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EP3594376A1 - Alliage en acier austénitique - Google Patents

Alliage en acier austénitique Download PDF

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Publication number
EP3594376A1
EP3594376A1 EP18190883.1A EP18190883A EP3594376A1 EP 3594376 A1 EP3594376 A1 EP 3594376A1 EP 18190883 A EP18190883 A EP 18190883A EP 3594376 A1 EP3594376 A1 EP 3594376A1
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austenitic steel
amount
mpa
steel alloy
austenitic
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EP3594376B1 (fr
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Ming-Huang Chiang
Ting-yi HUANG
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Apogean Metal Co Ltd
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Apogean Metal Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working

Definitions

  • the disclosure relates to an austenitic steel alloy, and more particularly to an austenitic steel alloy for hot work tools.
  • the disclosure also relates to a method for making an austenitic steel using the alloy, and an austenitic steel made by the method.
  • Martensitic steel is a steel material commonly used for making hot work tools due to its superior mechanical properties such as hardness and toughness. However, since the martensitic steel has a relatively low ductility, the hot work tools made therefrom are liable to cracking.
  • AISI H13 steel is an example of the martensitic steel commonly used for making the hot work tools, and includes carbon in an amount of from 0.32 wt% to 0.45 wt%, silicon in an amount of from 0.80 wt% to 1.20 wt%, manganese in an amount of from 0.20 wt% to 0.50 wt%, chromium in an amount of from 4.75 wt% to 5.50 wt%, molybdenum in an amount of from 1.10 wt% to 1.75 wt%, vanadium in an amount of from 0.80 wt% to 1.20 wt%, phosphorus in an amount of not more than 0.03 wt%, sulfur in an amount of not more than 0.03 wt%, and a balance of iron.
  • the AISI H13 steel has a room temperature hardness of from 55 to 58, an elongation at room temperature of from 3% to 5%, an impact toughness of from 5 Joules (J) to 10 J, and a high temperature Rockwell C hardness (HRc) of from 33 to 41. Since the AISI H13 steel having a relatively low elongation is liable to cracking during usage, the room temperature hardness thereof is usually reduced to a range of from 42 to 50 so as to increase the elongation to a range of from 5% to 8%.
  • QRO 90 steel is another example of the martensitic steel commonly used for making the hot work tools, and includes carbon in an amount of 0.38 wt%, silicon in an amount of 0.30 wt%, manganese in an amount of 0.75 wt%, chromium in an amount of 2.60 wt%, molybdenum in an amount of 2.25 wt%, vanadium in an amount of 0.9 wt%, and a balance of iron.
  • the QRO 90 steel has a room temperature hardness of 45, an elongation of about 11 %, an impact toughness of 10 J, and a high temperature Rockwell C hardness (HRc) of from 26 to 41.
  • austenitic Fe-Mn-Al-C steel has been subjected to extensive researches over the last several decades because of its promising application that is potential associated with high mechanical strength and high ductility.
  • Conventional austenitic Fe-Mn-Al-C steel containing carbon in an amount of greater than about 1.2 wt% may be deteriorated in terms of ductility and may be even cracked. Therefore, the amount of carbon in the conventional austenitic Fe-Mn-Al-C steel is usually controlled within a range of from 0.54 wt% to 1.3 wt% and is added with molybdenum (Mo), niobium (Nb), and/or tungsten (W) to enhance the mechanical strength thereof.
  • Mo molybdenum
  • Nb niobium
  • W tungsten
  • ductility (i.e., elongation) of the conventional austenitic Fe-Mn-Al-C steel may be undesirably reduced due to precipitation of coarse carbides on the grain boundaries of the austenitic Fe-Mn-Al-C steel during an aging treatment. Accordingly, the hot work tools made therefrom are liable to cracking.
  • Applicant's U.S. Patent No. 9,528,177 discloses a Fe-Mn-Al-C quarternary alloy which is essentially consisting of Fe, Mn, Al, and C in specific amounts. Specifically, the amount of carbon in the Fe-Mn-Al-C quarternary alloy is controlled within a range of from 1.4 wt% to 2.2 wt%.
