporates Cr, among other elements of the same group, it becomes highly resistant to corrosion.
Therefore, the alloy may be used in nonmagnetic corrosion-proofing materials.
Moreover, the Mn-based alloy of this invention is capable of being cold worked continuously. For the produc-tion of thin wires, for example, this ~In-based alloy can be cold drawn to economically form wires of high tensile strength having diameters in the range of 1 to 200 ~m. It is note-worthy that the tensile strength of the ~In-based alloy can be improved to even more than 150 kg/mm2. Such strength has not been previously attained using any of the nonferrous materials developed to date.
Because the Mn-based alloy of chis invention has the quality and structure described above, it can be readily used in the production of a variety of products including, nonmagnetic high resistance materials, nonmagnetic springs, nonmagnetic switch relays, belts, tires and other rubber reinforcements, plastics, concretes and other similar composite materials, and knit and woven fabrics such as fine mesh filters The present invention will now be described more specifically below with reference to working e~amples.
However, the present invention is not limited to be following examples.
Exa~ple 1 An alloy composed of 85 atomic % of ~In, 10 atomic %
`v-~ ~
of Al, and 5 atomic % of C and prepared in a molten state was extruded, under argon gas pressure of 2.5 kg/mm2, through a spinning nozzle of a varying diameter of 0.1 to 1 mm. The extrusion was made onto the surface of a steel roll having a diameter of 20 cm, rotating at a varying speed of 1000 to 5000 rpm, cooled and solidified to produce ribbons of 10 to 500 ~m in thickness.
The ribbons thus obtained were noted to trend toward gradual loss o-f toughness in proportion to growth in thickness.
Up to about 500 ~m of thickness, however, the ribbons were capable of being bent by 180 and folded fast over themselves without fracture. ~hen the ribbons were tested for texture by observation through an optical microscope, an X-ray diffraction meter and a transmission electron microscope, they were found to be composed of microcrystals of non-equilibrium austeni-te phase in the structure of a face centered cubic lattice. The crystals measured about 1 to 5 ~m. The crystals showed a trend toward gradual growth in particle diameter in proportion to growth in ribbon thickness.
The tough alloy ribbon having a nonequilibrium austenite phase and measuring 200 ~m in thickness was tested for tensile strength by an Instron tension tester over a test distance of 2.0 cm at a strain rate of 4.17 x lO 4/sec.
The ribbon was found to be a very tough material having tensile strength of 35kg/mm2, yield strength of 15 kg/mm2, and ~8~
elongation of 22%.
Example 2 An alloy composed of 75 atomic % of Mn, 1~ atomic % of Al, and 7 atomic % of C was melted. The molten alloy was extruded, under argon gas pressure of 3.0 kg/cm2, through a spinning nozzle 150 ~m in orifice diameter into a cooling water bath 2.5 cm in depth formed centrifugally (350 rpm) within a rotary cylinder 50 cm in diameter, there to be cooled and solidified with the rotating body of cooling water. As the thin wire of alloy of a circular cross section was cooled and solidified, it was continuously wound up on the inner wall of the rotary cylinder. (At this time, the speed of the cooling water (Vw) inside the rotary cylinder and the speed of the flow of molten alloy ~VJ) extruded through the spinning nozzle were adjusted, thus V~/VJ = 1.15.) This operation produced a continuous thin wire of a substantially circular cross section having a uniform dia-meter of 130 ~m.
When this thin wire was tested for texture in the same way as in Example 1, it was found to have a nonequilibrium austenite phase in the structure of a fcc. The particle dia-meter of the crystals was about 3 ~m.
This thin wire was found to be a highly tough material having tensile strength of 40 kg/mm2, yield strength of 25 kg/mm2 and e'ongation of 4%.
