WO2019239206A1 - Alliage d'acier à teneur élevée en manganèse et son procédé de production - Google Patents

Alliage d'acier à teneur élevée en manganèse et son procédé de production Download PDF

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Publication number
WO2019239206A1
WO2019239206A1 PCT/IB2018/057129 IB2018057129W WO2019239206A1 WO 2019239206 A1 WO2019239206 A1 WO 2019239206A1 IB 2018057129 W IB2018057129 W IB 2018057129W WO 2019239206 A1 WO2019239206 A1 WO 2019239206A1
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Prior art keywords
weight
plate
mpa
alloy
temperature
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PCT/IB2018/057129
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English (en)
Inventor
Mohsen ASKARI PAYKANI
Hamid Reza SHAHVERDI
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Askari Paykani Mohsen
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Publication of WO2019239206A1 publication Critical patent/WO2019239206A1/fr

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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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

Definitions

  • Alloy steels are used in a variety of applications, such as motor vehicles, ships, roads, railways, appliances, buildings, etc.
  • Production of alloy steels having reduced weight, superior mechanical properties (e.g., tensile strength, yield strength, ductility, etc.), lower material costs, etc. is a challenge but is imperative for improving many of the applications.
  • developing advanced alloy steels with superior mechanical properties may allow for using a reduced amount of alloy steel while maintaining sufficient strength.
  • a weight of a motor-vehicle employing the advanced alloy steels may be less than a second motor-vehicle employing less-advanced alloy steels.
  • an alloy steel may comprise 2 to 4 weight % chromium (Cr).
  • the alloy steel may comprise 12 to 16 weight % manganese (Mn).
  • the alloy steel may comprise at most 4 weight % silicone (Si).
  • the alloy steel may comprise 1 to 3 weight % aluminum (Al).
  • the alloy steel may comprise at most 0.3 weight % carbon (C).
  • the alloy steel may comprise iron (Fe).
  • a method for producing an alloy steel is provided.
  • An alloy mixture may be melted to produce a melted alloy mixture (e.g., a liquid state of the alloy mixture).
  • the melted alloy mixture may be formed into a product.
  • the product may be heated to produce a thermally homogenized product.
  • the thermally homogenized product may be hot rolled into a plate with a first thickness.
  • the plate may be warm rolled at a warm rolling temperature until the plate has a second thickness.
  • the warm rolling temperature may be configured such that a crystal structure of the plate has 30 to 70 volume % austenite.
  • a method for producing an alloy steel is provided.
  • An alloy mixture may be melted to produce a melted alloy mixture.
  • the alloy mixture may comprise 2 to 4 weight % chromium (Cr).
  • the alloy mixture may comprise 12 to 16 weight % manganese (Mn).
  • the alloy mixture may comprise at most 4 weight % silicone (Si).
  • the alloy mixture may comprise 1 to 3 weight % aluminum (Al).
  • the alloy mixture may comprise at most 0.3 weight % carbon (C).
  • the alloy mixture may comprise iron (Fe).
  • the melted alloy mixture may be formed into a product.
  • the product may be heated to produce a thermally homogenized product.
  • the thermally homogenized product may be hot rolled into a plate with a first thickness.
  • the plate may be warm rolled at a warm rolling temperature until the plate has a second thickness.
  • the warm rolling temperature may be configured such that a crystal structure of the plate has 30 to 70 volume % austenite.
  • FIG. 1 is an illustration of a table of a plurality of alloy steels and a plurality of chemical compositions corresponding to the plurality of alloy steels.
  • FIG. 2 is an illustration of an exemplary method for producing an alloy steel.
  • FIG. 3A is an illustration of an exemplary process for producing an alloy steel, where an alloy mixture is melted to produce a melted alloy mixture.
  • FIG. 3B is an illustration of an exemplary process for producing an alloy steel, where a melted alloy mixture is formed into a product.
  • FIG. 3C is an illustration of an exemplary process for producing an alloy steel, where a product is heated to produce a thermally homogenized product.
  • FIG. 3D is an illustration of an exemplary process for producing an alloy steel, where a thermally homogenized product is hot rolled to produce a plate with a first thickness.
  • FIG. 3E is an illustration of an exemplary process for producing an alloy steel, where a plate is heated using a furnace.
  • FIG. 3F is an illustration of an exemplary process for producing an alloy steel, where a plate is warm rolled at a warm rolling temperature until the plate has a second thickness.
  • FIG. 3G is an illustration of an exemplary process for producing an alloy steel, where a plate is heat treated using a furnace.
  • FIG. 4 is an illustration of a table of a plurality of heat treatment processes, a plurality of heat treatment temperatures corresponding to the plurality of heat treatment processes and a plurality of durations of time corresponding to the plurality of heat treatment processes.
  • FIG. 5 is an illustration of a table of a plurality of density measurements corresponding to a plurality of alloy steels.
  • FIG. 6A is an illustration of a first part of a table of mechanical properties corresponding to a plurality of alloy steels.
  • FIG. 6B is an illustration of a second part of a table of mechanical properties corresponding to a plurality of alloy steels.
  • FIG. 6C is an illustration of a third part of a table of mechanical properties corresponding to a plurality of alloy steels.
  • FIG. 6D is an illustration of a fourth part of a table of mechanical properties corresponding to a plurality of alloy steels.
  • FIG. 7A is an illustration of a table of mechanical properties corresponding to a set of alloy steels.
  • FIG. 7B is an illustration of a stress-strain diagram corresponding to an Alloy 13.
  • FIG. 7C is an illustration of a stress-strain diagram corresponding to an Alloy 19.
  • FIG. 7D is an illustration of a stress-strain diagram corresponding to an Alloy 23.
  • FIG. 8 is an illustration of a table of mechanical properties corresponding to an Alloy
  • the present disclosure provides steel compositions.
  • one or more of the steel compositions of the present disclosure provide improvements to one or more of the following properties: yield stress, ultimate tensile strength, total elongation, etc.
  • FIG. 1 presents a table 100 of a plurality of alloy steels and a plurality of chemical compositions corresponding to the plurality of alloy steels.
  • the plurality of chemical compositions may comprise weight percentages corresponding to elements comprised within the plurality of alloy steels. In some examples, weight percentages are based upon total weights of each alloy steel of the plurality of alloy steels.
  • an alloy 1 e.g., corresponding to an alloy steel
  • Each weight % value of a plurality of weight percentage values of the table 100 may correspond to a range of weight percentage values.
  • each range of weight percentage values may range from a lower limit to an upper limit.
  • the lower limit may be one of: about 20 weight % less than a corresponding weight % value, preferably about 5 weight % less than the corresponding weight % value, more preferably about 0.5 weight % less than the corresponding weight % value, even more preferably about 0.1 weight % less than the corresponding weight % value, or especially preferred about 0.05 weight % less than the corresponding weight % value.
  • the upper limit may be one of: about 20 weight % greater than the corresponding weight % value, preferably about 5 weight % greater than the corresponding weight % value, more preferably about 0.5 weight % greater than the corresponding weight % value, even more preferably about 0.1 weight % greater than the corresponding weight % value, or especially preferred about 0.05 weight % greater than the corresponding weight % value.
  • the chromium of the alloy 1 may be present at a percentage within a first range (e.g., wherein the first range is one of: about 0 to 36.8 weight %, preferably about 11.8 to 21.8 weight %, more preferably about 16.3 to 17.3 weight %, even more preferably about 16.7 to 16.9 weight %, or especially preferred about 16.75 to 16.85 weight %), the nickel of the alloy 1 may be present at a percentage within a second range (e.g., wherein the second range is one of: about 0 to 33.1 weight %, preferably about 8.1 to 18.1 weight %, more preferably about 12.6 to 13.6 weight %, even more preferably about 13.0 to 13.2 weight %, or especially preferred about 13.05 to 13.15 weight %), etc.
  • a first range e.g., wherein the first range is one of: about 0 to 36.8 weight %, preferably about 11.8 to 21.8 weight %, more preferably about 16.3 to 17.3 weight %, even
  • an alloy 13 of the table 100 may be provided comprising chromium, manganese, silicone, aluminum and/or carbon.
  • iron (Fe) may constitute the substantial balance of the alloy 13.
  • a combination of iron and/or one or more (e.g., other) elements may constitute a substantial balance of the alloy 13.