  • the Fe-Mn-Al-C quarternary alloy possesses superior ductility and high mechanical strength due to formation of a high density of fine K ' carbides within an austenite matrix by a spinodal decomposition phase transition mechanism during quenching from a solution heat treatment temperature.
  • a first object of the disclosure is to provide an austenitic steel alloy which possesses superior mechanical properties without compromising ductility at room temperature, and which also possesses superior mechanical properties at high temperature.
  • a second object of the disclosure is to provide a method for making an austenitic steel using the austenitic steel alloy.
  • a third object of the disclosure is to provide an austenitic steel made by the method.
  • an austenitic steel alloy which comprises manganese in an amount of from 25 wt% to 31 wt%, aluminum in an amount of from 7 wt% to 10 wt%, carbon in an amount of from 1.2 wt% to 1.6 wt%, molybdenum in an amount of more than 0 wt% and less than 6 wt%, and a balance of iron.
  • an austenitic steel made by the method of the second aspect of the disclosure.
  • the austenitic steel alloy according to the disclosure possesses superior mechanical properties both at room temperature and at high temperature (e.g., at about 500°C) which are achieved by adding molybdenum in an amount of less than 6 wt% into the austenitic steel alloy including manganese, aluminum, carbon, and iron in specific amounts.
  • An austenitic steel alloy according to the disclosure comprises manganese (Mn) in an amount of from 25 wt% to 31 wt%, aluminum (Al) in an amount of from 7 wt% to 10 wt%, carbon (C) in an amount of from 1.2 wt% to 1.6 wt%, molybdenum (Mo) in an amount of more than 0 wt% and less than 6 wt%, and a balance of iron (Fe).
  • Mn manganese
  • Al aluminum
  • C carbon
  • Mo molybdenum
  • Fe iron
  • the austenitic steel alloy according to the disclosure possesses superior mechanical properties and high ductility, and can be used for making general steel plates such as automobile steel plates, mechanical parts such as gears, hard work tools, and the like.
  • Mn is a strong austenite-stabilizing element.
  • An austenite phase is of face-center-cubic (FCC) structure with more dislocation slip systems, and thus possesses better ductility than other crystal structures, such as body-center-cubic (BCC) and hexagonal close packed (HCP) structures. Therefore, in order to obtain a fully austenite structure at room temperature, Mn is in an amount of from 25 wt% to 31 wt% in the austenitic steel alloy according to the disclosure. In certain embodiments, Mn is in an amount of from 26 wt% to 30 wt% . In certain embodiments, Mn is in an amount of from 27 wt% to 29 wt%.
  • Al not only is a strong ferrite-stabilizing element, but also is one of the primary elements for forming (Fe,Mn) 3 AlC x carbides (i.e., carbides).
  • Al is in an amount of from 7 wt% to 10 wt% in the austenitic steel alloy according to the disclosure. In certain embodiments, Al is in an amount of from 8 wt% to 10 wt%. In certain embodiments, Al is in an amount of from 8 wt% to 9 wt%.
  • C is in an amount of from 1.2 wt% to 1.6 wt% in the austenitic steel alloy according to the disclosure, which is relatively high as compared to the amount (i.e., up to 1.0 wt%) of C in the conventional austenitic Fe-Mn-Al-C steel, in which molybdenum (Mo), niobium (Nb), and/or tungsten (W) is added.
  • Mo molybdenum
  • Nb niobium
  • W tungsten
  • C is in an amount of from 1.4 wt% to 1.6 wt%.
  • Mo is a very strong carbide-forming element. Mo is in an amount of more than 0 wt% and less than 6 wt% in the austenitic steel alloy according to the disclosure. In certain embodiments, Mo is in an amount of from 2 wt% to 6 wt%.
  • the austenitic steel alloy according to the disclosure further comprises chromium (Cr).
  • Cr is also a very strong carbide-forming element. Cr is in an amount of less than 6 wt% in the austenitic steel alloy according to the disclosure.
  • the austenitic steel alloy according to the disclosure further comprises cobalt (Co).
