EP0077611B1 - Mn based alloy of nonequilibrium austenite phase - Google Patents
Mn based alloy of nonequilibrium austenite phase Download PDFInfo
- Publication number
- EP0077611B1 EP0077611B1 EP19820305101 EP82305101A EP0077611B1 EP 0077611 B1 EP0077611 B1 EP 0077611B1 EP 19820305101 EP19820305101 EP 19820305101 EP 82305101 A EP82305101 A EP 82305101A EP 0077611 B1 EP0077611 B1 EP 0077611B1
- Authority
- EP
- European Patent Office
- 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.)
- Expired
Links
Classifications
-
- 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
Definitions
- This invention relates to a Mn-based alloy of nonequilibrium austenite phase which possesses excellent tensile strength and high ductility.
- Mn-based alloy assumes an A-12 type a-Mn 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.
- a Mn-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 non- equilibrium austenite phase at room temperature is very rich in ductility and workability and capable of being cold worked.
- an Mn-based alloy consisting of 4 to 30 atomic percent of at least one element selected from the group consisting of Al, Ni, and Cr, 1 to 15 atomic percent of C, 30 atomic percent or less of at least one element selected from Co, Mo, W, Ta, Nb, V, Ti and Zr, and the balance of the alloy to make up 100 atomic percent, apart from any incidental ingredients and impurities, being Mn, the alloy having a non-equilibrium austenite phase.
- the Mn-based alloy of a non-equilibrium 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, inexpensive and, therefore, is highly useful in non-magnetic electromagnetic parts, composite materials, textile materials, etc.
- the Mn-based alloy of a non-equilibrium austenite 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 atomic % of at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr, and the balance to make up 100 atomic % being comprised substantially of Mn.
- the Mn-based alloy of this invention 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 solidifed 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 4 atomic %, the alloy produced will have very high brittleness because it can no longer be expected to enjoy the effect described above and further because the alloy suffers precipitation of an a-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 MnX (X denoting Ni, Al, or Cr). Thus, the alloy lacks practicability.
- the elongation of the alloy material is effected by the amounts of AI, Ni and/or Cr to be present. As the amount of these components increases, the elongation of the alloy decreases. The tensile strength is not affected much by the content of AI and is liable to increase with the content of Ni and/or Cr.
- the Mn-based alloy of this invention 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 Mn-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 quenching does not easily manifest its effect. If the concentration exceeds 15 atomic %, the produced alloy is brittle due to the precipitation of a carbide Mn 23 C 6-
- the Mn in the austenite phase which is stable only at elevated temperatures improves the mechanical properties of the alloy such as tensile strength. This improvement is brought about without impeding the conversion of the austenite phase, by quenching, into the nonequilibrium austenite phase which is stable even at room temperature.
- the concentration of the elements exceeds 30 atomic %, the Mn-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.
- Mn e.g., 25 to 95 atomic % of Mn
- the Mn-based alloy of the present invention is highly 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 to wire drawing, 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 proportionally 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 pm, preferably 50 pm or more.
- the reduction ratio of area is represented by the following equation: 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 subjecting 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 these additional elements are only present within a range of which the objects and effects of this invention are not impaired by their presence.
- the particle diameter of microcrystals in the nonequilibrium austenite phase varies with the alloy composition and cooling speed. However, 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 effecting this quenching.
- the single roll method, the double roll method, and the submerged rotary spinning method which are liquid quenching methods are particularly effective.
- 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 10 4 to 10 5 °C/sec., while the piston-anvil method or the splat etching method has a cooling speed in the range of about 10 5 to 10 6 °C/sec.
- the quenching of the molten alloy can be efficiently carried out.
- 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 spinning method is a method for obtaining a thin wire of a circular cross section by placing water 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.
- 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.
- the peripheral speed of the rotary drum is preferably 5 to 30% higher than the speed of the flow of molten alloy extruded through the spinning nozzle.
- the angle formed between the flow of molten metal extruded through the spinning nozzle and the water film formed on the inner wall surface of the rotary drum is preferably 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 AI) 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.
- the Mn-based alloy of this invention is capable of being cold worked continuously.
- this Mn-based alloy can be cold drawn to economically form wires of high tensile strength having diameters in the range of 1 to 200 pm. It is noteworthy that the tensile strength of the Mn-based alloy can be improved to even more than 150 kg/mm 2 . Such strength has not been previously attained using any of the nonferrous materials developed to date.
- the Mn-based alloy of this invention as 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.
- An alloy composed of 85 atomic % of Mn, 10 atomic % of AI, and 5 atomic % of C and prepared in a molten state was extruded, under argon gas pressure of 2.5 kg/mm 2 , 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 pm in thickness.
- the ribbons thus obtained were noted to trend toward gradual loss of 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.
- the ribbons were tested for texture by observation through an optical microscope, an X-ray diffraction meter and transmission electron microscope, they were found to be composed of microcrystals of non- equilibrium austenite phase in the structure of a face centered cubic lattice. The crystals measured about 1 to 5 pm. 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 pm in thickness was tested for tensile strength by an Instrom tension tester over a test distance of 2.0 cm at a strain rate of 4.17 ⁇ 10 -4 /sec.