  • the chromium of the alloy 13 may be present at about 3.0 weight %. Alternatively and/or additionally, the chromium of the alloy 13 may be present at a percentage within a third range (e.g., wherein the third range is one of: about 0 to 23 weight %, preferably about 0 to 8 weight %, more preferably about 2.5 to 3.5 weight %, even more preferably about 2.9 to 3.1 weight %, or especially preferred about 2.95 to 3.05 weight %).
  • the manganese of the alloy 13 may be present at about 14.0 weight %.
  • the manganese of the alloy 13 may be present at a percentage within a fourth range (e.g., wherein the fourth range is one of: about 0 to 34 weight %, preferably about 9 to 19 weight %, more preferably about 13.5 to 14.5 weight %, even more preferably about 13.9 to 14.1 weight %, or especially preferred about 13.95 to 14.05 weight %).
  • the silicone of the alloy 13 may be present at about 1.0 weight %.
  • the silicone of the alloy 13 may be present at a percentage within a fifth range (e.g., wherein the fifth range is one of: about 0 to 21 weight %, preferably about 0 to 6 weight %, more preferably about 0.5 to 1.5 weight %, even more preferably about 0.9 to 1.1 weight %, or especially preferred about 0.95 to 1.05 weight %).
  • the aluminum of the alloy 13 may be present at 2.0 weight %.
  • the aluminum of the alloy 13 may be present at a percentage within a sixth range (e.g., wherein the sixth range is one of: about 0 to 22 weight %, preferably about 0 to 7 weight %, more preferably about 1.5 to 2.5 weight %, even more preferably about 1.9 to 2.1 weight %, or especially preferred about 1.95 to 2.05 weight %).
  • the carbon of the alloy 13 may be present at about 0.1 weight %.
  • the carbon of the alloy 13 may be present at a percentage within a seventh range (e.g., wherein the seventh range is one of: about 0 to 10 weight %, preferably about 0 to 5 weight %, more preferably about 0 to 0.6 weight %, even more preferably about 0 to 0.2 weight %, or especially preferred about 0.05 to 0.15 weight %).
  • the seventh range is one of: about 0 to 10 weight %, preferably about 0 to 5 weight %, more preferably about 0 to 0.6 weight %, even more preferably about 0 to 0.2 weight %, or especially preferred about 0.05 to 0.15 weight %).
  • an alloy 19 of the table 100 may be provided comprising chromium, manganese, silicone, copper (Cu), aluminum and/or carbon.
  • iron may constitute the substantial balance of the alloy 19.
  • a combination of iron and/or one or more (e.g., other) elements may constitute a substantial balance of the alloy 19.
  • the copper of the alloy 19 may be present at about 2.0 weight %. Alternatively and/or additionally, the copper of the alloy 19 may be present at a percentage within an eight range (e.g., wherein the eighth range is one of: about 0 to 22 weight %, preferably about 0 to 7 weight %, more preferably about 1.5 to 2.5 weight %, even more preferably about 1.9 to 2.1 weight %, or especially preferred about 1.95 to 2.05 weight %).
  • the chromium of the alloy 19 may be present at about 3.0 weight %. Alternatively and/or additionally, the chromium of the alloy 19 may be present at a percentage within the third range.
  • the manganese of the alloy 19 may be present at about 14.0 weight %.
  • the manganese of the alloy 19 may be present at a percentage within the fourth range.
  • the silicone of the alloy 19 may be present at about 1.0 weight %.
  • the silicone of the alloy 19 may be present at a percentage within the fifth range.
  • the aluminum of the alloy 19 may be present at about 2.0 weight %.
  • the aluminum of the alloy 19 may be present at a percentage within the sixth range.
  • the carbon of the alloy 19 may be present at about 0.1 weight %.
  • the carbon of the alloy 19 may be present at a percentage within the seventh range.
  • an alloy 23 of the table 100 may be provided comprising chromium, nickel, manganese, silicone, copper, aluminum and/or carbon.
  • iron may constitute the substantial balance of the alloy 23.
  • a combination of iron and/or one or more (e.g., other) elements may constitute a substantial balance of the alloy 23.
  • the chromium of the alloy 23 may be present at about 2.5 weight %. Alternatively and/or additionally, the chromium of the alloy 23 may be present at a percentage within a ninth range (e.g., wherein the ninth range is one of: about 0 to 22.5 weight %, preferably about 0 to 7.5 weight %, more preferably about 2 to 3 weight %, even more preferably about 2.4 to 2.6 weight %, or especially preferred about 2.45 to 2.55 weight %).
  • the nickel of the alloy 23 may be present at about 1.3 weight %.
  • the nickel of the alloy 23 may be present at a percentage within a tenth range (e.g., wherein the tenth range is one of: about 0 to 21.3 weight %, preferably about 0 to 6.3 weight %, more preferably about 0.8 to 1.8 weight %, even more preferably about 1.2 to 1.4 weight %, or especially preferred about 1.25 to 1.35 weight %).
  • the manganese of the alloy 23 may be present at about 14.0 weight %.
  • the manganese of the alloy 23 may be present at a percentage within the fourth range.
  • the silicone of the alloy 23 may be present at about 2.7 weight %.
  • the silicone of the alloy 23 may be present at a percentage within an eleventh range (e.g., wherein the ninth range is one of: about 0 to 22.7 weight %, preferably about 0 to 7.7 weight %, more preferably about 2.2 to 3.2 weight %, even more preferably about 2.6 to 2.8 weight %, or especially preferred about 2.65 to 2.75 weight %).
  • the copper of the alloy 23 may be present at about 0.8 weight %.
  • the copper of the alloy 23 may be present at a percentage within a twelfth range (e.g., wherein the twelfth range is one of: about 0 to 20.8 weight %, preferably about 0 to 5.8 weight %, more preferably about 0.3 to 1.3 weight %, even more preferably about 0.7 to 0.9 weight %, or especially preferred about 0.75 to 0.85 weight %).
  • the aluminum of the alloy 23 may be present at about 2.0 weight %.
  • the aluminum of the alloy 23 may be present at a percentage within the sixth range.
  • the carbon of the alloy 23 may be present at about 0.2 weight %.
  • the carbon of the alloy 23 may be present at a percentage within a thirteenth range (e.g., wherein the thirteenth range is one of: about 0 to 10 weight %, preferably about 0 to 5.2 weight %, more preferably about 0 to 0.7 weight %, even more preferably about 0.1 to 0.3 weight %, or especially preferred about 0.15 to 0.25 weight %).
  • the thirteenth range is one of: about 0 to 10 weight %, preferably about 0 to 5.2 weight %, more preferably about 0 to 0.7 weight %, even more preferably about 0.1 to 0.3 weight %, or especially preferred about 0.15 to 0.25 weight %).
  • FIG. 2 illustrates a method 200 for producing an alloy steel.
  • the method 200 may be distinguished as (e.g., an example of) a warm rolling process.
  • the warm rolling process may comprise one or more hot rolling steps and/or one or more warm rolling steps.
  • the warm rolling process may (e.g., also) comprise one or more cold rolling steps.
  • the warm rolling process may not comprise (any) cold rolling steps.
  • an alloy mixture may be melted to produce a melted alloy mixture.
  • the alloy mixture having a composition corresponding to an alloy of the plurality of alloys in table 100, may be melted using a (e.g., vacuum induction melting) furnace.
  • an argon (Ar) atmosphere e.g., and/or a different type of atmosphere
  • the alloy mixture may be melted within the argon atmosphere. It may be appreciated that melting the alloy mixture within the argon atmosphere may reduce (e.g., and/or eliminate) oxidation of the alloy mixture.
  • the alloy mixture may be melted in an alumina crucible.
  • the melted alloy mixture may be formed into a product.
  • the melted alloy mixture may be cast in a water-cooled copper mold to form the product.
  • the product may comprise one or more slabs, one or more ingots and/or one or more billets.
  • the melted alloy mixture may be cooled to produce a solid alloy mixture.
  • the solid alloy mixture may be re melted to form a second melted alloy mixture.
  • the re-melted alloy mixture may be cast in the water-cooled copper mold to form the product.
  • the product may be heated to produce a thermally homogenized product.
  • the product may be heated at a first temperature for a first duration of time.
  • the product may be heated to the first temperature.
  • a temperature of the product may be maintained at the first temperature (e.g., and/or a second temperature) for the first duration of time.
  • the first temperature e.g., and/or the second temperature
  • the first temperature may be configured such that the product is thermally homogenized (e.g., thermally soaked).
  • the thermally homogenized product may have a uniform temperature (e.g., throughout the thermally homogenized product).
