EP3225702B1 - Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier - Google Patents

Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier Download PDF

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Publication number
EP3225702B1
EP3225702B1 EP16162652.8A EP16162652A EP3225702B1 EP 3225702 B1 EP3225702 B1 EP 3225702B1 EP 16162652 A EP16162652 A EP 16162652A EP 3225702 B1 EP3225702 B1 EP 3225702B1
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Prior art keywords
steel
content
weight
product
flat
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EP16162652.8A
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German (de)
English (en)
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EP3225702A1 (fr
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Hans-Günter KRULL
Frank van Soest
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Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
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Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
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Priority to EP16162652.8A priority Critical patent/EP3225702B1/fr
Priority to ES16162652T priority patent/ES2791887T3/es
Priority to PCT/EP2017/057359 priority patent/WO2017167778A1/fr
Priority to US16/089,616 priority patent/US20190119771A1/en
Publication of EP3225702A1 publication Critical patent/EP3225702A1/fr
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    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • 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
    • C21D8/0231—Warm rolling
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
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    • 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
    • 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
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to a steel with a reduced density as a result of its high Al content and to a method for producing a flat or long product from such a steel.
  • steel flat product or “flat product” denotes rolled products whose thickness is very much less than their length and width.
  • the steel flat products or flat products concerned are sheets, strips or blanks obtained from these sheets or strips.
  • long steel products or “long products”, on the other hand, refer to products obtained by forming a preliminary product, the length of which is significantly greater than its width and thickness, but for which the width and thickness are usually of comparable magnitudes.
  • Typical examples of long products are bars, rods, profiles and the like.
  • aluminum is one of the elements that have a ferrite-stabilizing effect and can even completely suppress the austenite-ferrite conversion.
  • a steel is known from JP H11-350087 A which is resistant to corrosion and is said to be inexpensive to produce.
  • this steel (in% by weight) consists of 0.01-3.0% Si, 0.01-3.0% Mn, 0.1-9.9% Cr, 0.1-10% Al and the balance of iron and unavoidable impurities, which include contents of up to 0.02% C, up to 0.03% P, up to 0.01% S and up to 0.02% N.
  • Ti can also be contained in this steel in order to improve the corrosion resistance.
  • a steel alloy with improved resistance, in particular to seawater corrosion which, in addition to iron 0.9-7% by weight Al and at least one further alloy component from the group "Co, Mo and Ti", in an amount of up to 5% by weight.
  • % Co, up to 5% by weight Mo and up to 1.5% by weight Ti and amounts customary for low-alloy steels of C, Mn, Si, P and S.
  • the object of the invention was to provide a reduced-density material based on iron, the mechanical properties of which make it suitable for a wide range of applications, in particular in the automotive industry.
  • the invention has achieved this object by the steel specified in claim 1.
  • the invention has achieved the above-mentioned object in that the working steps specified in claim 8 are used in the processing of steels according to the invention into flat or long products.
  • the required strength of more than 500 MPa is formed in addition to the known solid-solution strengthening elements chromium, molybdenum, silicon and manganese via precipitation phases. These phases are mainly excreted intracrystalline.
  • Strength-increasing intermetallic phases such as the Laves phase, essentially consist of iron, titanium and optionally of molybdenum, Ni (Mn, Al, Ti), Ni 2 MnAl, Ni 3 Ti and Cu. Fine carbides, fine nitrides and fine carbonitrides also contribute to the strength level.
  • alloying with carbon was largely dispensed with in the alloy concept according to the invention and the freedom from conversion was accepted.
  • the carbon and nitrogen contents in the steel according to the invention are instead limited to the lowest possible values so that at most isolated carbides or carbonitrides are formed during solidification.
  • the C content of the steel according to the invention is at most 0.2% by weight.
  • the formation of undesired carbides can be prevented particularly reliably if the C content is less than 0.1% by weight, in particular at most 0.02% by weight or at most 0.01% by weight.