This thin wire was cold drawn, without any process annealing, through a commercially available diamond die up to 79% of reduction of area. During the cold drawing, the wire sustained no damage of any sort. Thus, the cold drawing produced a very strong thin wire having a highly uniform tensile strength of 160 kg/mm2, a yield strength of 135 kg/
mm , and an elongation of 1.1~.
Example 3 By following che pTocedure of Example 2, a very tough continuous thin wire having a circular cross section 130 ~m in diameter was obtained from an alloy composed of 62 atomic % of ~ln, 18 atomic % of Al, 8 atomic % of Cr, 7 atomic % of C, and 5 atomic ~ of Ta.
When this thin wire was tested for texture by observation through an X-ray diffraction meter and a trans-mission electron ~icroscope, it was found to have a non-equilibrium austenite phase of crystals 2 to 3 ~m in particle diameter. The thin wire had tensile strength of 50 kg/mm2, yield strength of 30 kg/mm2, and elongation of 3.8%.
These test results indicate that the addition of Cr and Ta enabled the produced alloy to acquire enhanced toughness and improved tensile strength.
This thin wire was cold drawn, without any process annealing, through a commercially available diamond die to 79% of reduction of area. When the cold drawn wire was tested for tensile strength under the same conditions, it was found to be a heavy-duty wire having tensile strengtllof 190 kg/mm2, yield strengthofl40 kg/mm , and elongation of O.S %.
While the invention has been described in detail and with reference to specific embodiments thereof, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope thereof.
~IELD OF THE INVENTION
This invention relates to a Mn-based alloy of nonequilibrium austenite phase which possesses excellent tensile strength and high ductility.
BACKCROUND OF THE INVENTION
Conventional Mn-based alloy assumes an A~12 type ~-~ln structure containing 58 atoms in the unit cell at room temperature. Therefore, the alloy is too brittle to be normally worked or formed. Therefore, an inexpensive Mn-Al powder alloy has been found to have a small amount of utility as a material for a magnet. None of the Mn-based alloys existing today possess any appreciable degree of strength, elongation and high ductility.
SUMMARY OF THE INVE~TION
An object of this inven~ion is to provide a ~In-based alloy which is very rich in ductility and workability, capable o being cold worked, and excellent in mechanical properties including tensile strength. Another object of -this invention is to provide a Mn-based alloy which is useful in a great variety of products such as nonmagnetic electro-magnetic parts, composite materials, and textile materials.
As a resul~ of diligen~ efforts to meet the objects described above, the present inventors have found that a Mn-., - 1 - '~
~.9~
based alloy of a specific composition, when solidified by quenching, retains intact (even at room temperature) an austenite phase which is stable only at elevated temperatures.
The Mn-based alloy having a nonequilibrium austenite phase at room temperature is very rich in ductility and workability and capable of being cold worked.
More specifically, the invention is directed to providing a Mn-based alloy having a nonequilibrium austenite phase. The alloy is produced by solidifying by quenching an alloy comprising ~ to 30 a-tomic % o~ at least one element selected from the group consisting of Al, Ni, and Cr, 1 to 15 atomic % of C, not more than 30 atomic % of at least one elemen~ selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr. Ihe balance of the alloy making up 100 atomic % is comprised substantially of Mn. The ~In based alloy of a nonequilibrium austenite phase provided by this invention is very rich in ductility and workability.
Furthermore, the alloy is capable of being cold worked, excellent in mechanical properties including tensile strength, ~0 inexpensive and, therefore, is highly useful in nonmagnetic electromagnetic parts, composite materials, textile materials, etc.
DETAILED DESCRIPTION OF PREFERRED EMBODIMENT
The ~In-based alloy of a nonequilibrium austenite ~5 phase according to this invention is obtained by quenching and solidifying a molten alloy which comprises 4 to 30 atomic % of at least one element selected from the group consisting of Al, Ni, and Cr, 1 to 15 atomic % of C, not more than 30 atomi.c % of at least one element selected from the group consisting of Co, ~lo, W, Ta, Nb, V, Ti, and Zr, and the balance to make up 100 atomic % being comprised substantially of ~In.