  • the first temperature may be about 1100° C.
  • the first temperature may be within a first temperature range (e.g., wherein the first temperature range is one of: about 800° C to 1200° C, preferably about 1000° C to 1200° C, more preferably about 1050° C to 1150° C, even more preferably about 1075° C to 1125° C, or especially preferred about 1090° C to 1110° C).
  • the first duration of time may be about 4 hours.
  • the first duration of time may be within a first time duration range (e.g., wherein the first time duration range is one of: about 2 hours to 6 hours, preferably about 2.5 hours to 5.5 hours, more preferably about 3 hours to 5 hours, even more preferably about 3.75 hours to 4.25 hours, or especially preferred about 3.9 hours to 4.1 hours).
  • the first duration of time may be greater than 4 hours.
  • the thermally homogenized product may be hot rolled to produce a plate with a first thickness.
  • the thermally homogenized product may be hot rolled at one or more hot rolling temperatures.
  • the thermally homogenized product may undergo hot rolling wherein the thermally homogenized product may be hot rolled at a hot rolling start temperature at a beginning of the hot rolling (e.g., the thermally homogenized product) and the thermally homogenized product may be hot rolled at a hot rolling finishing temperature at an end of the hot rolling (e.g., the thermally homogenized product).
  • the hot rolling start temperature may be about 1100° C.
  • the hot rolling start temperature may be within a second temperature range (e.g., wherein the second temperature range is one of: about 800° C to 1200° C, preferably about 1000° C to 1200° C, more preferably about 1050° C to 1150° C, even more preferably about 1090° C to 1110° C, or especially preferred about 1095° C to 1105° C, etc.).
  • the hot rolling start temperature may be greater than 1100° C.
  • the hot rolling finishing temperature may be about 900° C.
  • the hot rolling finishing temperature may be within a third temperature range (e.g., wherein the third temperature range is one of: about 600° C to 1200° C, preferably about 800° C to 1000° C, more preferably about 850° C to 950° C, even more preferably about 890° C to 910° C, or especially preferred about 895° C to 905° C).
  • the hot rolling finishing temperature may be greater than 900° C.
  • the first thickness may be about 3 millimeters (mm).
  • the first thickness may be one of: about 1 mm, about 1.5 mm, about 2 mm, about 2.5 mm, about 3.5 mm, about 4 mm, about 4.5 mm, about 5 mm, about 6 mm, about 7 mm, about 8 mm, about 9 mm, about 10 mm, about 11 mm, about 12 mm, about 13 mm, about 14 mm or about 15 mm.
  • the first thickness may be within a first thickness range (e.g., wherein the first thickness range is one of: about 1 mm to 100 mm, preferably about 1 mm to 20 mm, more preferably about 1 mm to 10 mm, even more preferably about 1 mm to 5 mm, or especially preferred about 2 mm to 4 mm).
  • first thickness range is one of: about 1 mm to 100 mm, preferably about 1 mm to 20 mm, more preferably about 1 mm to 10 mm, even more preferably about 1 mm to 5 mm, or especially preferred about 2 mm to 4 mm).
  • a first thickness reduction of a thickness of the thermally homogenized product to the first thickness may be about 80%.
  • the thickness of the thermally homogenized product may be about 15 mm and the first thickness may be about 3 mm.
  • the first thickness reduction of the thickness of the thermally homogenized product to the first thickness may be one of: about 50%, about 55%, about 60%, about 65%, about 70%, about 75%, about 85%, about 90% or about 95%.
  • the first thickness reduction of the thickness of the thermally homogenized product to the first thickness may be within a first reduction range (e.g., wherein the first reduction range is one of: about 30% to 99%, preferably about 50% to 95%, more preferably about 60% to 95%, even more preferably about 70% to 90%, or especially preferred about 75% to 85%).
  • the first reduction range is one of: about 30% to 99%, preferably about 50% to 95%, more preferably about 60% to 95%, even more preferably about 70% to 90%, or especially preferred about 75% to 85%).
  • the plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate reaches a fourth temperature. Responsive to the plate reaching the fourth temperature, a plate temperature of the plate may be maintained at a fifth temperature (e.g., and/or the fourth temperature) for a second duration of time.
  • a fifth temperature e.g., and/or the fourth temperature
  • the fourth temperature may be about 700° C.
  • the fourth temperature may be within a fourth temperature range (e.g., wherein the fourth temperature range is one of: about 400° C to 1000° C, preferably about 600° C to 800° C, more preferably about 650° C to 750° C, even more preferably about 675° C to 725° C, or especially preferred about 690° C to 710° C).
  • the fourth temperature may be greater than 700° C.
  • the fifth temperature may be about 700° C.
  • the fifth temperature may be within a fifth temperature range (e.g., wherein the fifth temperature range is one of: about 400° C to 1000° C, preferably about 600° C to 800° C, more preferably about 650° C to 750° C, even more preferably about 675° C to 725° C, or especially preferred about 690° C to 710° C).
  • the fifth temperature may be greater than 700° C.
  • the second duration of time may be about 1 hour.
  • the second duration of time may be within a second time duration range (e.g., wherein the second time duration range is one of: about 0.1 hours to 5 hours, preferably about 0.1 hours to 3 hours, more preferably about 0.5 hours to 1.5 hours, even more preferably about 0.75 hours to 1.25 hours, or especially preferred about 0.9 hours to 1.1 hours).
  • the second duration of time may be greater than 1 hour.
  • the plate may not be cooled until the plate reaches the fourth temperature and/or the plate temperature of the plate may not be maintained at the fifth temperature.
  • the plate may undergo a coiling process (e.g., in industrial steel making) (e.g., rather than being cooled until the plate reaches the fourth temperature and/or the plate temperature of the plate being maintained at the fifth temperature).
  • the plate Responsive to completion of the maintaining the plate temperature of the plate at the fifth temperature (e.g., and/or the fourth temperature) for the second duration of time and/or responsive to completion of the plate undergoing the coiling process, the plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate reaches a sixth temperature.
  • the plate Responsive to completion of the maintaining the plate temperature of the plate at the fifth temperature (e.g., and/or the fourth temperature) for the second duration of time and/or responsive to completion of the plate undergoing the coiling process, the plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate reaches a sixth temperature.
  • the sixth temperature may be about 450° C.
  • the sixth temperature may be within a sixth temperature range (e.g., wherein the sixth temperature range is one of: about 150° C to 750° C, preferably about 350° C to 550° C, more preferably about 400° C to 500° C, even more preferably about 425° C to 475° C, or especially preferred about 440° C to 460° C).
  • the sixth temperature may be greater than 450° C.
  • the plate may be warm rolled at a warm rolling temperature until the plate has a second thickness.
  • the plate may be warm rolled responsive to the plate reaching the sixth temperature.
  • the second thickness may be about 1 mm.
  • the second thickness may be one of: about 0.5 mm, about 1.5 mm, about 2 mm, about 2.5 mm, about 3.5 mm, about 4 mm, about 4.5 mm, about 5 mm, about 6 mm, about 7 mm, about 8 mm, about 9 mm, about 10 mm, about 11 mm, about 12 mm, about 13 mm, about 14 mm or about 15 mm.
  • the second thickness may be within a second thickness range (e.g., wherein the second thickness range is one of: about 0.1 mm to 100 mm, preferably about 0.1 mm to 20 mm, more preferably about 0.1 mm to 10 mm, even more preferably about 0.1 mm to 5 mm, or especially preferred 0.5 to 2 mm).
  • the second thickness range is one of: about 0.1 mm to 100 mm, preferably about 0.1 mm to 20 mm, more preferably about 0.1 mm to 10 mm, even more preferably about 0.1 mm to 5 mm, or especially preferred 0.5 to 2 mm).
  • a second thickness reduction of the first thickness (e.g., of the plate) to the second thickness (e.g., of the plate) may be about 66.7%.
  • the first thickness may be about 3 mm and the second thickness may be about 1 mm.
  • the second thickness reduction of the first thickness to the second thickness may be one of: about 25%, about 30%, about 35%, about 40%, about 45%, about 50%, about 55%, about 60%, about 65%, about 70%, about 80%, about 85%, about 90% or about 95%.
  • the second thickness reduction of the first thickness to the second thickness may be within a second reduction range (e.g., wherein the second reduction range is one of: about 30% to 95%, preferably about 40% to 80%, more preferably about 50% to 75%, even more preferably about 60% to 70%, or especially preferred about 65% to 70%).