  • Co is also a very strong carbide-forming element. Co is in an amount of less than 5 wt% in the austenitic steel alloy according to the disclosure.
  • the amounts of low-melting elements (e.g., Mn and Al) in the austenitic steel alloy according to the disclosure may be slightly different from those of the low-melting elements in the austenitic steel made from the alloy due to the smelting that causes evaporation effect of the low-melting elements. However, the difference is within an acceptable tolerance. Therefore, the properties of the austenitic steel made from the alloy will not be affected.
  • an embodiment of a method for making an austenitic steel according to the disclosure comprises steps of:
  • the hot-worked body has a thickness of less than 25% of that of the cast piece.
  • the temperature for the aging treatment in step e) is from 480°C to 500°C, and the aging treatment is implemented for a period of from 5 hours to 12 hours.
  • the temperature for the aging treatment in step e) is larger than 500 °C and up to 600°C, and the aging treatment is implemented for a period of from 1 hour to 4 hours.
  • the method for making the austenitic steel according to the disclosure is different from the method for making the conventional austenitic Fe-Mn-Al-C steel having a relatively low carbon amount and containing strong carbide-forming elements. Specifically, in the method for making the conventional austenitic Fe-Mn-Al-C steel, a solution heat treatment is required after the hot-working treatment to dissolve the coarse carbides precipitated on the grain boundaries into a matrix phase so as to enhance the ductility of the conventional austenitic Fe-Mn-Al-C steel.
  • the temperature for implementing the hot-working treatment is controlled within a range of from 1100°C to 950°C such that the precipitation of the coarse carbides on the grain boundaries during the hot-working treatment can be avoided. Therefore, an austenitic steel having superior mechanical properties and high ductility can be made without the solution heat treatment, which is required in the method for making the conventional austenitic Fe-Mn-Al-C steel.
  • the aged body can be cooled down naturally to room temperature.
  • the solution heat treatment is not a requisite in the method for making the austenitic steel according to the disclosure, it may be optionally implemented, if desired.
  • the austenitic steel made by the method according to the disclosure has a fully austenitic phase, a yield strength at 25°C of from 1200 MPa to 1400 MPa, a Rockwell C hardness (HRc) at 25°C of from 45 to 55, an ultimate tensile strength at 25°C of from 1200 MPa to 1500 MPa, and an elongation at 25°C of from 20% to 40%.
  • the austenitic steel made by the method according to the disclosure has superior yield strength and ultimate tensile strength at high temperature up to 700°C. Therefore, the austenitic steel made by the method according to the disclosure can be used for making general steel plates such as automobile steel plates, mechanical parts such as gears, hard work tools, and the like.
  • the austenitic steel alloy according to the disclosure comprises carbon in an amount of from 1.42 wt% to 1.5 wt% and molybdenum in an amount of from 3.5 wt% to 5 wt%.
  • the austenitic steel made by the austenitic steel alloy according to the disclosure has an ultimate tensile strength at 25°C of from 1353 MPa to 1386 MPa, a yield strength at 25°C of from 1310 MPa and 1340 MPa, and a HRc at 25°C of from 47 to 47.7.
  • the austenitic steel alloy according to the disclosure comprises carbon in an amount of from 1.42 wt% to 1.45 wt% and molybdenum in an amount of from 3.5 wt% to 4 wt%.
  • the austenitic steel made by the austenitic steel alloy according to the disclosure has an elongation at 25°C of 25%.
  • the austenitic steel alloy according to the disclosure comprises manganese in an amount of from 27.7 wt% to 30 wt% and aluminum in an amount of from 8.2 wt% to 8.5 wt%.
  • the austenitic steel made by the austenitic steel alloy according to the disclosure has an ultimate tensile strength at 25°C of from 1280 MPa to 1386 MPa, a yield strength at 25°C of from 1250 MPa and 1350 MPa, a hardness (HRc) at 25°C of from 46.7 to 47.7, and an elongation at 25°C of from 20% to 32%.