The Mn-based alloy of this invention will now be described. It contains at least one element selected from the group consisting of Al, Ni, and Cr in a concentration of 4 to 30 atomic %. The elements and percentage amounts described above represent the metallic elements and the amounts which are essential for the purpose of enabling a Mn-alloy in a molten state to be solidified by quenching into a tough Mn-based alloy, whereby the austenite phase which is stable only at elevated temperatures is supercooled intact to room temperature. If the atomic % amount of these elements is less than ~ atomic %, the alloy produced will have very high bri.ttleness because it can no longer be expected to enjoy the effect described above and further because the alloy suffers precipitation of an ~-Mn phase.
An alloy which does not contain the indicated atomic % amounts of metals cannot be used to produce continuous ribbons and thin wires of fixed shapes. If the concentration exceeds 30 atomic %, the alloy to be produced is rigid and brittle due to the precipitation of an intermetallic compound ~n~ (X denoting Ni, Al, or Cr). Thus, the alloy lacks practicabîlity. The elongation of the alloy material is effected by the amounts of Al, ~i and/or Cr to be present.
As the amount of these components increases, the elonga-tion of the alloy decreases. The tensile strength is not affected much by the content of Al and is liable to increase with the content of Ni and/or Cr. The Mn-based alloy of this inven-tion further contains C in a concentration in the range of 1 to 15 atomic %. The carbon must be present in this amount to enable the austenite phase to be cooled down intact to room temperature when the molten ~In-based alloy is solidified by quenching. If the concentration is less than 1 atomic %, the alloy obtained produces the nonequilibrium austenite phase at room temperature with difficulty and shows very high brittleness because the quenchin~ does not easily manifest its effect. If the concentration exceeds 15 atomic %, the produced alloy is brittle due to the precipitation of a carbide ~In23C6.
When at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr is contained in a concentration of not more than 30 atomic %, the ~In in the austenite phase which is stable only at elevated tempera-tures improves the mechanical properties of the alloy such as tensile strength. This improvement is brought about - '1 -without impeding the conversion of the austenite phase, by quenching, into the nonequilibrium austenite phase which is stable even at room temperature. I~owever, if ~he concentra-tion of the elements exceeds 30 atomic %, ~he ~ln-based alloy will be too brittle to be useful due to the precipitation of a MnY (Y denoting Co, Mo, W, Ta, Nb, V, Ti, and/or Zr) type compound. Particularly in the aforementioned alloy composi-tion, an alloy composed of 7 to 26 atomic % of at least one element selected from the group consisting of Al, Ni and Cr, 3 to 10 atomic % of C, not more than 30 atomic % of at least one element selected from the group consisting of Cog Mo, W, Ta, Nb, V, Ti and Zr (providing that Co have concen~ration not exceedin~ 30 atomic %, ~lo and/or W have concentration not exceeding 20 atomic % and the at least one element selected from the group consisting of Ta, Nb, V, Ti and Zr have concentration not exceeding 10 atomic %), and the balance to make up 100 atomic % being comprised substantially of Mn (e.g.~ 25 to 95 atomic % of Mn), when converted from its molten state by quenching into a solid state, assumes a highly tough austenite phase.
The Mn-based alloy of the present invention is hi~hly desirable because uniform ribbons or thin wires of a circular cross section can be manufactured from this alloy.
Moreover~ the Mn-based alloy of this composition is capable of being cold rolled or cold drawn. Particularly with respect 36~ ~
to wire drawin~, it should be noted that the workability such as cold drawing of this alloy can be effected to more than 90% of reduction of area. The alloy is advantageous in that the tensile strength at fracture notably increases proportion-ally with respect to increases in the area of reduction.