- the ribbon was found to be a very tough material having tensile strength of 35 kg/mm 2 , yield strength of 15 kg/mm 2 , and elongation of 22%.
- This operation produced a continuous thin wire of a substantially circular cross section having a uniform diameter of 130 ⁇ m.
- This thin wire was found to be a highly tough material having tensile strength of 40 kg/mm 2 , yield strength of 25 kg/mm 2 and elongation 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/mm 2 , a yield strength of 135 kg/mm 2 , and an elongation of 1.1%.
- a very tough continuous thin wire having a circular cross section 130 um in diameter was obtained from an alloy composed of 62 atomic % of Mn, 18 atomic % of Al, 8 atomic % of Cr, 7 atomic % of C, and 5 atomic % of Ta.
- This thin wire was cold drawn, without any process annealing, through a commercially available diamond die to 79% of reduction of area.
- the cold drawn wire was tested for tensile strength under the same conditions, it was found to be a heavy-duty wire having tensile strength of 190 kg/mm 2 , yield strength of 140 kg/mm 2 , and elongation of 0.8 percent.
Description
- This invention relates to a Mn-based alloy of nonequilibrium austenite phase which possesses excellent tensile strength and high ductility.
- Conventional Mn-based alloy assumes an A-12 type a-Mn 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.
- An object of this invention is to provide a Mn-based alloy which is very rich in ductility and workability, capable of 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 result of diligent efforts to meet the objects described above, the present inventors have found that a Mn-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 non- equilibrium austenite phase at room temperature is very rich in ductility and workability and capable of being cold worked.
- According to the present invention there is provided an Mn-based alloy, consisting of 4 to 30 atomic percent of at least one element selected from the group consisting of Al, Ni, and Cr, 1 to 15 atomic percent of C, 30 atomic percent or less of at least one element selected from Co, Mo, W, Ta, Nb, V, Ti and Zr, and the balance of the alloy to make up 100 atomic percent, apart from any incidental ingredients and impurities, being Mn, the alloy having a non-equilibrium austenite phase. The Mn-based alloy of a non-equilibrium 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, inexpensive and, therefore, is highly useful in non-magnetic electromagnetic parts, composite materials, textile materials, etc.
Detailed description of preferred embodiment - The Mn-based alloy of a non-equilibrium austenite 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 atomic % of at least one element selected from the group consisting of Co, Mo, W, Ta, Nb, V, Ti, and Zr, and the balance to make up 100 atomic % being comprised substantially of Mn.
- 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 solidifed 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 4 atomic %, the alloy produced will have very high brittleness because it can no longer be expected to enjoy the effect described above and further because the alloy suffers precipitation of an a-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 MnX (X denoting Ni, Al, or Cr). Thus, the alloy lacks practicability. The elongation of the alloy material is effected by the amounts of AI, Ni and/or Cr to be present. As the amount of these components increases, the elongation of the alloy decreases. The tensile strength is not affected much by the content of AI and is liable to increase with the content of Ni and/or Cr. The Mn-based alloy of this invention 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 Mn-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 quenching does not easily manifest its effect. If the concentration exceeds 15 atomic %, the produced alloy is brittle due to the precipitation of a carbide Mn23C6-
- 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 Mn in the austenite phase which is stable only at elevated temperatures improves the mechanical properties of the alloy such as tensile strength. This improvement is brought about without impeding the conversion of the austenite phase, by quenching, into the nonequilibrium austenite phase which is stable even at room temperature. However, if the concentration of the elements exceeds 30 atomic %, the Mn-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 composition, 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 Co, Mo, W, Ta, Nb, V, Ti and Zr (providing that Co have concentration not exceeding 30 atomic %, Mo 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 highly 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 to wire drawing, 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 proportionally 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 pm, preferably 50 pm or more. The reduction ratio of area is represented by the following equation:
- 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 these additional elements are only present within a range of which the objects and effects of this invention are not impaired by their presence.
- The particle diameter of microcrystals in the nonequilibrium austenite phase varies with the alloy composition and cooling speed. However, 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 effecting this quenching. For example, the single roll method, the double roll method, and the submerged rotary spinning method which are liquid quenching methods are particularly effective. 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 105°C/sec., while the piston-anvil method or the splat etching method has a cooling speed in the range of about 105 to 106°C/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 spinning method is a method for obtaining a thin wire of a circular cross section by placing water 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% higher than the speed of the flow of molten alloy extruded through the spinning nozzle. The angle formed between the flow of molten metal extruded through the spinning nozzle and the water film formed on the inner wall surface of the rotary drum is preferably 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 AI) 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 production of thin wires, for example, this Mn-based alloy can be cold drawn to economically form wires of high tensile strength having diameters in the range of 1 to 200 pm. It is noteworthy that the tensile strength of the Mn-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 this invention as 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 examples. However, the present invention is not limited to the following examples.
- An alloy composed of 85 atomic % of Mn, 10 atomic % of AI, 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 pm in thickness.