  • the warm rolling temperature may be about 450° C.
  • the warm rolling temperature may be within a seventh temperature range (e.g., wherein the seventh temperature range is one of: about 150° C to 750° C, preferably about 350° C to 550° C, more preferably about 400° C to 500° C, even more preferably about 425° C to 475° C, or especially preferred about 440° C to 460° C).
  • the seventh temperature may be greater than 450° C.
  • the warm rolling temperature may be equal to the sixth temperature.
  • the warm rolling temperature may be approximately equal to the sixth temperature.
  • the warm rolling temperature and/or the sixth temperature may be configured based upon a phase diagram associated with the composition of the alloy mixture.
  • the warm rolling temperature and/or the sixth temperature may be configured such that a crystal structure of the composition of the plate has a first level of austenite (e.g., austenite phase) at one or more times (e.g., while the plate is being warm rolled and/or after the plate is warm rolled).
  • the first level of austenite may be about 50 volume % austenite.
  • the first level of austenite may be one of: about 20 volume % austenite, about 25 volume % austenite, about 30 volume % austenite, about 35 volume % austenite, about 40 volume % austenite, about 45 volume % austenite, about 55 volume % austenite, about 60 volume % austenite, about 65 volume % austenite, about 70 volume % austenite, about 75 volume % austenite, about 80 volume % austenite, about 85 volume % austenite, about 90 volume % austenite, about 95 volume % austenite or about 100 volume % austenite.
  • the first level of austenite may be within a first austenite level range (e.g., wherein the first austenite level range is one of: about 15 to 95 volume % austenite, preferably about 20 to 90 volume % austenite, more preferably about 30 to 70 volume % austenite, even more preferably about 40 to 60 volume % austenite, or especially preferred about 45 to 55 volume % austenite).
  • the plate may be heat treated (e.g., and/or annealed) at a heat treatment temperature for a third duration of time.
  • a furnace used for heat treating the plate may be controlled to an accuracy of 2° C greater than or less than the (e.g., desired) heat treatment temperature, 5° C greater than or less than the heat treatment temperature, or 10° C greater than or less than the heat treatment temperature.
  • the furnace may be a muffle furnace.
  • a rate of heating of the heat treating the plate may be 10° C per minute (e.g., and/or a different rate of heating).
  • the plate may be heat treated while (e.g., positioned) inside of (e.g., and/or on top of, adjacent to, etc.) a cast-iron filings medium.
  • FIG. 4 presents a table 400 of a plurality of heat treatment processes, a plurality of heat treatment temperatures corresponding to the plurality of heat treatment processes and a plurality of durations of time corresponding to the plurality of heat treatment processes.
  • the plate may be heat treated based upon a heat treatment process of the plurality of heat treatment processes of the table 400.
  • a heat treatment process HT 1 may correspond to a first heat treatment temperature of about 200° C and/or a fourth duration of time of about 20 minutes.
  • Each heat treatment temperature of the plurality of heat treatment temperatures of the table 400 may correspond to a range of heat treatment temperatures.
  • each range of heat treatment temperatures may range from a lower limit to an upper limit.
  • the lower limit may be one of: about 100° C less than a corresponding heat treatment temperature, preferably about 60° C less than the corresponding heat treatment temperature, more preferably about 40° C less than the corresponding heat treatment temperature, even more preferably about 10° C less than the corresponding heat treatment temperature, or especially preferred about 5° C less than the corresponding heat treatment temperature.
  • the upper limit may be one of: about 100° C greater than the corresponding heat treatment temperature, preferably about 60° C greater than the corresponding heat treatment temperature, more preferably about 40° C greater than the corresponding heat treatment temperature, even more preferably about 10° C greater than the corresponding heat treatment temperature, or especially preferred about 5° C greater than the corresponding heat treatment temperature.
  • the first heat treatment temperature of the first heat treatment process HT 1 may be within an eighth temperature range (e.g., wherein the eighth temperature range is one of: about 100° C to 300° C, preferably about 140° C to 260° C, more preferably about 160° C to 240° C, even more preferably about 190° C to 210° C, or especially preferred about 195° C to 205° C.
  • the eighth temperature range is one of: about 100° C to 300° C, preferably about 140° C to 260° C, more preferably about 160° C to 240° C, even more preferably about 190° C to 210° C, or especially preferred about 195° C to 205° C.
  • the heat treatment temperature (e.g., for heat treating the plate) may be configured such that the crystal structure of the composition of the plate has a second level of austenite at one or more times (e.g., while the plate is being heat treated and/or after the plate is heat treated).
  • the second level of austenite may be about 20 volume % austenite.
  • the second level of austenite may be one of: about 5 volume % austenite, about 10 volume % austenite, about 15 volume % austenite or about 30 volume % austenite.
  • the second level of austenite may be within a second austenite level range (e.g., wherein the austenite level range is one of: about 5 to 35 volume % austenite, preferably about 10 to 30 volume % austenite, more preferably about 15 to 25 volume % austenite, or even more preferably about 18 to 22 volume % austenite).
  • the heat treatment temperature e.g., for heat treating the plate
  • the crystal structure of the composition of the plate has a third level of austenite at one or more times (e.g., while the plate is being heat treated and/or after the plate is heat treated).
  • the third level of austenite may be equal to the first level of austenite. Alternatively and/or additionally, the third level of austenite may be approximately equal to the first level of austenite. For example, the third level of austenite may be about 50 volume % austenite. Alternatively and/or additionally, the third level of austenite may be one of: about 35 volume % austenite, about 40 volume % austenite, about 45 volume % austenite, about 55 volume % austenite or about 60 volume % austenite.
  • the third level of austenite may be within a third austenite level range (e.g., wherein the austenite level range is one of: about 30 to 70 volume % austenite, preferably about 35 to 65 volume % austenite, more preferably about 40 to 60 volume % austenite, even more preferably about 45 to 55 volume % austenite, or especially preferred about 48 to 52 volume % austenite).
  • the austenite level range is one of: about 30 to 70 volume % austenite, preferably about 35 to 65 volume % austenite, more preferably about 40 to 60 volume % austenite, even more preferably about 45 to 55 volume % austenite, or especially preferred about 48 to 52 volume % austenite).
  • the heat treatment temperature (e.g., for heat treating the plate) may be configured such that the crystal structure of the composition of the plate has a fourth level of austenite at one or more times (e.g., while the plate is being heat treated and/or after the plate is heat treated).
  • the fourth level of austenite may be about 80 volume % austenite.
  • the fourth level of austenite may be one of: about 65 volume % austenite, about 70 volume % austenite, about 75 volume % austenite, about 85 volume % austenite or about 90 volume % austenite.
  • the fourth level of austenite may be within a fourth austenite level range (e.g., wherein the fourth austenite level range is one of: about 65 to 95 volume % austenite, preferably about 70 to 90 volume % austenite, more preferably about 75 to 85 volume % austenite, or even more preferably about 78 to 72 volume % austenite).
  • the heat treatment temperature (e.g., for heat treating the plate) may be configured such that the crystal structure of the composition of the plate has a fifth level of austenite at one or more times (e.g., while the plate is being heat treated and/or after the plate is heat treated).
  • the fifth level of austenite may be about 100 volume % austenite.
  • the fifth level of austenite may be one of: about 95 volume % austenite, about 96 volume % austenite, about 97 volume % austenite, about 98 volume % austenite or about 99 volume % austenite.
  • the fifth level of austenite may be within a fifth austenite level range (e.g., wherein the austenite level range is about 92 to 100 volume % austenite, preferably about 95 to 100 volume % austenite, or more preferably about 98 to 100 volume %).
  • the plate may be cooled (e.g., using air cooling methods and/or other cooling methods).
  • a second method for producing an alloy steel may be implemented.
  • the second method may be distinguished as (e.g., an example of) a hot rolling process.
  • the hot rolling process may comprise one or more hot rolling steps.
  • the hot rolling process may comprise steps similar to steps 205, 210 and/or 215 of the method 200.
  • the thermally homogenized product may be hot rolled to produce a second plate with a third thickness.
  • the thermally homogenized product may be hot rolled at one or more second hot rolling temperatures.
  • the thermally homogenized product may undergo hot rolling wherein the thermally homogenized product may be hot rolled at a second hot rolling start temperature at a beginning of the hot rolling (e.g., the thermally homogenized product) and the thermally homogenized product may be hot rolled at a second hot rolling finishing temperature at an end of the hot rolling (e.g., the thermally homogenized product).