The alloy has been found to be highly suitable for economic production of nonferrous and nonmagnetic heavy-duty metal fibers having diameters not exceeding about 150 ~m,preferably 50 ~m or more. The reduction ratio of area is represented by the following equation:
D - d x 100 D
wherein D is a diameter of wire before the wire drawing and d is a diameter of the thin wire after repeatedly wire drawing. That is, it shows the reduction ratio of the cross section of thin wire to be reduced in accordance with sub-jecting to the drawing workability.
An alloy of the present invention may include additional elements such as Si~ B, P, Ge, Cu, and Hf in addition to the essential elements of this invention provided in that thesè additional elements are only present within a range in which the objects and effects of this invention are not impaired by their presence.
The particle diameter of microcrystals in the nonequilibrium austenite phase varys with the alloy composi-6~
tion and cooling speed. }~owever, it should be pointed out that it is the successful formation of the austenite phase and not the magnitude of the particle diameter of the crystals which is important.
The alloy of this invention is produced by preparing a molten alloy in the aforementioned composition and quenching this molten alloy. Various methods are available for effect-ing this quenching. For example, the single roll methodf the double roll method, and the submerged rotary spinning method which are liquid quenching methods are particularly eIfective.
Plates of the alloy may be produced by the piston-anvil method, the splat etching method, etc. The aforementioned liquid quenching methods (single roll method, double room method, or submerged rotary spinning method) have a cooling speed in the range of about 104 to 105C/sec., while the piston-anvil method or the splat etching method has a cooling speed in the range of about 105 to 106C/sec. By using some of these quenching methods, therefore, the quenching of the molten alloy can be efficiently carried out. The term "submerged rotary spinning method" refers to a method as disclosed in Japanese Patent Application (OPI) No. 64948/80 (The term "OPI" as used herein refers to a "published unexamined Japanese patent application.). The "submerged rotary spin-nina method is a method for obtaining a thin wire of a circular cross section by placing wa~er in a rotary drum in motion thereby centrifugally forming a film of water on the inner wall surface of the drum and extruding molten alloy through a spinning nozzle into the water film. To produce a continuous thin wire uniformly by this method, the peripheral speed of the rotary drum is preferably equal to or greater than the speed of the flow of molten alloy being thrown out of the spinning nozzle. Particularly, the peripheral speed of the rotary drum is preferably 5 to 30% high than the speed of the flow o~ molten alloy extruded through the spinning nozzle. The angle formed between the flow of molten metal extruded through the spinning no2zle and the water film formed on the inner wall surface of the rotary drum is prefer-ably greater than 20.
The Mn based alloy of this invention has a wider range of equilibrium austenite phase at elevated temperatures than the Fe-based alloy. It, therefore, acquires the non-equilibrium austenite phase at room temperature over a wide range of alloy compositions. At the same time, it enjoys stability because it is capable of keeping the austenite phase from converting into martensite. Particularly, the alloy acquires-a large thick austenite phase as compared with the Fe-X-C (X denoting Cr, Mo, W, or Al) alloy. This fact is profoundly significant from the industrial point of view.
When the Mn-based alloy incorporates Cr, among other elements of the same group, it becomes highly resistant to corrosion.
Therefore, the alloy may be used in nonmagnetic corrosion-proofing materials.
Moreover, the Mn-based alloy of this invention is capable of being cold worked continuously. For the produc-tion of thin wires, for example, this ~In-based alloy can be cold drawn to economically form wires of high tensile strength having diameters in the range of 1 to 200 ~m. It is note-worthy that the tensile strength of the ~In-based alloy can be improved to even more than 150 kg/mm2. Such strength has not been previously attained using any of the nonferrous materials developed to date.
Because the Mn-based alloy of chis invention has the quality and structure described above, it can be readily used in the production of a variety of products including, nonmagnetic high resistance materials, nonmagnetic springs, nonmagnetic switch relays, belts, tires and other rubber reinforcements, plastics, concretes and other similar composite materials, and knit and woven fabrics such as fine mesh filters The present invention will now be described more specifically below with reference to working e~amples.