  • the N content is limited to at most 0.020% by weight, in particular at most 0.005% by weight.
  • the Al content of steels according to the invention is 10-25% by weight.
  • the invention provides for Al contents of more than 12% by weight that the contents of Cr, Mo, Mn, Si, V, W, Ni, Nb, Ti meet the following condition: (% Cr + 2 *% Mo +% Mn +% Si +% V +% W +% Ni +% Nb +% Ti)> 0.05 *% Al with% Cr: Cr content of the steel,% Mo: Mo content of the steel,% Mn: Mn content of the steel,% Si: Si content of the steel,% V: V content of the steel,% W: W Steel content,% Ni: Ni content of steel,% Nb: Nb content of steel,% Ti: Ti content of steel and% Al: Al content of steel.
  • Si 0.1-3.5% by weight of Si, in particular up to 1.5% by weight of Si, is present in the steel according to the invention.
  • the presence of Si has a particularly safe effect if the Si content is at least 0.20% by weight.
  • Sulfur can be added to the steel according to the invention to improve its machinability in contents of up to 0.40% by weight, with optimum effects being obtained at contents of up to 0.28% by weight.
  • the S content of a steel according to the invention can be set to at least 0.01% by weight.
  • the strength of the material can be adjusted by the targeted addition of up to 10% by weight of Ti.
  • This effect of Ti can be achieved particularly reliably by at least 0.60% by weight of Ti in steel according to the invention are present.
  • Optimal effects of Ti result if the Ti content is at least 0.90% by weight or at most 2.0% by weight.
  • Chromium in contents of up to 6.0% by weight helps to avoid superstructure D03 and to solidify the solid solution.
  • the Cr content can be set to at least 0.30% by weight. Optimal effects result when at least 0.50% by weight or at most 3.5% by weight Cr is present in the steel according to the invention.
  • Mo in contents of up to 3.0% by weight helps to avoid superstructure D03, contributes to solidification of the solid solution and promotes the formation of desired precipitates.
  • the Mo content can be set to at least 0.1% by weight, optimal effects of the presence of Mo occurring in the steel according to the invention if its Mo content is at least 0.25% by weight or at most 2.8% by weight.
  • V is present in the steel according to the invention in contents of up to 1.0% by weight, superstructure D03 can also be avoided.
  • the V content can be set to at least 0.10% by weight, optimal effects of the presence of V occurring in the steel according to the invention if its V content is at least 0.20 or at most 0.50% by weight .-%.
  • Tungsten in contents of up to 1.0% by weight also has a positive effect on avoiding the superstructure D03.
  • the W content can be set to at least 0.20% by weight.
  • Optimal effects result when at least 0.40% by weight or at most 1.0% by weight W is present in the steel according to the invention.
  • W as an alternative to Mo
  • twice as much tungsten as molybdenum must be added.
  • Copper in contents of up to 4% by weight in the steel according to the invention has the effect that the strength is increased by copper precipitates. This effect can be used with certainty that the Cu content is at least 0.5% by weight, contents of at most 3.50% by weight having proven to be particularly positive. In order to ensure the hot formability, approximately the same amount of nickel should be alloyed to the material.
  • the addition of up to 0.08% by weight of boron can suppress the precipitation behavior of the hardness-increasing phases at the grain boundaries in the steel according to the invention. This can certainly be achieved by having at least 0.0005% by weight of B in the steel according to the invention. B contents of more than 0.08% by weight, on the other hand, have a negative effect on the formability of the steel. In order to reliably avoid this, the B content of the steel according to the invention can be limited to at most 0.0030% by weight.
  • Nb is present in the steel according to the invention in a content of up to 1.5% by weight, Nb also contributes to avoiding the superstructure D03 and strengthening precipitation phases are formed.
  • the Nb content can be set to at least 0.05% by weight, optimal effects of the presence of Nb occurring in the steel according to the invention if its Nb content is at least 0.10% by weight or at most Is 0.30% by weight.
