EP4190934A1 - Composant en acier allié b-zr - Google Patents

Composant en acier allié b-zr Download PDF

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Publication number
EP4190934A1
EP4190934A1 EP21211997.8A EP21211997A EP4190934A1 EP 4190934 A1 EP4190934 A1 EP 4190934A1 EP 21211997 A EP21211997 A EP 21211997A EP 4190934 A1 EP4190934 A1 EP 4190934A1
Authority
EP
European Patent Office
Prior art keywords
steel
weight
component
gew
optional
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
EP21211997.8A
Other languages
German (de)
English (en)
Inventor
Ali SOLIMANI
Matthew GALLER
Robert KIENREICH
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Wire Rod Austria GmbH
Kamax Holding GmbH and Co KG
Original Assignee
Voestalpine Wire Rod Austria GmbH
Kamax Holding GmbH and Co KG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Voestalpine Wire Rod Austria GmbH, Kamax Holding GmbH and Co KG filed Critical Voestalpine Wire Rod Austria GmbH
Priority to EP21211997.8A priority Critical patent/EP4190934A1/fr
Priority to PCT/EP2022/084020 priority patent/WO2023099654A1/fr
Priority to KR1020247015995A priority patent/KR20240089753A/ko
Priority to CA3238223A priority patent/CA3238223A1/fr
Priority to CN202280079461.5A priority patent/CN118339322A/zh
Priority to EP22826100.4A priority patent/EP4247993A1/fr
Publication of EP4190934A1 publication Critical patent/EP4190934A1/fr
Pending legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0087—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for chains, for chain links
    • 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
    • C21D9/0093—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for screws; for bolts
    • 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
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C21D2211/002—Bainite
    • 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
    • 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
    • C21D2211/008—Martensite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a component with a component made of steel, in which the steel is alloyed with boron (hereinafter also "B"), among other things.
  • B boron
  • the invention relates to a fastener such as a screw or a nut.
  • boron is often used as a cost-effective alloying element to improve through-hardenability.
  • Steels alloyed with boron are, for example, in WO 2021/009705 A1 and the WO 2008/142275 A2 described.
  • components made of boron-alloyed steels such as screws or nuts, often show a drop in hardness in the edge area, especially down to a depth of 300 ⁇ m below the surface, which limits the applicability for high-strength and ultra-high-strength products, such as high-strength and ultra-high-strength screws is.
  • Steels that contain boron are usually additionally alloyed with titanium and aluminum in order to keep boron in the dissolved state and not precipitate in the form of nitrides, carbides, carbonitrides, silicides or oxides. However, this is not sufficient to reduce the hardness inhomogeneity in the edge area described above.
  • the object of the present invention is therefore to reduce the drop in hardness in the edge area of components made of a conventional boron-alloyed steel.
  • the composition according to the invention in particular the zirconium added to the B-containing steel in the component according to the invention with a component made of steel, counteracts the drop in hardness in the edge region, in particular when the component made of steel is heat-treated.
  • Another surprising advantage of the component according to the invention with a component made of steel is the improved resistance to hydrogen embrittlement.
  • the zirconium added to the B-containing steel makes it possible to achieve significantly higher strengths, in particular in comparison to B-containing steels with an analogous composition but without zirconium.
  • the invention can thus also relate to a vehicle, an engine, a cylinder head, a chassis arrangement or a battery arrangement with a component according to the invention, in particular a fastening means.
  • the drop in hardness in the edge area of the components can be reduced particularly effectively.
  • the hydrogen embrittlement of the steel is greatly reduced.
  • the components Mo, Ni, Cu and Ca are optional, i.e. they can independently not be included or, if they are included, they can independently be included in the specified amounts of, for example, 0.01 - 0.20% by weight Mo, 0.01 - 0.50% by weight Ni, 0.01 - 0.50% by weight Cu and/or 0.0010 - 0.0100% by weight Ca in the steel.