However, the present invention is not limited to be following examples.
Exa~ple 1 An alloy composed of 85 atomic % of ~In, 10 atomic %
`v-~ ~
of Al, and 5 atomic % of C and prepared in a molten state was extruded, under argon gas pressure of 2.5 kg/mm2, through a spinning nozzle of a varying diameter of 0.1 to 1 mm. The extrusion was made onto the surface of a steel roll having a diameter of 20 cm, rotating at a varying speed of 1000 to 5000 rpm, cooled and solidified to produce ribbons of 10 to 500 ~m in thickness.
The ribbons thus obtained were noted to trend toward gradual loss o-f toughness in proportion to growth in thickness.
Up to about 500 ~m of thickness, however, the ribbons were capable of being bent by 180 and folded fast over themselves without fracture. ~hen the ribbons were tested for texture by observation through an optical microscope, an X-ray diffraction meter and a transmission electron microscope, they were found to be composed of microcrystals of non-equilibrium austeni-te phase in the structure of a face centered cubic lattice. The crystals measured about 1 to 5 ~m. The crystals showed a trend toward gradual growth in particle diameter in proportion to growth in ribbon thickness.
The tough alloy ribbon having a nonequilibrium austenite phase and measuring 200 ~m in thickness was tested for tensile strength by an Instron tension tester over a test distance of 2.0 cm at a strain rate of 4.17 x lO 4/sec.
The ribbon was found to be a very tough material having tensile strength of 35kg/mm2, yield strength of 15 kg/mm2, and ~8~
elongation of 22%.
Example 2 An alloy composed of 75 atomic % of Mn, 1~ atomic % of Al, and 7 atomic % of C was melted. The molten alloy was extruded, under argon gas pressure of 3.0 kg/cm2, through a spinning nozzle 150 ~m in orifice diameter into a cooling water bath 2.5 cm in depth formed centrifugally (350 rpm) within a rotary cylinder 50 cm in diameter, there to be cooled and solidified with the rotating body of cooling water. As the thin wire of alloy of a circular cross section was cooled and solidified, it was continuously wound up on the inner wall of the rotary cylinder. (At this time, the speed of the cooling water (Vw) inside the rotary cylinder and the speed of the flow of molten alloy ~VJ) extruded through the spinning nozzle were adjusted, thus V~/VJ = 1.15.) This operation produced a continuous thin wire of a substantially circular cross section having a uniform dia-meter of 130 ~m.
When this thin wire was tested for texture in the same way as in Example 1, it was found to have a nonequilibrium austenite phase in the structure of a fcc. The particle dia-meter of the crystals was about 3 ~m.
This thin wire was found to be a highly tough material having tensile strength of 40 kg/mm2, yield strength of 25 kg/mm2 and e'ongation of 4%.
This thin wire was cold drawn, without any process annealing, through a commercially available diamond die up to 79% of reduction of area. During the cold drawing, the wire sustained no damage of any sort. Thus, the cold drawing produced a very strong thin wire having a highly uniform tensile strength of 160 kg/mm2, a yield strength of 135 kg/
mm , and an elongation of 1.1~.
Example 3 By following che pTocedure of Example 2, a very tough continuous thin wire having a circular cross section 130 ~m in diameter was obtained from an alloy composed of 62 atomic % of ~ln, 18 atomic % of Al, 8 atomic % of Cr, 7 atomic % of C, and 5 atomic ~ of Ta.
When this thin wire was tested for texture by observation through an X-ray diffraction meter and a trans-mission electron ~icroscope, it was found to have a non-equilibrium austenite phase of crystals 2 to 3 ~m in particle diameter. The thin wire had tensile strength of 50 kg/mm2, yield strength of 30 kg/mm2, and elongation of 3.8%.