  • the austenitic steel alloy according to the disclosure comprises manganese in an amount of from 27 wt% to 29 wt%, aluminum in an amount of from 8.0 wt% to 8.5 wt%, and molybdenum in an amount of from 3.0 wt% to 6 wt%.
  • the austenitic steel made by the austenitic steel alloy according to the disclosure has an elongation at 25°C of more than 20%, an ultimate tensile strength at 25°C of more than 1280 MPa, a yield strength at 25°C of more than 1230 MPa, an ultimate tensile strength at 300 °C of more than 1000 MPa, and a yield strength at 300 °C of more than 1000 MPa.
  • the austenitic steel alloy according to the disclosure comprises molybdenum in an amount of 3.0 wt%, and further comprises chromium in an amount of 3 wt% or cobalt in an amount of 2 wt%.
  • the austenitic steel made by the austenitic steel alloy according to the disclosure has an ultimate tensile strength at 25°C of from 1280 MPa to 1344 MPa, a yield strength at 25°C of from 1230 MPa and 1300 MPa, a hardness (HRc) at 25°C of from 45 to 46.8, and an elongation at 25°C of from 24% to 37%.
  • the presently available steel for the hot work tools has a density of from 7.8 g/cm 3 to 7.9 g/cm 3 .
  • the austenitic steel made by the method according to the disclosure has a density of from 6.6 g/cm 3 to 6.8 g/cm 3 , which is 14% less than the density of the presently available steel. Therefore, in addition to superior mechanical properties and high ductility, the austenitic steel made by the method according to the disclosure has a lightweight advantage.
  • the conventional Fe-Mn-Al-C alloy having a relatively high amount of carbon of from 1.4 wt% to 2.2 wt% can possess a fully austenitic phase, form a high density of fine carbides (i.e., (Fe,Mn) 3 AlC x carbides) within an austenite matrix, and avoid the precipitation of coarse carbides on the grain boundaries so as to possess superior mechanical strength and high ductility by controlling the hot-working treatment, the solution heat treatment, and the water-quenching treatment.
  • fine carbides i.e., (Fe,Mn) 3 AlC x carbides
  • an austenitic steel according to the disclosure by adding specific amounts of the strong carbide-forming elements (i.e., Mo and optionally Cr and Co) in the austenitic steel alloy and by controlling the temperature for implementing the hot-working treatment within a specific range (i.e., from 1100°C to 950°C), the precipitation of coarse carbides on the grain boundaries during the hot-working treatment can be avoided. Therefore, an austenitic steel having superior mechanical properties and high ductility can be made without the solution heat treatment which is required in the method for making the conventional austenitic Fe-Mn-Al-C steel.
  • the strong carbide-forming elements i.e., Mo and optionally Cr and Co
  • a steel alloy containing 30 wt% of Mn, 85 wt% of Al, 1.45 wt% of C, 6 wt% of Mo, and a balance of Fe was smelted in a high-frequency smelting furnace under an atmosphere to obtain a molten steel alloy, followed by casting the molten steel alloy to obtain a cast piece having a thickness of 2 cm.
  • the cast piece was heated in a furnace at 1100°C, followed by hot-rolling at a temperature of from 1100°C to 950°C to obtain a test piece having a thickness of less than 25% of that of the cast piece.
  • test piece was subjected to an initial water-quenching treatment followed by cooling to room temperature to obtain a water-quenched body.
  • the water-quenched body was polished to remove an oxide layer, followed by an aging treatment at 500°C to obtain an aged body.
  • the aged body was subjected to a further water-quenching treatment followed by cooling to room temperature.
  • Example 1 In each of Examples 2 to 11, the procedure of Example 1 was repeated using the steel alloy shown in Table 1.