  • the structure matrix of the steel according to the invention largely exists, i.e. at least 85% by volume of ferrite, with higher ferrite contents of at least 90% by volume being particularly favorable.
  • An austenite content of up to 10% by volume in the structure can also have a positive effect on the toughness of the steel. Therefore it can It may be expedient to adjust the alloy of the steel according to the invention so that at least 2% by volume of austenite is present in the structure of the steel. If the austenite content is greater than 10 vol.%, This has a negative effect on the precipitation behavior of the intermetallic phases.
  • the remaining structural components not taken up by ferrite or austenite are contents of intermetallic phases as well as components of carbide, nitride, bainite or pearlite.
  • the proportions of these remaining constituents in the structure of the steel according to the invention are so small that they have at most insignificant effects on its properties.
  • Undesirable austenite fractions exceeding 10% by volume can be prevented by a suitable adjustment of the Mn and Ni contents of the steel according to the invention.
  • the Mn content of a steel according to the invention is limited to a maximum of 3.5% by weight and the Ni content to a maximum of 4.0% by weight.
  • the positive influence of Mn and Ni on the properties of the steel according to the invention can be used in an optimized manner if the sum of the contents of Mn and Ni is at most 5% by weight. It proves particularly advantageous if the Mn content is set to a maximum of 1.0% by weight or the Ni content to a maximum of 1.5 times the optionally present copper content.
  • the positive influences of the presence of Mn or Ni, such as the maintenance of optimized mechanical properties made possible by the targeted addition of Ni or Mn, in the steel according to the invention can be particularly exploited in that the Mn content of the steel is at least 0.20% by weight. is.
  • Negative effects of the S content specifically approved according to the invention can be avoided by setting the ratio% Mn /% S of the manganese content% Mn to the sulfur content% S to more than 2.0 becomes.
  • the hot forming in the temperature range of 700 - 1280 ° C achieves a complete solution of any precipitations, adequate forming forces, sufficient recrystallization kinetics and minimal grain growth.
  • the flat or long product obtained according to the invention can undergo different heat treatments in order to adjust its mechanical properties.
  • An advantageous way of such a heat treatment in terms of energy utilization can be that the steel flat or long product obtained after the hot forming after the hot forming with a cooling rate of max. 3.0 K / min, in particular 1.5 K / min, is slowly cooled, the cooling rate not being less than 1.0 K / min from a process economics point of view.
  • the final strength of the steel is achieved in a direct manner by eliminating the precipitation phases, such as Laves, Heussler, copper, Ni3Ti and / or Ni3Al phases. This procedure is particularly advantageous if the Ti content of the steel according to the invention is more than 0.60% by weight.
  • the tensile strength of the flat or long product obtained in this way is typically in the range from 700 to 1150 MPa.
  • the product obtained can be aged at temperatures of 150-700 ° C. over a period of 15 minutes to 30 hours in order to positively influence the state of excretion of its structure.
  • the Ti-containing precipitation phases are precipitated, which in particular cause an increase in strength.
  • a steel S1 with the composition given in Table 1 was melted and cast into a block. This preliminary product has been heated to a hot forming temperature of 1050 ° C and has been pressed at this temperature into a semi-finished product (long product).
  • the product thus obtained was solution-annealed at a solution annealing temperature of 1050 ° C. for 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 800 MPa and could be machined easily with this comparably low strength.
  • the processed product was aged for 4 hours at 500 ° C. to adjust its final strength. After this aging, the steel of the product had a strength of 1070 MPa. It turned out that the aging treatment led to minimal warpage of the product at best. An aging at a temperature of 550 ° C and a duration of 1 h resulted in a strength of 1200 MPa. A strength of 1300 MPa could be achieved at a temperature of 600 ° C and the same aging time of 1 h.
  • the density of the steel S1 used in Example 1 was 6.9 kg / dm 3 .