These test results indicate that the addition of Cr and Ta enabled the produced alloy to acquire enhanced toughness and improved tensile strength.
This thin wire was cold drawn, without any process annealing, through a commercially available diamond die to 79% of reduction of area. When the cold drawn wire was tested for tensile strength under the same conditions, it was found to be a heavy-duty wire having tensile strengtllof 190 kg/mm2, yield strengthofl40 kg/mm , and elongation of O.S %.
While the invention has been described in detail and with reference to specific embodiments thereof, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope thereof.
Claims (7)
1. An Mn-based alloy, comprising:
4 to 30 atomic % of at least one element selected from the group consisting of Al, Ni, and Cr;
1 to 15 atomic % of C;
30 atomic % or less of at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr; and the balance of the alloy to make up 100 atomic %
being comprised substantially of Mn, the alloy having a non-equilibrium austenite phase.
4 to 30 atomic % of at least one element selected from the group consisting of Al, Ni, and Cr;
1 to 15 atomic % of C;
30 atomic % or less of at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr; and the balance of the alloy to make up 100 atomic %
being comprised substantially of Mn, the alloy having a non-equilibrium austenite phase.
2. An Mn-based alloy as claimed in claim 1, wherein the alloy is comprised of from 25 to 95 atomic % of Mn.
3. An Mn-based alloy as claimed in claim 1, wherein the alloy is comprised of from 7 to 26 atomic % of at least one element selected from the group consisting of Al, Ni and Cr.
4. An Mn-based alloy as claimed in claim 1, wherein the alloy is comprised of from 3 to 10 atomic % of C.
5. An Mn-based alloy as claimed in claim 1, wherein the alloy is comprised of 30 atomic % or less of cobalt.
6. An Mn-based alloy as claimed in claim 5, wherein the alloy is comprised of 20 atomic % or less of at least one element selected from the group consisting of Mo and W.
7. An Mn-based alloy as claimed in Claim 5, wherein the alloy is comprised of 10 atomic % or less of at least one element selected from the group consisting of Ta, Nb, V, Ti and Zr.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15406481A JPS5855548A (en) | 1981-09-29 | 1981-09-29 | Mn-based alloy consisting of unequilibratory austenitic phase |
| JP154064/81 | 1981-09-29 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1198610A true CA1198610A (en) | 1985-12-31 |
Family
ID=15576103
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000412373A Expired CA1198610A (en) | 1981-09-29 | 1982-09-28 | Mn-based alloy of nonequilibrium austenite phase |
Country Status (4)
| Country | Link |
|---|---|
| EP (1) | EP0077611B1 (en) |
| JP (1) | JPS5855548A (en) |
| CA (1) | CA1198610A (en) |
| DE (1) | DE3270276D1 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3647885B2 (en) * | 1993-05-07 | 2005-05-18 | 日本電信電話株式会社 | Image processing device |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4023991A (en) * | 1973-08-02 | 1977-05-17 | Matsushita Electric Industrial Co., Ltd. | Anisotropic permanent magnet of Mn-Al-C alloy |
| US4116682A (en) * | 1976-12-27 | 1978-09-26 | Polk Donald E | Amorphous metal alloys and products thereof |
-
1981
- 1981-09-29 JP JP15406481A patent/JPS5855548A/en active Granted
-
1982
- 1982-09-28 EP EP19820305101 patent/EP0077611B1/en not_active Expired
- 1982-09-28 DE DE8282305101T patent/DE3270276D1/en not_active Expired
- 1982-09-28 CA CA000412373A patent/CA1198610A/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| EP0077611A2 (en) | 1983-04-27 |
| JPH0124854B2 (en) | 1989-05-15 |
| EP0077611B1 (en) | 1986-04-02 |
| JPS5855548A (en) | 1983-04-01 |
| EP0077611A3 (en) | 1983-05-25 |
| DE3270276D1 (en) | 1986-05-07 |
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