  • Example 1 In each of Comparative Examples 1 to 3, the procedure of Example 1 was repeated using the steel alloy shown in Table 1. Table 1: Steel Alloy Fe (wt%) Mn (wt%) Al (wt%) C (wt%) Mo (wt%) Cr (wt%) Co (wt%) Ex. 1 balance 30 8.5 1.45 6 - - Ex. 2 balance 30 8.5 1.45 4 - - Ex. 3 balance 30 8.5 1.50 3.5 - - Ex. 4 balance 27 8.5 1.48 6 - - Ex. 5 balance 27.5 8.3 1.43 5 - - Ex. 6 balance 28 8.2 1.42 3.5 - - Ex. 7 balance 28.5 8.4 1.46 2 - - Ex. 8 balance 30 8.5 1.45 3 3 - Ex.
  • test pieces were subjected a tensile test according to the specification of ASTM E8/E8M using an Instron tensile tester at a strain rate of 10 -3 /sec at a desirable temperature (i.e., 25°C, 300°C, 500°C, or 700°C). For each of the test pieces, a relationship between stress and strain was recorded to obtain a stress-strain curve at the desirable temperature as that shown below.
  • L2 and L3 are parallel to L1.
  • Yield Strength Yield strength is defined as the stress obtained at 0.2% offset strain in the stress-strain curve, as shown by point A in the stress-strain curve.
  • Ultimate Tensile Strength UTS: Ultimate tensile strength is defined as a maximum stress obtained before failure, as shown by point B in the stress-strain curve.
  • Elongation El: Elongation is defined as the strain shown by point C in the stress-strain curve.
  • the test pieces of Examples 1 to 11 have a yield strength at 25°C of from 1230 MPa to 1350 MPa, an ultimate tensile strength at 25°C of from 1280 MPa to 1386 MPa, an elongation at 25° of from 20% to 37%, and a Rockwell C hardness (HRc) of from 45.0 to 47.7. It is demonstrated that the test pieces of Examples 1 to 11 have superior mechanical strength and ductility as compared to the test pieces of Comparative Examples 1 and 2.
  • the austenitic steel alloy of Examples 1 to 11 has superior mechanical strength and ductility at room temperature (i.e., 25°C) and sufficient mechanical strength at high temperature as well, by controlling the Mo amount in the steel alloy within a range of from 2 wt% to 6 wt% as compared to the steel alloy of Comparative Examples 1 to 3 and conventional AISI H13 and QRO 90 alloys. Therefore, when the austenitic steel alloy according to the disclosure is used to make hot work tools, the cracking problem encountered in the prior art can be avoided.
  • the mechanical strength of each of the test pieces of Examples 1 to 11 is not significantly affected by the aging time of from 5 hours to 12 hours. It is demonstrated that the precipitation of coarse carbides on the grain boundaries of the austenitic steel can be avoided by controlling the temperature during the hot-working treatment. Therefore, the time period for the aging treatment of the austenitic steel alloy according to the disclosure can be more flexible, and the problem of significant precipitation of coarse carbides due to the longer aging time can be alleviated or even avoided.
  • the test pieces of Examples 4, 7, and 9 has a yield strength at 300°C of from 970 MPa to 1030 MPa, an ultimate tensile strength at 300°C of from 1022 MPa to 1070 MPa, a yield strength at 500°C of from 650 MPa to 700 MPa, an ultimate tensile strength at 500°C of from 719 MPa to 786 MPa, a yield strength at 700°C of from 410 MPa to 420 MPa, and an ultimate tensile strength at 700°C of from 440 MPa to 449 MPa.
  • the test piece of Comparative Example 3 has good ductility at 25°C, the yield strengths and the ultimate tensile strengths at 25°C, 300°C, and 500°C are relatively low as compared to the test pieces of Examples 4, 7, and 9. It is demonstrated that the austenitic steel made by the austenitic steel alloy according to the disclosure has superior mechanical strength both at room temperature (i.e., 25°C) and at high temperature, and thus can be used for making a hot work tools.
  • the ductility of the austenitic steel made thereby can be improved by adding relatively low amount (s) of the strong carbide-forming element (s) such as molybdenum and/or tungsten.
  • the mechanical strength of the austenitic steel cannot be significantly enhanced.
  • the mechanical strength thereof can be improved by adding relatively high amount(s) of the strong carbide-forming element(s).
  • the ductility thereof cannot be maintained.