  • the components Mo, Ni, Cu and Ca are contained in the steel independently of one another.
  • the steel contains 0.01 - 0.20 wt% Mo, 0.01 - 0.50 wt% Ni, 0.01 - 0.50 wt% Cu and/or 0 0.0010 - 0.0100% by weight Ca, more preferably 0.01 - 0.16% by weight Mo, 0.01 - 0.40% by weight Ni, 0.01 - 0.30% by weight -% Cu and/or 0.0010 - 0.0080% by weight Ca.
  • zirconium is a micro-alloying element, ie it develops even in very small quantities, in particular also below of 0.05% by weight has an effect.
  • Boron, titanium and vanadium are also micro-alloying elements.
  • the zirconium acts in conjunction with the other alloying elements. Surprisingly, the zirconium achieves a more homogeneous distribution of the boron in the steel over the entire cross section, in particular a more homogeneous distribution in the edge area as well. The zirconium counteracts the drop in hardness in the edge area in particular and leads to a reduction in hydrogen embrittlement.
  • the drop in hardness in the edge area of the components can be reduced particularly effectively if the ratio of (Zr+Ti+Al) to N is in a range from 2.7 to 150, more preferably 2.8 to 130, particularly preferably 3 to 100.
  • the respective weight percentages of Zr, Ti, Al and N are used in the above formula.
  • the component according to the invention with a component made of steel is preferably a fastening means, particularly preferably selected from the group consisting of screws, nuts, rivets, bolts and chains.
  • a component made of steel within the meaning of the invention can in particular be understood to mean that at least part of the component, ie a volume area, is made of steel. It is preferred that the steel component makes up ⁇ 80% by weight, more preferably ⁇ 90% by weight, particularly preferably ⁇ 95% by weight of the component. This means that the component consists of ⁇ 80% by weight, more preferably ⁇ 90% by weight, particularly preferably ⁇ 95% by weight, of steel. As a result, a particularly good mechanical strength of the component, in particular of the fastening means, can be achieved. In order to increase the mechanical strength, it is particularly preferred if the component made of steel is in one piece. “In one piece” can in particular be understood to mean that at least the one-piece part has been created in a forming process and/or is connected.
  • the component according to the invention is preferably a high-strength or ultra-high-strength component, in particular with strengths of more than 1000 MPa, preferably more than 1200 MPa, particularly preferably 1200-1900 MPa.
  • Preferred high-strength and ultra-high-strength components are high-strength or ultra-high-strength screws, nuts, chain drives, formed components and/or structural components.
  • the component according to the invention in particular the high-strength or ultra-high-strength component, preferably a welded component, an additively manufactured component or a case-hardened component.
  • the component or the steel is heat-treated, a so-called tempering, for example by salt bath tempering, in order to set a preferred microstructure.
  • the structure of the steel is ⁇ 70% by volume, more preferably ⁇ 80% by volume, particularly preferably ⁇ 90% by volume, bainitic and/or martensitic, in particular after tempering such as heat treatment.
  • the proportion of microstructures in volume percent can be determined, for example, in microscopic images of microsections, since the surfaces reflect the volumes on average over several micrographs. For this purpose, the surfaces are determined in several micrographs and the arithmetic mean is formed.
  • the structure of the steel is ⁇ 70% by weight, more preferably ⁇ 80% by weight, particularly preferably ⁇ 90% by weight, bainitic and/or martensitic is.
  • the proportion of austenite (residual austenite) is also preferably ⁇ 20% by volume or weight, in particular ⁇ 10% by volume or weight.
  • This structure gives the component according to the invention particularly high strength and toughness. They can be subjected to high and often dynamic axial stress.
  • the structure of the component according to the invention is preferably ⁇ 90% by volume ferritic and/or pearlitic.
  • the microstructure of the component according to the invention is preferably ⁇ 90% by weight ferritic and/or pearlitic prior to tempering.
  • the component according to the invention is a formed component.
  • a formed component is to be understood in particular as a component which is formed by means of a forming step, in particular a cold forming process became.
  • reducing hydrogen embrittlement is advantageous, because formed components already have a certain degree of brittleness due to the accumulated forest dislocations (e.g. two or more dislocations that run across or perpendicular to one another on different slip planes).
  • This structural component within the meaning of the invention is present in particular when the component is a load-bearing component.
  • This structural component has, in particular, two load application sections, which advantageously have load application structures, such as assembly recesses or openings, and a transmission area arranged between the load application sections, which transfers a load, in particular a bending load and/or tensile load, from one load application section to the other load application section can and/or transmits.
  • the improvement in the resistance to hydrogen embrittlement is attributed to the fact that additional connection points for diffusible hydrogen are created in the microstructure, in particular a heat-treated microstructure of the steel, in particular by precipitation-forming elements such as Al, Cu, Mo, V, Zr, Ti, B with C, N, O, Si and/or due to the structure set by heat treatment.
  • the component according to the invention with a component made of steel is a fastening means in a preferred embodiment.
  • the fastening means according to the invention can in particular be non-positive fastening means such as screws, bolts or nuts.
  • Force-locking fastening means are characterized in particular by the fact that they have a threaded section for bracing or fastening, in particular with an external thread or an internal thread.
  • the threaded section can therefore be an external thread or an internal thread.
  • this threaded portion is introduced into a part of the fastener, which consists of steel is.
  • the fastening means can expediently have a shank area.
  • This shank area can be formed adjacent to the threaded section and/or a drive area, in particular a head, of the fastening means.
  • the shank region can preferably be designed without a thread and/or be designed as a cylindrical section.
  • the diameter of the shank can be larger, smaller or equal to the thread diameter in the threaded section.
  • the screws are advantageously high-strength or ultra-high-strength screws.
  • the component is a high-strength or ultra-high-strength screw.
  • a high-strength bolt is a bolt with a tensile strength of at least 800 MPa.
  • High-strength screws are, for example, screws in strength classes 8.8, 10.9 and 12.9.
  • the strength classes of the invention correspond to ISO 898-1 in the version valid in January 2021.
  • An ultra-high-strength screw is understood to mean a screw with a tensile strength, in particular of at least 1200 MPa and/or advantageously at least 1400 MPa.
  • ultra-high-strength screws are screws in strength classes 12.8, 12.9, 14.8, 14.9, 15.8, 15.9, 16.8, 16.9, 17.8 and 12.8U, 12.9U, 14.8U, 14.9U, 15.8U, 15.9U, 16.8U, 17.8U.
  • a high-strength bolt is a bolt that is at least high-strength, but can also be ultra-high-strength. It is preferably a high-strength or ultra-high-strength screw with a strength of more than 1000 MPa.
  • the screw can have a head with tool gripping surfaces, these tool gripping surfaces in particular forming an internal or external hexagon with one another.
  • the preferred method according to the invention has the advantage of a resource-saving and cost-efficient process route since, for example, a wire rod can be processed directly without GKZ annealing being required in between.
  • a ferrite-pearlite structure can be achieved in the wire rod state by means of TM rolling (thermo-mechanical rolling).
  • Thermomechanical rolling is preferably carried out in step b).
  • Thermomechanical rolling is particularly preferred, in which the material is rolled with a final shape temperature in a range from Ar 3 -50° C. and +100° C., Ar 3 being referred to as the austenite-proeutectoid transformation temperature in the Fe-C diagram.
  • a structure predominantly made of ferrite and pearlite is particularly preferably produced, in particular with an average secondary grain size of 8 or finer according to ASTM E112.
  • step d) the optional GKZ annealing, it is preferred that the steel is annealed for 6-10 hours, for example 8 hours, with a holding temperature of 700-750° C., for example 735° C., and a structure is thus formed Ferrite and nodular cementite is obtained.