- The ribbons thus obtained were noted to trend toward gradual loss of toughness in proportion to growth in thickness. Up to about 500 µm of thickness, however, the ribbons were capable of being bent by 180° and folded fast over themselves without fracture. When the ribbons were tested for texture by observation through an optical microscope, an X-ray diffraction meter and transmission electron microscope, they were found to be composed of microcrystals of non- equilibrium austenite phase in the structure of a face centered cubic lattice. The crystals measured about 1 to 5 pm. 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 pm in thickness was tested for tensile strength by an Instrom tension tester over a test distance of 2.0 cm at a strain rate of 4.17×10-4/sec. The ribbon was found to be a very tough material having tensile strength of 35 kg/mm2, yield strength of 15 kg/mm2, and elongation of 22%.
- An alloy composed of 75 atomic % of Mn, 18 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 µm 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 solidifed, 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 Vw/Vj=1.15).
- This operation produced a continuous thin wire of a substantially circular cross section having a uniform diameter of 130 µm.
- 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 diameter of the crystals was about 3 µm.
- 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 elongation 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/mm2, and an elongation of 1.1%.
- By following the procedure of Example 2, a very tough continuous thin wire having a circular cross section 130 um in diameter was obtained from an alloy composed of 62 atomic % of Mn, 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 transmission electron microscope, it was found to have a nonequilibrium austenite phase of crystals 2 to 3 um 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 tests 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 strength of 190 kg/mm2, yield strength of 140 kg/mm2, and elongation of 0.8 percent.
Claims (7)
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 (3)
Publication Number | Publication Date |
---|---|
EP0077611A2 EP0077611A2 (en) | 1983-04-27 |
EP0077611A3 EP0077611A3 (en) | 1983-05-25 |
EP0077611B1 true EP0077611B1 (en) | 1986-04-02 |
Family
ID=15576103
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP19820305101 Expired EP0077611B1 (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 |
JPS5855548A (en) | 1983-04-01 |
DE3270276D1 (en) | 1986-05-07 |
CA1198610A (en) | 1985-12-31 |
JPH0124854B2 (en) | 1989-05-15 |
EP0077611A3 (en) | 1983-05-25 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0096551B1 (en) | Amorphous iron-based alloy excelling in fatigue property | |
Inoue et al. | Microstructure and mechanical properties of rapidly quenched L1 1 alloys in Ni-Al-X systems | |
EP0066356B1 (en) | Process for the production of fine amorphous metallic wires | |
Inoue et al. | Microstructure and mechanical properties of rapidly quenched L2 0 and L2 0+ L1 2 alloys in Ni-Al-Fe and Ni-Al-Co systems | |
Kim et al. | Increase in mechanical strength of Al–Y–Ni amorphous alloys by dispersion of nanoscale fcc-Al particles | |
Hagiwara et al. | Mechanical properties of Fe-Si-B amorphous wires produced by in-rotating-water spinning method | |
US4478791A (en) | Method for imparting strength and ductility to intermetallic phases | |
EP0147937B1 (en) | Iron-base amorphous alloys having improved fatigue and toughness characteristics | |
US4806179A (en) | Fine amorphous metal wire | |
EP0093487B1 (en) | Nickel-based alloy | |
CA1231559A (en) | Iron-base alloy materials having excellent workability | |
JPH08269647A (en) | Ni-based amorphous metallic filament | |
US4609528A (en) | Tri-nickel aluminide compositions ductile at hot-short temperatures | |
US4415529A (en) | Mn-Based alloy of nonequilibrium austenite phase | |
EP0077611B1 (en) | Mn based alloy of nonequilibrium austenite phase | |
JPS6411704B2 (en) | ||
US4404028A (en) | Nickel base alloys which contain boron and have been processed by rapid solidification process | |
JPH0147540B2 (en) | ||
Inoue et al. | Microstructure and mechanical properties of metastable fcc phase wires in Mn-Al-C system manufactured by in-rotating-water spinning method | |
Inoue et al. | Microstructure and mechanical properties of metastable lath martensite wires in the Fe-Ni-Cr-Al-C system produced by melt spinning in rotating water | |
INOUE et al. | Microstructure and Mechanical Properties of Metastable Austenite Wires in Fe-Mn-Cr-Al-C System Produced by the In-rotating-water Spinning Method | |
JPH051346A (en) | High strength aluminum-base alloy | |
JPH0260747B2 (en) | ||
CA1266389A (en) | Method for imparting strength and ductility to intermetallic phases | |
JPS63303032A (en) | Amorphous alloy |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
PUAL | Search report despatched |
Free format text: ORIGINAL CODE: 0009013 |
|
AK | Designated contracting states |
Designated state(s): DE FR GB |
|
AK | Designated contracting states |
Designated state(s): DE FR GB |
|
17P | Request for examination filed |
Effective date: 19831123 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): DE FR GB |
|
ET | Fr: translation filed | ||
REF | Corresponds to: |
Ref document number: 3270276 Country of ref document: DE Date of ref document: 19860507 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed | ||
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 19930909 Year of fee payment: 12 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 19930920 Year of fee payment: 12 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 19930922 Year of fee payment: 12 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Effective date: 19940928 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 19940928 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Effective date: 19950531 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DE Effective date: 19950601 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST |