WO2025003736A1 - Steel sheet and high strength press hardened steel part having excellent bending anisotropy and method of manufacturing the same - Google Patents

Steel sheet and high strength press hardened steel part having excellent bending anisotropy and method of manufacturing the same Download PDF

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Publication number
WO2025003736A1
WO2025003736A1 PCT/IB2023/056848 IB2023056848W WO2025003736A1 WO 2025003736 A1 WO2025003736 A1 WO 2025003736A1 IB 2023056848 W IB2023056848 W IB 2023056848W WO 2025003736 A1 WO2025003736 A1 WO 2025003736A1
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WIPO (PCT)
Prior art keywords
steel
steel sheet
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inclusions
blank
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.)
Ceased
Application number
PCT/IB2023/056848
Other languages
French (fr)
Inventor
Sebastian Cobo
Guillaume STECHMANN
Matthieu SALIB
Emmanuel Lucas
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.)
ArcelorMittal SA
Original Assignee
ArcelorMittal SA
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 ArcelorMittal SA filed Critical ArcelorMittal SA
Priority to PCT/IB2023/056848 priority Critical patent/WO2025003736A1/en
Priority to CN202511040116.2A priority patent/CN121496286A/en
Priority to DE202024001581.5U priority patent/DE202024001581U1/en
Priority to EP24726970.7A priority patent/EP4469612A1/en
Priority to CN202511040112.4A priority patent/CN121065590A/en
Priority to KR1020247028272A priority patent/KR20250005057A/en
Priority to CA3316187A priority patent/CA3316187A1/en
Priority to MX2024010231A priority patent/MX2024010231A/en
Priority to PCT/IB2024/054085 priority patent/WO2024171173A1/en
Priority to CA3316203A priority patent/CA3316203A1/en
Priority to CN202511041559.3A priority patent/CN121137474A/en
Priority to CN202511040118.1A priority patent/CN121204554A/en
Priority to CN202480001638.9A priority patent/CN118786237B/en
Priority to JP2024549668A priority patent/JP7804090B2/en
Priority to CA3316174A priority patent/CA3316174A1/en
Priority to CA3253193A priority patent/CA3253193A1/en
Priority to ZA2024/06317A priority patent/ZA202406317B/en
Priority to US18/811,384 priority patent/US12312661B2/en
Priority to US18/988,516 priority patent/US12428711B2/en
Priority to US18/988,468 priority patent/US12404571B2/en
Publication of WO2025003736A1 publication Critical patent/WO2025003736A1/en
Priority to JP2025072071A priority patent/JP2025118699A/en
Priority to US19/295,461 priority patent/US20250361588A1/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/064—Dephosphorising; Desulfurising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving particular fabrication steps or treatments of ingots or slabs
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0242—Flattening; Dressing; Flexing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment 
    • C—CHEMISTRY; METALLURGY
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    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • 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
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
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    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
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    • 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
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    • 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
    • C21D2211/004—Dispersions; Precipitations
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    • 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
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    • 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

Definitions

  • the present invention relates to steel sheets and to high strength press hardened steel parts.
  • High strength press-hardened parts can be used as structural elements in automotive vehicles for anti-intrusion or energy absorption functions.
  • This weight reduction can be achieved in particular thanks to the use of steel parts with a predominantly martensitic microstructure.
  • the purpose of the current invention is to address the above-mentioned challenge and to provide a press hardened steel part having a combination of high mechanical properties with a tensile strength after hot stamping above or equal to 1300 MPa and a very small anisotropy in bending angle between the rolling direction and the transverse direction.
  • Another purpose of the invention is to provide a steel sheet that can be transformed by hot forming into such a press hardened steel part and to provide a process to manufacture such a steel sheet.
  • the object of the present invention is achieved by providing a steel sheet according to claim 1 , optionally having the features of claim 2 to 4. Another object of the present invention is achieved by providing a press hardened steel part according to claim 5. The steel part can also comprise characteristics of claim 6 to 7. A further object of the present invention is a manufacturing method for said hot stamped part according to claim 8, optionally comprising the characteristics of claim 9.
  • Figure 1 is a schematic cross section of a steel sheet according to the invention.
  • a blank of steel refers to a flat sheet of steel, which has been cut to any shape suitable for its use.
  • a blank has a top and bottom face, which are also referred to as a top and bottom side or as a top and bottom surface. The distance between said faces is designated as the thickness of the blank.
  • the thickness can be measured for example using a micrometer, the spindle and anvil of which are placed on the top and bottom faces. In a similar way, the thickness can also be measured on a formed part.
  • Hot stamping is a forming technology which involves heating a blank up to a temperature at which the microstructure of the steel has at least partially transformed to austenite, forming the blank at high temperature by stamping it and quenching the formed part to obtain a microstructure having a very high strength. Hot stamping allows to obtain very high strength parts with complex shapes and presents many technical advantages.
  • the thermal treatment to which a part is submitted includes not only the above-described thermal cycle of the hot stamping process itself, but also possibly other subsequent heat treatment cycles such as for example the paint baking step, performed after the part has been painted in order to cure the paint.
  • the mechanical properties of hot stamped parts below are those measured after the full thermal cycle, including optionally for example a paint baking step, in case paint baking has indeed been performed.
  • the ultimate tensile strength is measured according to ISO standard ISO 6892-1 , published in October 2009.
  • the tensile test specimens are cut-out from flat areas of the hot stamped part. If necessary, small size tensile test samples are taken to accommodate for the total available flat area on the part.
  • the bending angle is measured according to the VDA-238-100 bending standard, according to the version published in June 2017. The bending angle was measured using a laser measurement device.
  • the samples are cut-out from flat areas of the part. If necessary, small size samples are taken to accommodate for the total available flat area on the part.
  • the bending angle of a part is representative of the ability of the part to resist deformation without the formation of cracks.
  • the bending angle is measured in the rolling direction (RD), i.e. the direction along which the steel sheet travelled during the hot-rolling step, and in the transverse direction (TD), i.e. at a 90° orientation compared to the rolling direction.
  • the bending anisotropy is defined as the absolute value of the difference between the bending angle measured on a given sample in the rolling direction and in the transverse direction.
  • the rolling direction on the hot stamped part is not known, it can be determined using Electron Back-Scattered Diffraction (EBSD) analysis across the section of the sample in a Scanning Electron Microscope (SEM).
  • ODF Orientation Density Function
  • compositions are given in terms of a lower and upper limit of the composition range, said limits being comprised within the possible composition range according to the invention.
  • the present invention also discloses all possible combinations of these preferred ranges for each individual element.
  • the carbon ranges from 0.2% to 0.4% to ensure a satisfactory strength. Above 0.4% of carbon, weldability and bendability of the steel sheet may be reduced. If the carbon content is lower than 0.2%, the tensile strength will not reach the targeted value. In a specific embodiment, the carbon ranges from 0.2% to 0.3%, in order to ensure sufficient strength while further controlling excellent weldability and bendability. In a specific embodiment, the carbon ranges from 0.2% to 0.25%, in order to ensure sufficient strength while even further controlling excellent weldability and bendability.
  • the manganese content ranges from 0.8% to 2.0 %. Above 2.0% of addition, the risk of MnS formation is increased to the detriment of the bendability. Below 0.8% the hardenability of the steel sheet during the hot stamping process is reduced. In a specific embodiment, the manganese content ranges from 1.0% to 1.4 % in order to further improve the hardenability of the steel and further limit the formation of MnS, thus improving bendability.
  • the silicon content ranges from 0.1 % to 0.5%. Silicon is an element participating in the hardening in solid solution. Silicon is added to limit carbides formation. Above 0.5%, silicon oxides form at the surface, which impairs the coatability of the steel. Moreover, the weldability of the part produced with said steel sheet may be reduced. In a specific embodiment, the silicon content ranges from 0.1 % to 0.4 % in order to further improve coatability and weldability. In a specific embodiment, the silicon content ranges from 0.15% to 0.35% in order to further harden the steel and further improve coatability and weldability.
  • the Aluminum content ranges from 0.01 % to 0.1 % as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration.
  • Aluminum can protect boron if titanium content is not sufficient.
  • the Aluminum content is lower than 0.1 % to avoid oxidation problems and ferrite formation during press hardening.
  • Preferably the Aluminum content ranges from 0.02% to 0.06% to further ensure good deoxidization of the steel in the liquid phase while further avoiding oxidation problems and ferrite formation during press hardening.
  • the titanium content ranges from 0.01 % to 0.1 % in order to protect boron, which would otherwise be trapped within BN precipitates. Titanium content is limited to 0.1 % to avoid excess TiN formation. In a specific embodiment, Ti content ranges from 0.02% to 0.06% in order to further protect boron while further avoiding excess TiN formation.
  • the boron content ranges from 0.0005% to 0.005%. Boron improves the hardenability of the steel.
  • the boron content is not higher than 0.005% to avoid slab breaking issues during continuous casting.
  • the boron content ranges from 0.002% to 0.004% in order to further ensure the hardenability of the steel and further avoid slab breaking issues.
  • Phosphorous is controlled to below 0.040%, because it leads to fragility and weldability issues.
  • the P content is controlled to below 0.020% to further avoid fragility and weldability issues.
  • Calcium is controlled to below 0.01 % because the presence of Calcium in the liquid steel can lead to the formation of coarse inclusions which are detrimental to bendability.