  • a tempering step with the known tempering of steels being possible.
  • an annealing step can also take place during and/or at the same time as the heat treatment step. In other words, the tempering and the heating can take place together in one step.
  • the structure of the steel component is after rolling in step b), in particular a thermomechanical rolling, and before the heat treatment in Step f) predominantly ferritic-pearlitic, bainitic and/or a mixed structure.
  • the structure of the steel is preferably ⁇ 80% by volume, particularly preferably ⁇ 90% by volume, ferritic-pearlitic, bainitic and/or a mixed structure.
  • the microstructure of the component is predominantly martensitic and/or bainitic, as described above.
  • the microstructure of the steel component in the component according to the invention is ⁇ 70% by volume, more preferably ⁇ 80% by volume, particularly preferably ⁇ 90% by volume, bainitic or martensitic, as described above.
  • the structure of the steel in the edge area in particular the area from the surface of the steel component to a depth of 15 ⁇ m, preferably up to 12 ⁇ m, particularly preferably up to 10 ⁇ m, measured perpendicularly from the surface of the Component made of steel, is predominantly ferritic and/or pearlitic, preferably ⁇ 80% by volume, particularly preferably ⁇ 90% by volume, ferritic and/or pearlitic.
  • the steel below the depths mentioned above ie below a depth of 15 ⁇ m, preferably below a depth of 12 ⁇ m, particularly preferably below a depth of 10 ⁇ m, preferably has the structure described above, ie preferably ⁇ 70% by volume, more preferably ⁇ 80% by volume, particularly preferably ⁇ 90% by volume, bainitic or martensitic.
  • the steel component has a Vickers hardness of ⁇ 350 HV in the edge region, in particular at a depth of 30-100 ⁇ m, preferably 50-150 ⁇ m, measured from the surface perpendicular to the surface of the steel component 0.5, more preferably ⁇ 400 HV 0.5, particularly preferably ⁇ 430 HV 0.5, in particular ⁇ 450 HV 0.5.
  • the steel component has a Vickers hardness at a depth of 30-100 ⁇ m, preferably 40-120 ⁇ m, particularly preferably 50-150 ⁇ m, measured from the surface perpendicular to the surface of the steel component , which is less than 150 HV 0.5 below the Vickers hardness HV 0.5 of the steel component at a depth of 300-400 ⁇ m, in particular at a depth of 400 ⁇ m, particularly preferably at a depth of 1 ⁇ 4 the diameter of the steel component.
  • the steel component has a Vickers hardness of less than 100 at a depth of 30-100 ⁇ m, preferably 40-120 ⁇ m, more preferably 50-150 ⁇ m, measured from the surface perpendicular to the surface of the steel component HV 0.5, more preferably less than 60 HV 0.5, in particular less than 30 HV 0.5, below the Vickers hardness HV 0.5 of the steel component at a depth of 300-400 ⁇ m, also measured by the surface to the depth of the steel component, perpendicular to the surface of the steel component, in particular at a depth of 400 ⁇ m, particularly preferably at a depth of % of the diameter of the steel component.
  • the invention also relates to a component with a component made of steel, obtainable by the method according to the invention.
  • the component and/or the component made of steel can also have the aforementioned features with regard to the method.
  • the hardness of the steel can be seen as a function of the edge distance, measured perpendicularly to the surface, of a screw according to the invention and it can be seen that there is only a slight drop in hardness.
  • In 2 shows the hardness profile of the steel in the edge area of a bainitic heat-treated B-alloy screw, with a conventional B-alloy steel being used. It can be seen that there is a clear drop in hardness in the edge area in connection with a greater depth of hardness drop, measured perpendicular to the surface of the screw.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP21211997.8A 2021-12-02 2021-12-02 Composant en acier allié b-zr Pending EP4190934A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP21211997.8A EP4190934A1 (fr) 2021-12-02 2021-12-02 Composant en acier allié b-zr
PCT/EP2022/084020 WO2023099654A1 (fr) 2021-12-02 2022-12-01 Élément en acier allié à base de b-zr
KR1020247015995A KR20240089753A (ko) 2021-12-02 2022-12-01 B~Zr 합금강으로 제작된 부품
CA3238223A CA3238223A1 (fr) 2021-12-02 2022-12-01 Element en acier allie a base de b-zr
CN202280079461.5A CN118339322A (zh) 2021-12-02 2022-12-01 由B-Zr合金钢构成的构件
EP22826100.4A EP4247993A1 (fr) 2021-12-02 2022-12-01 Élément en acier allié à base de b-zr