  • the second hot rolling start temperature may be about 1100° C. Alternatively and/or additionally, the second hot rolling start temperature may be within the second temperature range. Alternatively and/or additionally, the second hot rolling start temperature may be greater than 1100° C.
  • the second hot rolling finishing temperature may be about 900° C. Alternatively and/or additionally, the second hot rolling finishing temperature may be within the third temperature range. Alternatively and/or additionally, the second hot rolling finishing temperature may be greater than 900° C.
  • the third thickness may be about 1 mm.
  • the third thickness may be one of: about 0.5 mm, about 1.5 mm, about 2 mm, about 2.5 mm, about 3.5 mm, about 4 mm, about 4.5 mm, about 5 mm, about 6 mm, about 7 mm, about 8 mm, about 9 mm, about 10 mm, about 11 mm, about 12 mm, about 13 mm, about 14 mm or about 15 mm.
  • the third thickness may be within the second thickness range.
  • the third thickness may be greater than 15 mm.
  • a third thickness reduction of the thickness of the thermally homogenized product to the third thickness may be about 93.3%.
  • the thickness of the thermally homogenized product may be about 15 mm and the third thickness may be about 1 mm.
  • the third thickness reduction of the thickness of the thermally homogenized product to the third thickness may be one of: about 50%, about 55%, about 60%, about 65%, about 70%, about 75%, about 85%, about 90%, about 95% or about 98%.
  • the third thickness reduction of the thickness of the thermally homogenized product to the third thickness may be within a third reduction range (e.g., wherein the third reduction range is one of: about 30% to 99%, preferably about 50% to 99%, 98%, more preferably about 75% to 97%, even more preferably about 85% to 96%, or especially preferred about 92% to 95%).
  • the third reduction range is one of: about 30% to 99%, preferably about 50% to 99%, 98%, more preferably about 75% to 97%, even more preferably about 85% to 96%, or especially preferred about 92% to 95%).
  • the second plate may be heat treated (e.g., and/or annealed) at a second heat treatment temperature for a fifth duration of time.
  • the second heat treatment temperature and/or the fifth duration of time may be based upon the plurality of heat treatment processes of the table 400.
  • the second heat treatment temperature and/or the fifth duration of time may be different than (e.g., each of) the plurality of heat treatment processes of the table 400.
  • the second heat treatment temperature may be configured such that a second crystal structure of a composition of the second plate has one of: the second level of austenite, the third level of austenite, the fourth level of austenite or the fifth level of austenite (e.g., at one or more times while the second plate is being heat treated and/or after the second plate is heat treated).
  • the second plate may be cooled (e.g., using air cooling methods and/or other cooling methods).
  • a third method for producing an alloy steel may be implemented.
  • the third method may be distinguished as (e.g., an example of) a cold rolling process.
  • the cold rolling process may comprise one or more hot rolling steps and/or one or more cold rolling steps.
  • the cold rolling process may comprise steps similar to steps 205, 210, 215 and/or 220 of the method 200.
  • the thermally homogenized product may be hot rolled (e.g., at the hot rolling start temperature and/or the hot rolling finishing temperature) to produce a third plate with the first thickness (e.g., and/or a fourth thickness).
  • a fourth thickness reduction of the thickness of the thermally homogenized product to the first thickness may be about 80%.
  • the thickness of the thermally homogenized product may be about 15 mm and the first thickness may be about 3 mm.
  • the fourth thickness reduction of the thickness of the thermally homogenized product to the first thickness may be one of: about 50%, about 55%, about 60%, about 65%, about 70%, about 75%, about 85%, about 90% or about 95%.
  • the fourth thickness reduction of the thickness of the thermally homogenized product to the first thickness may be within a fourth reduction range (e.g., wherein the fourth reduction range is one of: about 30% to 99%, preferably about 50% to 95%, more preferably about 60% to 95%, even more preferably about 70% to 90%, or especially preferred about 79% to 81%).
  • the third plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the third plate reaches the fourth temperature. Responsive to the third plate reaching the fourth temperature, a plate temperature of the third plate may be maintained at the fifth temperature (e.g., and/or the fourth temperature) for the second duration of time.
  • the third plate may not be cooled until the third plate reaches the fourth temperature and/or the plate temperature of the third plate may not be maintained at the fifth temperature.
  • the third plate may undergo a coiling process (e.g., in industrial steel making) (e.g., rather than being cooled until the third plate reaches the fourth temperature and/or the plate temperature of the third plate being maintained at the fifth temperature).
  • the third plate Responsive to completion of the maintaining the plate temperature of the third plate at the fifth temperature (e.g., and/or the fourth temperature) for the second duration of time and/or responsive to completion of the third plate undergoing the coiling process, the third plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the third plate reaches a ninth temperature.
  • the ninth temperature may correspond to ambient temperature (e.g., room temperature).
  • the ninth temperature may be within a ninth temperature range (e.g., wherein the ninth temperature range is one of: about 0° C to 100° C, preferably about 5° C to 50° C, more preferably about 10° C to 40° C, even more preferably about 15° C to 30° C, or especially preferred about 20° C to 25° C).
  • the third plate may be cold rolled at the ninth temperature (e.g., and/or a tenth temperature) until the plate has the second thickness (e.g., and/or a fifth thickness). In some examples, the third plate may be cold rolled responsive to the third plate reaching the ninth temperature.
  • a fifth thickness reduction of the first thickness of the third plate to the second thickness of the third plate may be about 66.7%.
  • the first thickness may be about 3 mm and the second thickness may be about 1 mm.
  • the fifth thickness reduction of the first thickness to the second thickness may be one of: about 25%, about 30%, about 35%, about 40%, about 45%, about 50%, about 55%, about 60%, about 65%, about 70%, about 80%, about 85%, about 90% or about 95%.
  • the fifth thickness reduction of the first thickness to the second thickness may be within a fifth reduction range (e.g., wherein the fifth reduction range is one of: about 30% to 95%, preferably about 40% to 80%, more preferably about 50% to 75%, even more preferably about 60% to 70%, or especially preferred about 65% to 70%).
  • the third plate may be heat treated (e.g., and/or annealed) at a third heat treatment temperature for a sixth duration of time.
  • the third heat treatment temperature and/or the sixth duration of time may be based upon the plurality of heat treatment process of the table 400.
  • the third heat treatment temperature and/or the sixth duration of time may be different than (e.g., each of) the plurality of heat treatment process of the table 400.
  • the third heat treatment temperature may be configured such that a third crystal structure of a composition of the third plate has one of: the second level of austenite, the third level of austenite, the fourth level of austenite or the fifth level of austenite (e.g., at one or more times while the third plate is being heat treated and/or after the third plate is heat treated).
  • the third plate may be cooled (e.g., using air cooling methods and/or other cooling methods).
  • the third plate may be cooled (e.g., using air cooling methods and/or other cooling methods).
  • FIGs. 3A-3G illustrate examples of a process 300 for producing an alloy steel.
  • the process 300 may be distinguished as (e.g., an example of) the warm rolling process.
  • FIG. 3A illustrates an alloy mixture 306 being melted to produce a melted alloy mixture 310.
  • the alloy mixture 306 having a composition corresponding to an alloy of the plurality of alloys in table 100, may be melted using a (e.g., vacuum induction melting) furnace.
  • the alloy mixture 306 may be melted in a crucible 304.
  • the crucible 304 may be an alumina crucible.
  • FIG. 3B illustrates the melted alloy mixture 310 being formed into a product.
  • the melted alloy mixture 310 may be cast in a (e.g., water-cooled) copper mold 308 to form the product.
  • Fig. 3C illustrates the product being heated to produce a thermally homogenized product 320.
  • the product may comprise one or more slabs 312.
  • the one or more slabs 312 may be heated inside a furnace 316 at a first temperature (e.g., about 1100° C or a different temperature) for a first duration of time (e.g., about 4 hours or a different duration of time).
  • the one or more slabs 312 may be heated using a burner 314.
  • the one or more slabs 312 may be heated using one or more (other) heating devices (e.g., electromagnetic heating devices, etc.) of the furnace 316.
  • other heating devices e.g., electromagnetic heating devices, etc.
  • FIG. 3D illustrates the thermally homogenized product 320 being hot rolled to produce a plate 324 with a first thickness.
  • the thermally homogenized product 320 may be hot rolled at one or more hot rolling temperatures.