  • an austenitic steel possessing superior mechanical strength and high ductility both at room temperature and at high temperature can be made using the austenitic steel alloy via a method of this disclosure that includes a hot-working treatment at a temperature of from 1100°C to 950°C.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
EP18190883.1A 2018-07-11 2018-08-27 Alliage d'acier austénitique pour la formation à chaud Active EP3594376B1 (fr)

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TW107123925A TWI715852B (zh) 2018-07-11 2018-07-11 沃斯田體合金鋼

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JP (1) JP6735798B2 (fr)
KR (1) KR102211466B1 (fr)
CN (1) CN110714167A (fr)
AU (1) AU2018220088B1 (fr)
CA (1) CA3014436C (fr)
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Citations (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1262613B (de) * 1957-07-02 1968-03-07 Langley Alloys Ltd Verwendung einer Stahllegierung als Werkstoff fuer Gegenstaende mit hoher Festigkeit, Verschleissfestigkeit und verhaeltnismaessig geringem spezifischem Gewicht
US4865662A (en) * 1987-04-02 1989-09-12 Ipsco Inc. Aluminum-manganese-iron stainless steel alloy
GB2220674A (en) * 1988-06-29 1990-01-17 Nat Science Council Alloys useful at elevated temperatures
FR2634221A1 (fr) * 1988-07-13 1990-01-19 Nat Science Council Pieces coulees en alliages a base de fe-mn-al-cr-si-c
US4944814A (en) * 1989-03-02 1990-07-31 Ipsco Enterprises, Inc. Aluminum-manganese-iron steel alloy
JPH02228450A (ja) * 1989-03-02 1990-09-11 Tokushu Denkyoku Kk 鋳造用合金
US4975335A (en) * 1988-07-08 1990-12-04 Fancy Steel Corporation Fe-Mn-Al-C based alloy articles and parts and their treatments
WO1991003579A1 (fr) * 1989-08-31 1991-03-21 Ipsco Enterprises Inc. Alliage d'acier a base d'aluminium, de manganese et de fer
US5167733A (en) * 1992-02-06 1992-12-01 Eastern Precision Casting Co., Ltd. Method for manufacturing iron-manganese-aluminum alloy castings
US8313592B2 (en) * 2008-07-28 2012-11-20 Ati Properties, Inc. Thermal mechanical treatment of martensitic stainless steel
US20130081740A1 (en) * 2011-09-29 2013-04-04 National Chiao Tung University Composition design and processing methods of high strength, high ductility, and high corrosion resistance FeMnAlC alloys
US20140007992A1 (en) * 2011-01-11 2014-01-09 Thyssenkrupp Steel Europe Ag Method for Producing a Hot-Rolled Flat Steel Product
US20150075682A1 (en) * 2011-02-15 2015-03-19 Jfe Steel Corporation High tensile strength steel plate having excellent weld heat-affected zone low-temperature toughness and method for producing same
US20170114432A1 (en) * 2015-10-21 2017-04-27 Caterpillar Inc. High manganese steel with enhanced wear and impact characteristics
WO2017203347A1 (fr) * 2016-05-24 2017-11-30 Arcelormittal Tôle d'acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4875933A (en) * 1988-07-08 1989-10-24 Famcy Steel Corporation Melting method for producing low chromium corrosion resistant and high damping capacity Fe-Mn-Al-C based alloys
JPH0699775B2 (ja) * 1991-12-27 1994-12-07 東大精密鋳造股▲フン▼有限公司 鉄−マンガン−アルミニウム合金の精密鋳造方法
JP4235077B2 (ja) 2003-06-05 2009-03-04 新日本製鐵株式会社 自動車用高強度低比重鋼板とその製造方法
JP4179112B2 (ja) * 2003-09-08 2008-11-12 ダイキン工業株式会社 設備機器管理装置、設備機器管理システムおよび設備機器管理方法
JP5317048B2 (ja) * 2008-06-10 2013-10-16 株式会社Ｎｅｏｍａｘマテリアル 抵抗合金の製造方法