  • a steel S2 with the composition given in Table 1 was melted and cast into a block.
  • the preliminary product in question was formed at a hot forming temperature of 1050 ° C by pressing.
  • the product thus obtained was solution-annealed at a solution annealing temperature of 1050 ° C. for 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 920 MPa and could be easily machined with this comparably low strength.
  • the product was aged for 4 hours after mechanical processing at 500 ° C. After this aging, the steel of the product had a strength of 1175 MPa. It was also shown here that the aging treatment resulted in minimal warpage of the product.
  • the density of the steel S2 used in Example 2 was 6.9 kg / dm 3 .
  • a steel S3 with the composition given in Table 1 was melted and cast into a block.
  • the preliminary product in question was formed into a block at a hot forming temperature of 1000 ° C. by pressing.
  • the product thus obtained was solution-annealed at a solution annealing temperature of 1075 ° C. for 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 860 MPa and could be easily machined with this comparably low strength.
  • the product was aged for 1 hour at 550 ° C to adjust its final strength. After this aging, the steel of the product had a strength of 1540 MPa. It turned out that the aging treatment led to minimal warpage of the product at best.
  • the density of the steel S3 used in Example 3 was 6.7 kg / dm 3 .
  • a steel S4 with the composition given in Table 1 was melted and cast into a block. Chromium and molybdenum were added to the melt to avoid a harmful superstructure (D03) and to solidify the solid solution.
  • the preliminary product in question was formed at a hot forming temperature of 1075 ° C by pressing.
  • the product thus obtained was solution-annealed at a solution annealing temperature of 1050 ° C. for 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 805 MPa and could be machined easily with this comparably low strength.
  • the product was aged at 550 ° C for 1 hour. After this outsourcing, the steel of the product showed a strength of 1260 MPa. It turned out that the aging treatment led to minimal warpage of the product at best.
  • the density of the steel S4 used in Example 4 was 6.1 kg / dm 3 .

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (13)

  1. Acier ayant une densité inférieure à 7,25 kg/dm3 et composé de, en % massiques C : jusqu'à 0,20 % Si : 0,1 à 3,50 % Mn : 0,1 à 3,50 % N : jusqu'à 0,020 % S : jusqu'à 0,40 % P : jusqu'à 0,009 % Al : 10,0 à 25,0 % Ti : 0,55 à 10,0 % Cr : jusqu'à 6,0 % Mo : jusqu'à 3,0 % Ni : jusqu'à 4,0 % V : jusqu'à 1,0 % W : jusqu'à 1,0 % Cu : jusqu'à 4,0 % B : jusqu'à 0,08 % Nb : jusqu'à 1,5 %
    le reste étant du fer et des impuretés inévitables liées à la fabrication, la structure de l'acier présentant plus de 85 % volumiques de ferrite ainsi que jusqu'à 10 % volumiques d'austénite et comme reste des teneurs en phases intermétalliques ainsi que des parts de carbure, de nitrure, de bainite ou de perlite.
  2. Acier selon la revendication 1, caractérisé en ce que sa teneur en C est inférieure à 0,02 % massique.
  3. Acier selon l'une des revendications précédentes, caractérisé en ce que pour le rapport %Mn/%S de sa teneur en Mn %Mn et de sa teneur en S %S, la relation %Mn/%S > 2,0 s'applique.
  4. Acier selon l'une des revendications précédentes, caractérisé en ce que la somme de ses teneurs en Ni et en Mn est égale au maximum à 5 % massiques.
  5. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en N est égale au maximum à 0,005 % massique.
  6. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Al est supérieure à 12 % massique et les teneurs en Cr, Mo, Mn, Si, V, W, Ni, Nb, Ti remplissent les conditions suivantes :
    (%Cr + 2*%Mo + %Mn + %Si + %V + %W + %Ni + %Nb + %Ti) > 0,05*%Al
    avec
    %Cr : teneur en Cr de l'acier,
    %Mo : teneur en Mo de l'acier,
    %Mn : teneur en Mn de l'acier,
    %Si : teneur en Si de l'acier,
    %V : teneur en V de l'acier,
    %W : teneur en W de l'acier,
    %Ni : teneur en Ni de l'acier,
    %Nb : teneur en Nb de l'acier,
    %Ti : teneur en Ti de l'acier,
    %Al : teneur en Al de l'acier.
  7. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en B est égale à au moins 0,0005 % massique.
  8. Procédé de fabrication d'un produit plat ou long en acier, comprenant les étapes suivantes
    a) mise à disposition d'un produit semi-fini composé d'un acier formé selon l'une des revendications précédentes, tel qu'une brame, une brame mince, une billette ou un feuillard coulé,
    b) chauffage du produit semi-fini à une température de déformation à chaud de 700 à 1280 °C,
    c) déformation à chaud du produit semi-fini chauffé à la température de déformation à chaud en le produit plat ou long en acier,
    d) traitement thermique optionnel du produit plat ou long en acier obtenu en vue de régler ses propriétés mécaniques.
  9. Procédé selon la revendication 8, caractérisé en ce que la température de déformation à chaud est égale au maximum à 1000 °C.
  10. Procédé selon la revendication 8 ou 9, caractérisé en ce que la teneur en Ti de l'acier est égale au moins à 0,60 % massique et en ce que le produit plat ou long en acier obtenu, à la suite de la déformation à chaud, est refroidi lentement avec une vitesse de refroidissement maximale de 3 K/min.
  11. Procédé selon la revendication 8 ou 9, caractérisé en ce que la teneur en Ti de l'acier est égale au moins à 0,60 % massique et en ce que le produit plat ou long en acier obtenu après la déformation à chaud est refroidi directement à partir de la chaleur de déformation ou après un recuit de mise en solution rapidement avec une vitesse de refroidissement d'au moins 25,0 K/min à une température de 700 à 1250 °C.
  12. Procédé selon la revendication 11, caractérisé en ce que le produit plat ou long en acier est durci par précipitation dans une étape de traitement thermique supplémentaire à des températures de 150 à 700 °C sur une durée de 15 min à 30 heures.
  13. Procédé selon la revendication 11, caractérisé en ce que le produit plat ou long en acier est usiné mécaniquement après le refroidissement rapide.
EP16162652.8A 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier Active EP3225702B1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
EP16162652.8A EP3225702B1 (fr) 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier
ES16162652T ES2791887T3 (es) 2016-03-29 2016-03-29 Acero con densidad reducida y procedimiento para la fabricación de un producto plano de acero o un producto alargado de acero a partir de un acero de este tipo
PCT/EP2017/057359 WO2017167778A1 (fr) 2016-03-29 2017-03-29 Acier de masse volumique réduite et procédé de fabrication d'un produit acier plat ou d'un produit acier allongé réalisé dans un acier de ce type
US16/089,616 US20190119771A1 (en) 2016-03-29 2017-03-29 Steel with Reduced Density and Method for Producing a Flat Steel or Long Steel Product from Such a Steel

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Application Number Priority Date Filing Date Title
EP16162652.8A EP3225702B1 (fr) 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier

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EP3719158B9 (fr) * 2019-04-01 2022-07-27 Deutsche Edelstahlwerke Specialty Steel GmbH & Co. KG Utilisation d'une poudre d'acier, procédé de fabrication d'un composant d'acier selon un procédé de fabrication additive
CN113718161B (zh) * 2021-09-01 2022-04-22 新疆八一钢铁股份有限公司 一种防止20Ni2MoA齿轮钢加工开裂的控制方法

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US20190119771A1 (en) 2019-04-25
EP3225702A1 (fr) 2017-10-04
WO2017167778A1 (fr) 2017-10-05
ES2791887T3 (es) 2020-11-06

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