  • the thermally homogenized product 320 may undergo hot rolling wherein the thermally homogenized product 320 may be hot rolled at a hot rolling start temperature (e.g., about 1100° C or a different temperature) at a beginning of the hot rolling (e.g., the thermally homogenized product 320) and the thermally homogenized product 320 may be hot rolled at a hot rolling finishing temperature (e.g., about 900° C or a different temperature) at an end of the hot rolling (e.g., the thermally homogenized product 320).
  • a hot rolling start temperature e.g., about 1100° C or a different temperature
  • a hot rolling finishing temperature e.g., about 900° C or a different temperature
  • a first thickness reduction of a thickness of the thermally homogenized product 320 to the first thickness may be about 80% (e.g., or a different value).
  • the thickness of the thermally homogenized product 320 may be about 15 mm and the first thickness may be about 3 mm.
  • the plate 324 may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate 324 reaches a second temperature (e.g., about 700° C or a different temperature).
  • a second temperature e.g., about 700° C or a different temperature
  • FIG.3E illustrates the plate 324 being heated using a second furnace 328.
  • a plate temperature of the plate 324 may be maintained at a third temperature (e.g., about 700° C or a different temperature) for a second duration of time (e.g., about 1 hour or a different duration of time).
  • a second burner 326 e.g., and/or one or more heating devices of the second furnace 328
  • the second furnace 328 may be the same as the furnace 316.
  • the second furnace 328 may be different than the furnace 316.
  • FIG. 3F illustrates the plate 324 being warm rolled at a warm rolling temperature (e.g., 450° C or a different temperature) until the plate has a second thickness.
  • a warm rolling temperature e.g., 450° C or a different temperature
  • the plate 324 may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate 324 reaches a fourth temperature (e.g., 450° C or a different temperature).
  • a second thickness reduction of the first thickness (e.g., of the plate 324) to the second thickness (e.g., of the plate 324) may be about 66.7% (e.g., or a different value).
  • the second thickness may be about 1 mm.
  • FIG. 3G illustrates the plate 324 being heat treated (e.g., and/or annealed) using a third furnace 334.
  • the third furnace 334 may be a muffle furnace.
  • the plate 324 may be heat treated at a heat treatment temperature for a third duration of time using a third burner 332 and/or one or more heating devices of the third furnace 334.
  • the third furnace 334 may be the same as the furnace 316 and/or the second furnace 328. Alternatively and/or additionally, the third furnace 334 may be different than the furnace 316 and/or the second furnace 328.
  • the plate 324 may be heat treated while (e.g., positioned) inside of (e.g., and/or on top of, adjacent to, etc.) a cast-iron filings medium.
  • FIG. 5 illustrates a table 500 of a plurality of density measurements corresponding to the plurality of alloy steels (e.g., presented in the table 100).
  • the plurality of density measurements may be represented in grams (g) per cubic centimeter (cm3).
  • the plurality of density measurements were measured at ambient temperature based upon the Archimedean technique using an electronic balance.
  • the plurality of density measurements may have been measured with a precision of ⁇ 0.01 g.
  • the plurality of density measurements may range from about 7.43 g/cm3 to 7.66 g/cm3.
  • each hot rolled alloy steel of the set of hot rolled alloy steels may have a thickness of about 3 mm.
  • FIGs. 6A-6D illustrate a table 600 of mechanical properties corresponding to the plurality of alloy steels (e.g., presented in the table 100).
  • the table 600 may comprise a plurality of sets of mechanical properties.
  • Each set of mechanical properties of the plurality of sets of mechanical properties may correspond to an alloy steel of the plurality of alloy steels, a rolling process (e.g., wherein“HR” indicates the hot rolling process of the second method and“CR” indicates the cold rolling process of the third method) and/or a heat treatment process (e.g., corresponding to the plurality of heat treatment processes of the table 400).
  • a first set of mechanical properties may correspond to a first instance of the Alloy 1 that underwent the hot rolling process and did not undergo a heat treatment process.
  • the first instance of the Alloy 1 may have a yield strength of about 586+16 megapascals (MPa), a tensile strength (e.g., and/or an ultimate tensile strength) of about 695+12 MPa and an elongation of about 50.0+2%.
  • a second set of mechanical properties may correspond to a second instance of the Alloy 1 that underwent the hot rolling process and underwent a heat treatment process HT 18 of the plurality of heat treatment processes of the table 400.
  • the second instance of the Alloy 1 may have a yield strength of about 219+2 MPa, a tensile strength (e.g., and/or an ultimate tensile strength) of about 568+10 MPa and an elongation of about 83.0+5%.
  • the mechanical properties of the table 600 were measured using uniaxial tensile testing techniques at ambient temperature. Tests were performed on specimens of each (e.g., instance of each) alloy steel of the table 100 and/or the table 600. Each specimen, prepared and/or produced by electrical discharge machining techniques, had a cross-section of about 3x1 mm2 and/or a gauge length of about 11.4 mm. Uniaxial tensile tests were conducted along a rolling direction of the specimens using an Instron 5967 30kN testing machine at a strain rate of 8.5x10-4 s-l (0.6 mm/minute). Yield strengths were measured using a 0.2% offset plastic strain method.
  • Each measurement of the mechanical properties may be a mean value of three measurements corresponding to three tests performed on three specimens (e.g., of the same type).
  • a plurality of yield strength measurements of the table 600 may range from about 211 to 2000 MPa.
  • a plurality of tensile strength measurements of the table 600 may range from about 568 to 2070 MPa.
  • a plurality of elongation measurements of the table 600 may range from about 0.2% to 92.3%.
  • FIGs. 7A-7D illustrate mechanical properties corresponding to a set of alloy steels of the plurality of alloy steels (e.g., presented in the table 100) that undergo (e.g., a process similar to) the warm rolling process of the method 200.
  • the set of alloy steels may comprise an Alloy 13, an Alloy 19 and an Alloy 23.
  • the Alloy 13, the Alloy 19 and the Alloy 23 may be selected for the warm rolling process based upon work-hardening capacities of the Alloy 13, the Alloy 19 and the Alloy 23 (e.g., that may be higher than work-hardening capacities of other alloy steels of the plurality of alloy steels) determined based upon the plurality of sets of mechanical properties of the table 600.
  • FIG. 7 A illustrates a table 700 of the mechanical properties corresponding to the set of alloy steels.
  • the table 700 comprises a second plurality of sets of mechanical properties.
  • Each set of mechanical properties of the second plurality of sets of mechanical properties may correspond to an alloy steel of the set of alloy steels, the warm rolling process (e.g., wherein“WR” indicates the warm rolling process of the method 200) and/or a heat treatment process (e.g., corresponding to the plurality of heat treatment processes of the table 400).
  • the mechanical properties of the table 700 were measured using uniaxial tensile testing techniques at ambient temperature. Tests were performed on specimens of the Alloy 13, the Alloy 19 and the Alloy 23. Each specimen, prepared and/or produced by electrical discharge machining techniques, had a cross-section of about 3x1 mm2 and/or a gauge length of about 11.4 mm. Each specimen may have been cut parallel to a rolling direction. Uniaxial tensile tests were conducted on the specimens using an Instron 5967 30kN testing machine at an (e.g., initial) strain rate of 8.5x10-4 s-l (0.6 mm/minute). A second plurality of yield strength measurements of the table 700 may range from about 345 to 1603 MPa. A second plurality of tensile strength measurements of the table 700 may range from about 1280 to 1824 MPa. A plurality of elongation measurements of the table 600 may range from about 18% to 55.1%.
  • a first set of mechanical properties of the table 700 may correspond to a first instance of the Alloy 13 that underwent the warm rolling process and did not undergo a heat treatment process.
  • the first instance of the Alloy 13 may have a yield strength of about 1495+19 MPa, a tensile strength (e.g., and/or an ultimate tensile strength) of about 1824+59 MPa and an elongation of about 18+5%.
  • a second set of mechanical properties of the table 700 may correspond to a second instance of the Alloy 13 that underwent the warm rolling process and underwent the heat treatment process HT 1 of the plurality of heat treatment processes of the table 400.
  • the first heat treatment temperature of the heat treatment process HT 1 may cause a crystal structure of the Alloy 13 to have the second level of austenite.
  • the second instance of the Alloy 13 may have a yield strength of about 1000+22 MPa, a tensile strength of about 1579+71 MPa and an elongation of about 34.8+7%.