  • the Ca content is controlled to below 0.005% to further avoid coarse inclusions issues.
  • Sulphur is controlled to below 0.006% because the presence of Sulphur in the liquid steel can lead to the formation of MnS precipitates which are detrimental to bendability.
  • the S content is controlled to below 0.005% to further avoid the formation of MnS precipitates.
  • Nitrogen is controlled to below 0.01 % preferentially below 0.008% even more preferentially below 0.005%.
  • the presence of Nitrogen can lead to the formation of precipitates such as TiN or TiNbCN, which are detrimental to the bendability.
  • Chromium is optionally added up to 0.4%. Chromium can be used to provide strength by solid solution hardening and to improve the hardenability of the steel sheet during hot stamping. Chromium is limited to 0.4% to limit costs and avoid processing issues. Molybdenum is optionally added up to 0.3%. Molybdenum improves the hardenability of the steel. Molybdenum is limited to 0.3% to limit costs and avoid processing issues.
  • Niobium is optionally added up to 0.1 %. Niobium improves ductility of the steel. Niobium is limited to 0.1 % to limit costs and avoid processing issues.
  • Vanadium is optionally added up to 0.3%. Vanadium improves the hardenability of the steel. Vanadium is limited to 0.3% to limit costs and avoid processing issues.
  • the chemical composition is further controlled so that the following condition is verified:
  • the inventors have found that this allowed to further control the inclusion population of the steel sheet and therefore further improve bendability and bending anisotropy.
  • the remainder of the composition of the steel is iron and impurities resulting from the elaboration process.
  • the level of impurities resulting from the elaboration process will depend on the production route used and the level of scrap used in the steel melt. For example, when using a Basic oxygen furnace route with a low level of steel scrap (recycled steel), the level of impurities will remain very low. It is however also possible to add a high amount of scrap in the converter to the pig iron produced in the basic oxygen furnace, which will increase the level of impurities. Furthermore, when elaborating the steel using an electric furnace for example, with a very high ratio of recycled scrap steel, the level of impurities will be significantly increased.
  • the level of Cu can go up to 0.25%
  • Ni can go up to 0.25%
  • Sn can go up to 0.05%
  • Sb can go up to 0.03%
  • Pb can go up to 0.03%.
  • the steel sheet has a microstructure comprising in surface fraction on any analyse cross section:
  • the rest being comprised of carbides FesC and hard phases such as martensite and bainite.
  • the steel sheet 1 according to the invention comprises a bulk portion 3 and a top and bottom skin layer 2.
  • the skin layers 2 occupy the outermost 10% of the thickness on either sides of the bulk and the bulk of the steel sheet represents 80% of the steel sheet thickness.
  • the inventors have found that there is a correlation between the bending anisotropy and the inclusion population in the bulk portion of the steel sheet. In particular, it is possible to limit the bending anisotropy to less than or equal to 7° when controlling the sum of the clustering indexes of MnS and TiN /Ti(C,N) inclusions in the bulk portion of the steel to below 300pm/mm 2 .
  • the cross-sections of the steel sheet on which the inclusions are observed are taken in the rolling direction of the steel.
  • the plane of the observed cross section has the transverse direction as its normal direction.
  • the inclusions present in the steel sheet have been characterized using a Scanning Electron Microscope (SEM) with Field Effect Gun (FEG).
  • SEM Scanning Electron Microscope
  • FEG Field Effect Gun
  • a Tescan Mira 3 SEM was used at a 14kV power setting. This allows to detect particles as small as 0.5 pm.
  • Using a FEG SEM setup allows to obtain stable images with an excellent resolution over a long period of time, which can be necessary for completing image analysis over broad areas - using a FEG SEM setup it is possible to acquire image fields during up to 48 hours which can be necessary for multi samples analysis.
  • EDS Energy Dispersive Spectrometry
  • a 120mm 2 Broker EDS probe having large active surface was used in order to detect light elements (0, N) and to get a high count rate and thus allow a precise quantification.
  • the phi-rho-Z method was used to obtain an accurate quantification.
  • the Automated Steel Cleanliness Analysis Tool (ASCAT) of the RJ Lee group is used to pilot the SEM & associated EDS, based on Computer Control Scanning Electron Microscopy technologies.
  • Six individual samples can be analysed in the same batch.
  • the sample surface is divided in three areas (Top skin, bottom skin, bulk, as described previously). Each area is divided in fields. In each field, inclusions are detected.
  • the scanning pixel size is set to the very low value of 0.11 pm. This is in order to reduce matrix noise of SEM images.
  • a first selection of objects which will be termed particles, is made by selecting objects forming a solid and having a grey level, on a scale of 0 to 255, either below 150 or above 220 (the extreme values are excluded).
  • a zoom is then made on each individual particle to catch their morphological features and to perform an EDS analysis.
  • a database of all particles is created using ASCAT and taking into account, for all acquired images, the chemical and morphological features of all analysed particles.
  • each inclusion is then classified in one of the following families: TiN, alumina, Complex oxides, Oxysulfide particles, MnS and others.
  • table 1 details the precise rules that were used by the inventors to classify MnS and TiN I Ti(C, N) inclusions.
  • Oxygen quantification is made possible by high performance EDS detectors. The oxygen level is checked in order to separate TiN from TiO2 and MnS from complex oxysulfide inclusions.
  • the clustering index calculation method is based on the DBSCAN (for Density-Based Spatial Clustering of Applications with Noise) algorithm, as detailed in the article “A density-based algorithm for discovering clusters in large spatial databases with noise”, Ester, Martin; Kriegel, Hans-Peter; Sander, Jorg; Xu, Xiaowei (1996), in Proceedings of the Second International Conference on Knowledge Discovery and Data Mining (KDD-96). AAAI Press, pp. 226-231.
  • a cluster is characterized by the following features:
  • the inclusions are all at a distance inferior to Max_distance from at least one other inclusion
  • Min_it comprises a number of individual inclusions equal to or greater than Min_points.
  • the inventors have found that a good detection of clusters is obtained with a maximum distance Max_distance of 30 pm and a minimum number of inclusions per cluster Min_points of 4.
  • the length L of a given cluster is computed in the following way: -the convex hull of the cluster is first determined using a known algorithm (see for example the chapter “Convex Hulls: Basic Algorithms” In: Computational Geometry, Preparata, F.P., Shamos, M.I., 1985, Texts and Monographs in Computer Science. Springer, New York, NY)
  • Dmax The maximum Feret diameter of said convex hull, which will be termed Dmax, is then determined and the Feret diameter taken in the perpendicular direction to Dmax, which will be termed Dperp, is also determined.
  • Dperp the Feret diameter taken in the perpendicular direction to Dmax
  • the clusters density C_density of a given type of inclusion is the number of clusters per mm 2 .
  • the cluster index is expressed in pm/mm 2 The inventors have found that said cluster index allows to compare samples having different characteristics using a unique number and that it is well correlated to the bending behaviour of said samples.
  • the steel sheet according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the below described steps.
  • ladle refers to the vessel used to contain the liquid steel during the refining process.
  • the refining process is referred to as the step at which the final chemical composition and temperature of the melt is adjusted before casting the steel into its first solidified form (for example before casting it into slabs, which will subsequently be hot rolled).
  • said liquid steel is tapped into the ladle from the previous steelmaking process step.
  • said previous process step is the electric arc furnace process itself.
  • said previous process step is the converter.
  • the Sulphur content of the liquid steel before the refining step is measured, for example by taking a sample of said liquid steel and analysing it using a spark spectrometer. Said sulphur content is for example measured by sampling directly the liquid steel in the ladle or by taking a sample when the liquid steel is being tapped into said ladle. Said sulphur content before the refining step, measured in weight%, will be termed S_start in the following description.
  • Al_added The amount of Al added in the liquid steel at the beginning of the refining process, expressed in kg of aluminium per ton of liquid steel (kg/ton), will be termed Al_added in the following description.
  • the liquid steel is reheated by aluminothermic heating. This is performed by adding a determined amount of aluminium and jointly blowing into the liquid steel a determined amount of oxygen, corresponding to the stoichiometric ratio necessary to form AI2O3 with the added aluminium.
  • the strongly exothermal reaction between Al and O2 allows to increase the temperature of the liquid steel.
  • C>2_inj The amount of O2 injected during this optional step will be termed C>2_inj and is expressed in Normal cubic meters of O2 per ton of liquid steel (Nm 3 /ton). Since there is a direct stochiometric relationship between the C>2_inj and the associated Al injection for aluminothermic re-heating, said amount of injected Al for aluminothermy will not be considered separately in the current description. It should be noted that said injected Al for aluminothermy is distinct from the previously mentioned Al_added.
  • the slag composition above the melt is adjusted by adding the appropriate amount of minerals in order to ensure that the ratio %CaO I %Al2Os of the slag is above 1 , that the amount of slag per ton of liquid steel is at least 10kg/ton of liquid steel and that the slag remains liquid in order to promote chemical exchanges with the steel, to be able to access the steel below the slag and to be able to tap the steel and I or the slag separately (the liquid state of the slag is verified visually and I or using thermodynamic rules based on its composition and temperature),
  • the liquid steel is stirred by blowing an inert gas, for example by blowing Ar, within the liquid steel. This is done in order to promote the exchanges between the liquid steel and the slag, which will allow to lower the sulphur content of the liquid steel.
  • an inert gas for example by blowing Ar
  • Ca is added to the ladle in order to globularise the inclusions present within the liquid steel.
  • Ca is added in the form of Silicon Calcium (SiCa) or in the form of Ferro-calcium (FeCa), or as pure Calcium.
  • SiCa or FeCa is added to the ladle in the form of a cored wire - advantageously, this allows to easily control the amount of Ca added by controlling the length and the injection speed of cored wire inserted into the melt.
  • the amount of Ca added in the liquid steel, measured in weight% within the liquid steel, will be termed Ca_added in the following description.
  • -Said heats are processed using different refining process parameters, in particular different levels of measured Sulphur at the beginning of the refining process, Al addition at the beginning of the refining process, Ca addition during the refining process and volume of O2 blowing.
  • the ranges of tested refining process parameters are chosen so as to be representative of the industrial variation of these parameters. For example, a set of 6 different heats with 6 different sets of refining process parameters is chosen. For example, a set of 8 different heats with 8 different sets of refining process parameters is chosen.
  • a cut-off value is determined below which the sum of clustering indexes of MnS and TiN / Ti(C, N) inclusions in the bulk portion of the steel sheets is lower than 300pm/mm 2 .
  • Said cut-off value of combination C1 will determine how to control the refining process for the specific industrial installation that is being considered.
  • C1 By controlling C1 below said cut-off value, it will be possible to produce steel sheets having a sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion below 300pm/mm 2 and thus to reach the associated excellent bending anisotropy of less than or equal to 7°.
  • said cut-off value is equal to 1.80.
  • the method for manufacturing the steel sheet according to the present invention preferably comprises the following steps:
  • the semi-products are slabs produced in a continuous sequence by casting in a mold the product of multiple heats poured into a tundish, specific refractories and linings can be used in the tundish, specific allocation rules can be used for first of sequence slabs and transient slabs between two different heats, etc.
  • the semi product is then optionally reheated at a temperature comprised from 1150°C to 1300°C.
  • the steel sheet is then hot rolled at a finish hot rolling temperature comprised from 800°C to 950°C.
  • the hot-rolled steel is then cooled and coiled at a temperature Tcoii lower than 670°C, and optionally pickled to remove oxidation.
  • the coiled steel sheet is then optionally cold rolled to obtain a cold rolled steel sheet.
  • the cold-rolling reduction ratio preferably ranges from 20% to 80%. Below 20%, the recrystallization during subsequent heat-treatment is not favored, which may impair the ductility of the steel sheet. Above 80%, there is a risk of edge cracking during cold rolling.
  • the steel sheet is heated in an annealing furnace to a soaking temperature comprised from 700°C to 850°C and maintained at said soaking temperature for a soaking time comprised from 10 seconds to 20 minutes.
  • the thus annealed steel sheet is cooled to a temperature range from 400°C to 700°C and further coated with a metallic coating.
  • Said metallic coating is for example an aluminum based metallic coating comprising at least 50% of aluminum in weight.
  • Said metallic coating is for example a zinc based metallic coating comprising at least 50% of zinc in weight.
  • the steel sheet is then cooled to room temperature.
  • Said cut-off value having been determined for the specific industrial equipment which is being used so that when C1 is below the cut-off value, the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel is below 300pm/mm 2 .
  • a steel blank is cut out of the steel sheet according to the invention and heated in an austenitizing furnace.
  • the steel blank is heated to a temperature comprised from 880°C to 950°C during 10 seconds to 15 minutes to obtain a heated steel blank.
  • the heated blank is then transferred to a forming press before being hot formed and die-quenched to obtain a pressed part.
  • the hot stamped part is further submitted to a paint baking step in which the part is heated to a temperature between 150°C and 250°C for a duration of 10 minutes to 2 hours.
  • the microstructure of the pressed part comprises in surface fraction on any analysed cross-section, more than 95% of martensite and less than 5% of bainite + ferrite. Furthermore, the pressed part according to the invention comprises a bulk portion and a top and bottom skin layer, wherein the skin layers occupy the outermost 10% of the thickness on either side of the bulk. Said bulk portion has a sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions below 300pm/mm 2 .
  • the pressed part according to the invention has a tensile strength above 1300MPa, preferably above 1350MPa, preferably above 1400MPa, and a bending angle anisotropy less than or equal to 7°.
  • a high tensile strength and low bending anisotropy confer to said part a very good mechanical resistance, especially in the case of a crash and further allows to have very predictable and uniform behaviours in all directions. These characteristics afford a very good energy absorption capacity and anti-intrusion capacity in all direction, thereby increasing the safety of the vehicle.
  • All the produced samples have followed the same industrial production process in the steel shop. All samples have been coated after annealing using an AlSi based coating containing 8 - 12wt% Si, 2 - 4wt% Fe, the balance being Al.
  • the tested compositions are gathered in the following table wherein the element contents are expressed in weight percent, the remainder of the composition being iron and unavoidable impurities resulting from the elaboration process:
  • the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel can be controlled to below 300 pm/mm 2 by ensuring that the refining process parameters are appropriately controlled to keep C1 equal to or lower than 1.80.
  • this cut-off value of 1.80 is specific to the industrial setup on which the trials were performed and the appropriate cut-off factor for a given industrial setup will need to be determined, for example by following the above-described methodology.
  • Table 5 shows that the samples according to the invention have a tensile strength above 1300MPa (both in RD and TD) while having a bending anisotropy which is below 7°.
  • the reference samples while having comparable tensile strength levels above 1300MPa, have a bending anisotropy which is above 7°.
  • the inventors have found that this very good bending anisotropy is correlated to the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel, as can be seen in table 3.
  • a higher sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel results in a higher bending anisotropy.
  • a cut-off value of 300 pm/mm 2 allows to control the bending anisotropy to below 7°. With this very low level of bending anisotropy, the behavior of the hot stamped part will be very homogeneous when submitted to loads coming from any direction. This very stable behavior of the hot stamped part under load allows for a simplified design of parts, for example in the case of automotive parts and ensures very good, robust and stable crash worthiness of the hot stamped part.

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Abstract

Steel sheet having a chemical composition comprising in wt% C : 0.2 - 0.4%, Mn : 0.8 - 2.0%, Si : 0.1 - 0.5 %, Al : 0.01 - 0.1 %, Ti: 0.01 - 0.1 %, B: 0.0005 - 0.005 %, P <≤ 0.040 %, Ca ≤ 0.01 %, S ≤ 0.006 %, N ≤ 0.01 %, Said steel sheet comprising from the bulk to the surface of the coated steel sheet a bulk and a skin layer occupying the outermost 10% of the thickness on either side of the bulk, said bulk comprising an inclusion population wherein the sum of clustering indexes of MnS and TiN / Ti(C,N) inclusions is less than or equal to 300μm/mm2. This allows to manufacture hot pressed parts having a tensile strength equal to or greater than 1300MPa and a bending anisotropy equal to or lower than 7°.

Description

Steel sheet and high strength press hardened steel part having excellent bending anisotropy and method of manufacturing the same
The present invention relates to steel sheets and to high strength press hardened steel parts.
High strength press-hardened parts can be used as structural elements in automotive vehicles for anti-intrusion or energy absorption functions.
In such type of applications, it is desirable to produce steel parts that combine high mechanical strength and high impact resistance. Moreover, one of the major challenges in the automotive industry is to decrease the weight of vehicles in order to improve their fuel efficiency in view of the global environmental conservation, without neglecting the safety requirements.
This weight reduction can be achieved in particular thanks to the use of steel parts with a predominantly martensitic microstructure.
It is challenging to produce very high strength steels which also have a good and uniform resistance to the formation of cracks under bending. Indeed, very high strength steels tend to crack early on when submitted to a bending load. This is detrimental to the crash worthiness of a part produced with such high strength steel, because even though the material is able to withstand very high loads thanks to its high tensile strength, once cracks start to appear in the part, these cracks will quickly propagate under the continued load and the part will fail prematurely.
In particular, it is challenging to produce very high strength press hardened steels having an isotropic bending behavior. Indeed, it is well known that generally speaking the bending behavior of a steel sheet is better in the rolling direction than in the transverse direction. This anisotropic behavior introduces constraints when designing steel parts and when conceiving the hot stamping process. It is therefore very interesting to provide a steel sheet and a method to produce such steel which allows to reach very similar bending behavior in all directions.
The purpose of the current invention is to address the above-mentioned challenge and to provide a press hardened steel part having a combination of high mechanical properties with a tensile strength after hot stamping above or equal to 1300 MPa and a very small anisotropy in bending angle between the rolling direction and the transverse direction.
Another purpose of the invention is to provide a steel sheet that can be transformed by hot forming into such a press hardened steel part and to provide a process to manufacture such a steel sheet.
The object of the present invention is achieved by providing a steel sheet according to claim 1 , optionally having the features of claim 2 to 4. Another object of the present invention is achieved by providing a press hardened steel part according to claim 5. The steel part can also comprise characteristics of claim 6 to 7. A further object of the present invention is a manufacturing method for said hot stamped part according to claim 8, optionally comprising the characteristics of claim 9.
The invention will now be described in detail and illustrated by examples without introducing limitations, and referring to Figure 1 , which is a schematic cross section of a steel sheet according to the invention.
A blank of steel refers to a flat sheet of steel, which has been cut to any shape suitable for its use. A blank has a top and bottom face, which are also referred to as a top and bottom side or as a top and bottom surface. The distance between said faces is designated as the thickness of the blank. The thickness can be measured for example using a micrometer, the spindle and anvil of which are placed on the top and bottom faces. In a similar way, the thickness can also be measured on a formed part.
Hot stamping is a forming technology which involves heating a blank up to a temperature at which the microstructure of the steel has at least partially transformed to austenite, forming the blank at high temperature by stamping it and quenching the formed part to obtain a microstructure having a very high strength. Hot stamping allows to obtain very high strength parts with complex shapes and presents many technical advantages. It should be understood that the thermal treatment to which a part is submitted includes not only the above-described thermal cycle of the hot stamping process itself, but also possibly other subsequent heat treatment cycles such as for example the paint baking step, performed after the part has been painted in order to cure the paint. The mechanical properties of hot stamped parts below are those measured after the full thermal cycle, including optionally for example a paint baking step, in case paint baking has indeed been performed.
The ultimate tensile strength is measured according to ISO standard ISO 6892-1 , published in October 2009. The tensile test specimens are cut-out from flat areas of the hot stamped part. If necessary, small size tensile test samples are taken to accommodate for the total available flat area on the part.
The bending angle is measured according to the VDA-238-100 bending standard, according to the version published in June 2017. The bending angle was measured using a laser measurement device. When performing bending tests on hot stamped part, the samples are cut-out from flat areas of the part. If necessary, small size samples are taken to accommodate for the total available flat area on the part.
The bending angle of a part is representative of the ability of the part to resist deformation without the formation of cracks.
The bending angle is measured in the rolling direction (RD), i.e. the direction along which the steel sheet travelled during the hot-rolling step, and in the transverse direction (TD), i.e. at a 90° orientation compared to the rolling direction. The bending anisotropy is defined as the absolute value of the difference between the bending angle measured on a given sample in the rolling direction and in the transverse direction.
If the rolling direction on the hot stamped part is not known, it can be determined using Electron Back-Scattered Diffraction (EBSD) analysis across the section of the sample in a Scanning Electron Microscope (SEM). The rolling direction is determined according to the intensity of the Orientation Density Function (ODF) representative of the major fibers at <p2 = 45°, where <p2 is the Euler angle as defined in “H.-J. Bunge: Texture Analysis in Materials Science - Mathematical Methods. 1 st English Edition by Butterworth Co (Publ.) 1982” (see Figures 2.2 and 2.3 for the definition of cp2). The composition of the steel according to the invention will now be described, the content being expressed in weight percent. The chemical compositions are given in terms of a lower and upper limit of the composition range, said limits being comprised within the possible composition range according to the invention. In the case when preferred ranges for a given element are disclosed, the present invention also discloses all possible combinations of these preferred ranges for each individual element.
According to the invention the carbon ranges from 0.2% to 0.4% to ensure a satisfactory strength. Above 0.4% of carbon, weldability and bendability of the steel sheet may be reduced. If the carbon content is lower than 0.2%, the tensile strength will not reach the targeted value. In a specific embodiment, the carbon ranges from 0.2% to 0.3%, in order to ensure sufficient strength while further controlling excellent weldability and bendability. In a specific embodiment, the carbon ranges from 0.2% to 0.25%, in order to ensure sufficient strength while even further controlling excellent weldability and bendability.
The manganese content ranges from 0.8% to 2.0 %. Above 2.0% of addition, the risk of MnS formation is increased to the detriment of the bendability. Below 0.8% the hardenability of the steel sheet during the hot stamping process is reduced. In a specific embodiment, the manganese content ranges from 1.0% to 1.4 % in order to further improve the hardenability of the steel and further limit the formation of MnS, thus improving bendability.
The silicon content ranges from 0.1 % to 0.5%. Silicon is an element participating in the hardening in solid solution. Silicon is added to limit carbides formation. Above 0.5%, silicon oxides form at the surface, which impairs the coatability of the steel. Moreover, the weldability of the part produced with said steel sheet may be reduced. In a specific embodiment, the silicon content ranges from 0.1 % to 0.4 % in order to further improve coatability and weldability. In a specific embodiment, the silicon content ranges from 0.15% to 0.35% in order to further harden the steel and further improve coatability and weldability.
According to the invention, the Aluminum content ranges from 0.01 % to 0.1 % as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration. Aluminum can protect boron if titanium content is not sufficient. The Aluminum content is lower than 0.1 % to avoid oxidation problems and ferrite formation during press hardening. Preferably the Aluminum content ranges from 0.02% to 0.06% to further ensure good deoxidization of the steel in the liquid phase while further avoiding oxidation problems and ferrite formation during press hardening.