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP21211997.8A EP4190934A1 (fr) 2021-12-02 2021-12-02 Composant en acier allié b-zr

Publications (1)

Publication Number Publication Date
EP4190934A1 true EP4190934A1 (fr) 2023-06-07

Family

ID=78821234

Family Applications (2)

Application Number Title Priority Date Filing Date
EP21211997.8A Pending EP4190934A1 (fr) 2021-12-02 2021-12-02 Composant en acier allié b-zr
EP22826100.4A Pending EP4247993A1 (fr) 2021-12-02 2022-12-01 Élément en acier allié à base de b-zr

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP22826100.4A Pending EP4247993A1 (fr) 2021-12-02 2022-12-01 Élément en acier allié à base de b-zr

Country Status (5)

Country Link
EP (2) EP4190934A1 (fr)
KR (1) KR20240089753A (fr)
CN (1) CN118339322A (fr)
CA (1) CA3238223A1 (fr)
WO (1) WO2023099654A1 (fr)

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008142275A2 (fr) 2007-04-12 2008-11-27 Arcerlormittal Gandrange Acier micro-allié à bonne tenue à l'hydrogène pour le formage à froid de pièces mécaniques à hautes caractéristiques
EP2484789A1 (fr) * 2009-10-02 2012-08-08 Kabushiki Kaisha Kobe Seiko Sho Acier pour construction de machines et son procédé de fabrication, composants en acier cémenté et leur procédé de fabrication
EP2546380A1 (fr) * 2010-03-11 2013-01-16 Nippon Steel Corporation Acier à haute résistance et boulon à haute résistance dotés d'une excellente résistance à la rupture différée et leur procédé de fabrication
EP3078758A1 (fr) * 2013-12-02 2016-10-12 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Fil d'acier pour boulon, boulon, et leur procédé de production
WO2021009705A1 (fr) 2019-07-16 2021-01-21 Arcelormittal Procédé de production d'une pièce en acier, et pièce en acier

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008142275A2 (fr) 2007-04-12 2008-11-27 Arcerlormittal Gandrange Acier micro-allié à bonne tenue à l'hydrogène pour le formage à froid de pièces mécaniques à hautes caractéristiques
EP2484789A1 (fr) * 2009-10-02 2012-08-08 Kabushiki Kaisha Kobe Seiko Sho Acier pour construction de machines et son procédé de fabrication, composants en acier cémenté et leur procédé de fabrication
EP2546380A1 (fr) * 2010-03-11 2013-01-16 Nippon Steel Corporation Acier à haute résistance et boulon à haute résistance dotés d'une excellente résistance à la rupture différée et leur procédé de fabrication
EP3078758A1 (fr) * 2013-12-02 2016-10-12 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Fil d'acier pour boulon, boulon, et leur procédé de production
WO2021009705A1 (fr) 2019-07-16 2021-01-21 Arcelormittal Procédé de production d'une pièce en acier, et pièce en acier

Also Published As

Publication number Publication date
EP4247993A1 (fr) 2023-09-27
WO2023099654A1 (fr) 2023-06-08
CA3238223A1 (fr) 2023-06-08
KR20240089753A (ko) 2024-06-20
CN118339322A (zh) 2024-07-12

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