  • a third set of mechanical properties of the table 700 may correspond to a third instance of the Alloy 13 that underwent the warm rolling process and underwent a heat treatment process HT 5 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 5 may cause the crystal structure of the Alloy 13 to have the third level of austenite.
  • the third instance of the Alloy 13 may have a yield strength of about 1040+43 MPa, a tensile strength of about 1740+44 MPa and an elongation of about 36.8+9%.
  • a fourth set of mechanical properties of the table 700 may correspond to a fourth instance of the Alloy 13 that underwent the warm rolling process and underwent a heat treatment process HT 9 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 9 may cause the crystal structure of the Alloy 13 to have the fourth level of austenite.
  • the fourth instance of the Alloy 13 may have a yield strength of about 1050+21 MPa, a tensile strength of about 1570+32 MPa and an elongation of about 33+8%.
  • a fifth set of mechanical properties of the table 700 may correspond to a fifth instance of the Alloy 13 that underwent the warm rolling process and underwent a heat treatment process HT 17 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 17 may cause the crystal structure of the Alloy 13 to have the fifth level of austenite.
  • the fifth instance of the Alloy 13 may have a yield strength of about 345+10 MPa, a tensile strength of about 1500+19 MPa and an elongation of about 32.8+8%.
  • a sixth set of mechanical properties of the table 700 may correspond to a first instance of the Alloy 19 that underwent the warm rolling process and did not undergo a heat treatment process.
  • the first instance of the Alloy 19 may have a yield strength of about 1143+44 MPa, a tensile strength of about 1570+55 MPa and an elongation of about 48+7%.
  • a seventh set of mechanical properties of the table 700 may correspond to a second instance of the Alloy 19 that underwent the warm rolling process and underwent a heat treatment process HT 2 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 2 may cause a crystal structure of the Alloy 19 to have the second level of austenite.
  • the second instance of the Alloy 19 may have a yield strength of about 1050+21 MPa, a tensile strength of about 1400+32 MPa and an elongation of about 48.8+4%.
  • an eighth set of mechanical properties of the table 700 may correspond to a third instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 5 of the plurality of heat treatment processes of the table 400.
  • the heat treatment temperature of the heat treatment process HT 5 may cause the crystal structure of the Alloy 19 to have the third level of austenite.
  • the third instance of the Alloy 19 may have a yield strength of about 1040+54 MPa, a tensile strength of about 1370+17 MPa and an elongation of about 50.3+11%.
  • a ninth set of mechanical properties of the table 700 may correspond to a fourth instance of the Alloy 19 that underwent the warm rolling process and underwent a heat treatment process HT 11 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 11 may cause the crystal structure of the Alloy 19 to have the fourth level of austenite.
  • the fourth instance of the Alloy 19 may have a yield strength of about 770+17 MPa, a tensile strength of about 1440+26 MPa and an elongation of about 50+8%.
  • a tenth set of mechanical properties of the table 700 may correspond to a fifth instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 17 of the plurality of heat treatment processes of the table 400.
  • the heat treatment temperature of the heat treatment process HT 17 may cause the crystal structure of the Alloy 19 to have the fifth level of austenite.
  • the fifth instance of the Alloy 19 may have a yield strength of about 413+21 MPa, a tensile strength of about 1280+12 MPa and an elongation of about 52+10%.
  • an eleventh set of mechanical properties of the table 700 may correspond to a first instance of the Alloy 23 that underwent the warm rolling process and did not undergo a heat treatment process.
  • the first instance of the Alloy 23 may have a yield strength of about 1500+15 MPa, a tensile strength of about 1650+22 MPa and an elongation of about 28.8+3%.
  • a twelfth set of mechanical properties of the table 700 may correspond to a second instance of the Alloy 23 that underwent the warm rolling process and underwent a heat treatment process HT 3 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 3 may cause a crystal structure of the Alloy 23 to have the second level of austenite.
  • the second instance of the Alloy 23 may have a yield strength of about 1603+19 MPa, a tensile strength of about 1730+32 MPa and an elongation of about 42+5%.
  • a thirteenth set of mechanical properties of the table 700 may correspond to a third instance of the Alloy 23 that underwent the warm rolling process and underwent a heat treatment process HT 6 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 6 may cause the crystal structure of the Alloy 23 to have the third level of austenite.
  • the third instance of the Alloy 23 may have a yield strength of about 1510+11 MPa, a tensile strength of about 1720+20 MPa and an elongation of about 45.4+6%.
  • a fourteenth set of mechanical properties of the table 700 may correspond to a fourth instance of the Alloy 23 that underwent the warm rolling process and underwent a heat treatment process HT 10 of the plurality of heat treatment processes of the table 400.
  • a heat treatment temperature of the heat treatment process HT 10 may cause the crystal structure of the Alloy 23 to have the fourth level of austenite.
  • the fourth instance of the Alloy 23 may have a yield strength of about 1500+18 MPa, a tensile strength of about 1690+33 MPa and an elongation of about 45+4%.
  • a fifteenth set of mechanical properties of the table 700 may correspond to a fifth instance of the Alloy 23 that underwent the warm rolling process and underwent the heat treatment process HT 17 of the plurality of heat treatment processes of the table 400.
  • the heat treatment temperature of the heat treatment process HT 17 may cause the crystal structure of the Alloy 23 to have the fifth level of austenite.
  • the fifth instance of the Alloy 23 may have a yield strength of about 561.2+14 MPa, a tensile strength of about 1670+21 MPa and an elongation of about 55.1+15%.
  • FIG. 7B illustrates a stress-strain diagram corresponding to the Alloy 13.
  • Stress (MPa) values e.g., y-axis
  • elongation (%) values e.g., x-axis.
  • a first curve 722 may represent the first instance of the Alloy 13 that underwent the warm rolling process and did not undergo a heat treatment process.
  • a second curve 730 may represent the third instance of the Alloy 13 that underwent the warm rolling process and underwent the heat treatment process HT 5.
  • a third curve 728 may represent the second instance of the Alloy 13 that underwent the warm rolling process and underwent the heat treatment process HT 1.
  • a fourth curve 726 may represent the fourth instance of the Alloy 13 that underwent the warm rolling process and underwent the heat treatment process HT 9.
  • a fifth curve 724 may represent the fifth instance of the Alloy 13 that underwent the warm rolling process and underwent the heat treatment process HT 17.
  • FIG. 7C illustrates a stress-strain diagram corresponding to the Alloy 19.
  • Stress (MPa) values e.g., y-axis
  • elongation (%) values e.g., x-axis.
  • a first curve 742 may represent the first instance of the Alloy 19 that underwent the warm rolling process and did not undergo a heat treatment process.
  • a second curve 744 may represent the third instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 5.
  • a third curve 746 may represent the second instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 2.
  • a fourth curve 748 may represent the fourth instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 11.
  • a fifth curve 750 may represent the fifth instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 17.
  • FIG. 7D illustrates a stress-strain diagram corresponding to the Alloy 23. Stress (MPa) values (e.g., y-axis) are shown as a function of elongation (%) values (e.g., x-axis).
  • a first curve 762 may represent the first instance of the Alloy 23 that underwent the warm rolling process and did not undergo a heat treatment process.
  • a second curve 764 may represent the second instance of the Alloy 23 that underwent the warm rolling process and underwent the heat treatment process HT 3.
  • a third curve 766 may represent the third instance of the Alloy 19 that underwent the warm rolling process and underwent the heat treatment process HT 6.
  • a fourth curve 768 may represent the fourth instance of the Alloy 23 that underwent the warm rolling process and underwent the heat treatment process HT 10.
  • a fifth curve 770 may represent the fifth instance of the Alloy 23 that underwent the warm rolling process and underwent the heat treatment process HT 17.
  • the Alloy 13, the Alloy 19 and/or the Alloy 23 may undergo a process similar to the cold rolling process of the third method.
  • the process may comprise melting an alloy mixture to produce a melted alloy mixture using a (e.g., vacuum induction melting) furnace.
  • a (e.g., vacuum induction melting) furnace e.g., an argon atmosphere (e.g., and/or a different type of atmosphere) may be maintained in the furnace.
  • the melted alloy mixture may be formed into a product (e.g., using one or more fast solidification methods).
  • the melted alloy mixture may be cast in a water-cooled copper mold to form the product (e.g., comprising one or more slabs, one or more ingots and/or one or more billets).
  • the product may be heated to produce a thermally homogenized product.
  • the product may be heated to a first temperature for a first duration of time.