DE102011117135A1 (de) * 2010-11-26 2012-05-31 Salzgitter Flachstahl Gmbh Energie speicherndes Behältnis aus Leichtbaustahl
US10626476B2 (en) * 2013-12-26 2020-04-21 Posco High specific strength steel sheet and method for manufacturing same
US20170088910A1 (en) * 2015-09-29 2017-03-30 Exxonmobil Research And Engineering Company Corrosion and cracking resistant high manganese austenitic steels containing passivating elements
KR102077414B1 (ko) * 2015-10-06 2020-02-13 닛테츠 스테인레스 가부시키가이샤 오스테나이트계 스테인리스 강판
CN106244927B (zh) * 2016-09-30 2018-04-03 北京理工大学 一种低密度超高强度钢及其制备方法
KR101836714B1 (ko) * 2016-10-12 2018-03-09 현대자동차주식회사 고망간강

Patent Citations (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1262613B (de) * 1957-07-02 1968-03-07 Langley Alloys Ltd Verwendung einer Stahllegierung als Werkstoff fuer Gegenstaende mit hoher Festigkeit, Verschleissfestigkeit und verhaeltnismaessig geringem spezifischem Gewicht
US4865662A (en) * 1987-04-02 1989-09-12 Ipsco Inc. Aluminum-manganese-iron stainless steel alloy
GB2220674A (en) * 1988-06-29 1990-01-17 Nat Science Council Alloys useful at elevated temperatures
US4975335A (en) * 1988-07-08 1990-12-04 Fancy Steel Corporation Fe-Mn-Al-C based alloy articles and parts and their treatments
FR2634221A1 (fr) * 1988-07-13 1990-01-19 Nat Science Council Pieces coulees en alliages a base de fe-mn-al-cr-si-c
US4944814A (en) * 1989-03-02 1990-07-31 Ipsco Enterprises, Inc. Aluminum-manganese-iron steel alloy
JPH02228450A (ja) * 1989-03-02 1990-09-11 Tokushu Denkyoku Kk 鋳造用合金
WO1991003579A1 (fr) * 1989-08-31 1991-03-21 Ipsco Enterprises Inc. Alliage d'acier a base d'aluminium, de manganese et de fer
US5167733A (en) * 1992-02-06 1992-12-01 Eastern Precision Casting Co., Ltd. Method for manufacturing iron-manganese-aluminum alloy castings
US8313592B2 (en) * 2008-07-28 2012-11-20 Ati Properties, Inc. Thermal mechanical treatment of martensitic stainless steel
US20140007992A1 (en) * 2011-01-11 2014-01-09 Thyssenkrupp Steel Europe Ag Method for Producing a Hot-Rolled Flat Steel Product
US20150075682A1 (en) * 2011-02-15 2015-03-19 Jfe Steel Corporation High tensile strength steel plate having excellent weld heat-affected zone low-temperature toughness and method for producing same
US20130081740A1 (en) * 2011-09-29 2013-04-04 National Chiao Tung University Composition design and processing methods of high strength, high ductility, and high corrosion resistance FeMnAlC alloys
US9528177B2 (en) 2011-09-29 2016-12-27 Apogean Metal Incorporation Composition design and processing methods of high strength, high ductility, and high corrosion resistance FeMnAlC alloys
US20170114432A1 (en) * 2015-10-21 2017-04-27 Caterpillar Inc. High manganese steel with enhanced wear and impact characteristics
WO2017203347A1 (fr) * 2016-05-24 2017-11-30 Arcelormittal Tôle d'acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule

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CA3014436C (fr) 2024-01-09
JP2020007632A (ja) 2020-01-16
CN110714167A (zh) 2020-01-21
TWI715852B (zh) 2021-01-11
AU2018220088B1 (en) 2020-01-02
MX2018016180A (es) 2020-01-13
EP3594376B1 (fr) 2021-01-06
US20200017929A1 (en) 2020-01-16
JP6735798B2 (ja) 2020-08-05
KR102211466B1 (ko) 2021-02-03
TW202006153A (zh) 2020-02-01
CA3014436A1 (fr) 2020-01-11

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