  • a temperature of the product may be maintained at the first temperature for the first duration of time.
  • the first temperature may be about 1100° C (e.g., and/or a different temperature).
  • the first duration of time may be about 2 hours (e.g., and/or a different duration of time).
  • a thickness of the thermally homogenized product may be 15 mm.
  • a size of the thermally homogenized product may be 50x30x15 mm3.
  • the thermally homogenized product may be hot rolled (e.g., for 10 passes and/or a different number of passes) to produce a plate with a first thickness (e.g., about 3mm or a different thickness).
  • the thermally homogenized product may be rolled using a 200mm trial rolling mill.
  • the thermally homogenized product may undergo hot rolling wherein the thermally homogenized product may be hot rolled at a hot rolling start temperature at a beginning of the hot rolling (e.g., the thermally homogenized product) and the thermally homogenized product may be hot rolled at a hot rolling finishing temperature at an end of the hot rolling (e.g., the thermally homogenized product).
  • the hot rolling start temperature may be about 1100° C (e.g., and/or a different temperature) and/or the hot rolling finishing temperature may be about 950° C (e.g., and/or a different temperature).
  • the plate Responsive to (e.g., completion of) the hot rolling the thermally homogenized product (e.g., and/or responsive to producing the plate), the plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate reaches a second temperature (e.g., about 700° C or a different temperature). Responsive to the plate reaching the second temperature, a plate temperature of the plate may be maintained at a third temperature (e.g., about 700° C or a different temperature) for a second duration of time (e.g., 1 hour and/or a different duration of time). In some examples, rather than cooling the plate until the plate reaches the second temperature, the plate may be cooled until the plate reaches ambient temperature. The plate may then be heated to a fourth temperature (e.g., about 700° C or a different temperature). Responsive to the plate reaching the fourth temperature, the plate temperature of the plate may be maintained at the third temperature for the second duration of time.
  • a second temperature
  • the plate Responsive to completion of the maintaining the plate temperature of the plate at the third temperature for the second duration of time and/or responsive to completion of the plate undergoing the coiling process, the plate may be cooled (e.g., using air cooling methods and/or other cooling methods) until the plate reaches a fifth temperature (e.g., ambient temperature and/or a different temperature).
  • a fifth temperature e.g., ambient temperature and/or a different temperature
  • the plate may be cold rolled at the fifth temperature until the plate has a second thickness.
  • a cold rolling thickness reduction of the first thickness to the second thickness may be at a first thickness reduction level (e.g., about 33%), a second thickness reduction level (e.g., about 40%) or a third thickness reduction level (e.g., about 44%).
  • the plate may be heat treated (e.g., and/or annealed) at a heat treatment temperature for a third duration of time.
  • the heat treatment temperature and/or the third duration of time may be based upon the plurality of heat treatment process of the table 400.
  • the heat treatment temperature and/or the third duration of time may be different than (e.g., each of) the plurality of heat treatment process of the table 400.
  • the heat treatment temperature may be configured such that a crystal structure of a composition of the plate has one of: a second level of austenite (e.g., about 20%), a third level of austenite (e.g., about 50%), a fourth level of austenite (e.g., about 80%) or a fifth level of austenite (e.g., about 100%) (e.g., at one or more times while the plate is being heat treated and/or after the plate is heat treated).
  • a second level of austenite e.g., about 20%
  • a third level of austenite e.g., about 50%
  • a fourth level of austenite e.g., about 80%
  • a fifth level of austenite e.g., about 100%
  • the third plate may be cooled (e.g., using air cooling methods and/or other cooling methods).
  • FIG. 8 illustrates a table 800 of mechanical properties corresponding to the Alloy 13, the Alloy 19 and the Alloy 23.
  • the table 800 comprises a third plurality of sets of mechanical properties.
  • Each set of mechanical properties of the third plurality of sets of mechanical properties may correspond to an alloy steel (e.g., the Alloy 13, the Alloy 19 or the Alloy 23), a rolling process (e.g., wherein“CR” indicates the cold rolling process of the third method), the cold rolling thickness reduction (e.g., the first thickness reduction level of about 33%, the second thickness reduction level of about 40% or the third thickness reduction level of about 44%) and/or a heat treatment process (e.g., corresponding to the plurality of heat treatment processes of the table 400).
  • an alloy steel e.g., the Alloy 13, the Alloy 19 or the Alloy 23
  • a rolling process e.g., wherein“CR” indicates the cold rolling process of the third method
  • the cold rolling thickness reduction e.g.,
  • a third plurality of yield strength measurements of the table 800 may range from about 590 to 1557 MPa.
  • a third plurality of tensile strength measurements of the table 800 may range from about 1310 to 2200 MPa.
  • a third plurality of elongation measurements of the table 800 may range from about 3.4% to 67.2%.
  • One or more alloy steels provided herein and/or one or more methods for producing alloy steels may lead to benefits including improved mechanical properties, such as a combination of higher ductility (e.g., elongation), higher yield strength and/or higher tensile strength. Accordingly, the one or more alloy steels may be beneficial for use in a variety of applications such as motor vehicles, ships, roads, railways, appliances, buildings, industrial applications, etc. For example, a weight of a motor-vehicle employing the one or more alloy steels may have less weight than a motor- vehicle employing different steels. Further, a safety, fuel consumption, etc.
  • the one or more alloy steels comprise low- cost elements and/or materials and do not comprise (e.g., a substantial amount of) high-cost elements and/or materials. Accordingly, the one or more alloy steels may be beneficial for use in a variety of applications such as motor vehicles, ships, roads, railways, appliances, buildings, industrial applications, etc. as a result of the lower costs of the one or more alloy steels.
  • first,”“second,” and/or the like are not intended to imply a temporal aspect, a spatial aspect, an ordering, etc. Rather, such terms are merely used as identifiers, names, etc. for features, elements, items, etc.
  • a first object and a second object generally correspond to object A and object B or two different or two identical objects or the same object.
  • example is used herein to mean serving as an instance, illustration, etc., and not necessarily as advantageous.
  • “or” is intended to mean an inclusive “or” rather than an exclusive “or”.
  • “a” and “an” as used in this application are generally be construed to mean “one or more” unless specified otherwise or clear from context to be directed to a singular form.
  • at least one of A and B and/or the like generally means A or B or both A and B.
  • such terms are intended to be inclusive in a manner similar to the term “comprising”.

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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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Abstract

L'invention concerne un procédé de production d'un acier allié. Un mélange d'alliage peut être fondu en vue de produire un mélange d'alliage fondu. Le mélange d'alliage comporte 2 à 4 % en poids de chrome (Cr), 12 à 16 % en poids de manganèse (Mn), au plus 4 % en poids de silicium (Si), 1 à 3 % en poids d'aluminium (Al), au plus 0,3 % en poids de carbone (C) et du fer (Fe). Le mélange d'alliage fondu peut être formé en un produit. Le produit peut être chauffé en vue de produire un produit homogénéisé thermiquement. Le produit homogénéisé thermiquement peut être laminé à chaud en une plaque dotée d'une première épaisseur. La plaque peut être laminée à chaud à une température de laminage à chaud jusqu'à ce que la plaque présente une seconde épaisseur. La température de laminage à chaud peut être conçue de sorte qu'une structure cristalline de la plaque présente 30 à 70 % en volume d'austénite. La température de laminage à chaud peut être comprise entre 350 °C et 550 °C.
PCT/IB2018/057129 2018-06-12 2018-09-18 Alliage d'acier à teneur élevée en manganèse et son procédé de production WO2019239206A1 (fr)

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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4512804A (en) * 1982-04-13 1985-04-23 Vereinigte Edelstahlwerke Aktiengesellschaft (Vew) Work-hardenable austenitic manganese steel and method for the production thereof
EP2663411B1 (fr) * 2011-01-11 2017-02-15 ThyssenKrupp Steel Europe AG Procédé de fabrication d'un produit en acier plat laminé a chaud

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106119493B (zh) * 2016-07-25 2019-01-18 钢铁研究总院 具有优良塑性的超高强度中锰汽车钢板及制备方法

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4512804A (en) * 1982-04-13 1985-04-23 Vereinigte Edelstahlwerke Aktiengesellschaft (Vew) Work-hardenable austenitic manganese steel and method for the production thereof
EP2663411B1 (fr) * 2011-01-11 2017-02-15 ThyssenKrupp Steel Europe AG Procédé de fabrication d'un produit en acier plat laminé a chaud

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