According to the invention, the titanium content ranges from 0.01 % to 0.1 % in order to protect boron, which would otherwise be trapped within BN precipitates. Titanium content is limited to 0.1 % to avoid excess TiN formation. In a specific embodiment, Ti content ranges from 0.02% to 0.06% in order to further protect boron while further avoiding excess TiN formation.
According to the invention, the boron content ranges from 0.0005% to 0.005%. Boron improves the hardenability of the steel. The boron content is not higher than 0.005% to avoid slab breaking issues during continuous casting. In a specific embodiment, the boron content ranges from 0.002% to 0.004% in order to further ensure the hardenability of the steel and further avoid slab breaking issues.
Phosphorous is controlled to below 0.040%, because it leads to fragility and weldability issues. In a specific embodiment, the P content is controlled to below 0.020% to further avoid fragility and weldability issues.
Calcium is controlled to below 0.01 % because the presence of Calcium in the liquid steel can lead to the formation of coarse inclusions which are detrimental to bendability. In a specific embodiment, the Ca content is controlled to below 0.005% to further avoid coarse inclusions issues.
Sulphur is controlled to below 0.006% because the presence of Sulphur in the liquid steel can lead to the formation of MnS precipitates which are detrimental to bendability. In a specific embodiment, the S content is controlled to below 0.005% to further avoid the formation of MnS precipitates.
Nitrogen is controlled to below 0.01 % preferentially below 0.008% even more preferentially below 0.005%. The presence of Nitrogen can lead to the formation of precipitates such as TiN or TiNbCN, which are detrimental to the bendability.
Chromium is optionally added up to 0.4%. Chromium can be used to provide strength by solid solution hardening and to improve the hardenability of the steel sheet during hot stamping. Chromium is limited to 0.4% to limit costs and avoid processing issues. Molybdenum is optionally added up to 0.3%. Molybdenum improves the hardenability of the steel. Molybdenum is limited to 0.3% to limit costs and avoid processing issues.
Niobium is optionally added up to 0.1 %. Niobium improves ductility of the steel. Niobium is limited to 0.1 % to limit costs and avoid processing issues.
Vanadium is optionally added up to 0.3%. Vanadium improves the hardenability of the steel. Vanadium is limited to 0.3% to limit costs and avoid processing issues.
In case one or several of the above elements are added, the following formula is further verified: Cr + Mo + Nb + V < 0.5% in order to limit costs and avoid processing issues.
In a specific embodiment, the chemical composition is further controlled so that the following condition is verified:
(S-Ca*32/40) + (30*Ti*N) < 0.0045
The inventors have found that this allowed to further control the inclusion population of the steel sheet and therefore further improve bendability and bending anisotropy.
The remainder of the composition of the steel is iron and impurities resulting from the elaboration process. The level of impurities resulting from the elaboration process will depend on the production route used and the level of scrap used in the steel melt. For example, when using a Basic oxygen furnace route with a low level of steel scrap (recycled steel), the level of impurities will remain very low. It is however also possible to add a high amount of scrap in the converter to the pig iron produced in the basic oxygen furnace, which will increase the level of impurities. Furthermore, when elaborating the steel using an electric furnace for example, with a very high ratio of recycled scrap steel, the level of impurities will be significantly increased. When using a high level of scrap, the level of Cu can go up to 0.25%, Ni can go up to 0.25%, Sn can go up to 0.05%, As can go up to 0.03%, Sb can go up to 0.03% and Pb can go up to 0.03%. The microstructure of the steel sheet according to the invention will now be described.
The steel sheet has a microstructure comprising in surface fraction on any analyse cross section:
-75% to 90% of ferrite,
-the rest being comprised of carbides FesC and hard phases such as martensite and bainite.
Referring to figure 1 , the steel sheet 1 according to the invention comprises a bulk portion 3 and a top and bottom skin layer 2. The total thickness of the steel sheet 1 is to and the thickness ts of the skin layers 2 is such that ts = t0*10%. In other words, the skin layers 2 occupy the outermost 10% of the thickness on either sides of the bulk and the bulk of the steel sheet represents 80% of the steel sheet thickness.
The inventors have found that there is a correlation between the bending anisotropy and the inclusion population in the bulk portion of the steel sheet. In particular, it is possible to limit the bending anisotropy to less than or equal to 7° when controlling the sum of the clustering indexes of MnS and TiN /Ti(C,N) inclusions in the bulk portion of the steel to below 300pm/mm2.
The following is a description of the methodology that was used in order to characterize the inclusions in the steel sheet and steel parts. It should be understood that this is only one possible methodology and that other protocols can also be implemented.
The cross-sections of the steel sheet on which the inclusions are observed are taken in the rolling direction of the steel. In other words, the plane of the observed cross section has the transverse direction as its normal direction.
The inclusions present in the steel sheet have been characterized using a Scanning Electron Microscope (SEM) with Field Effect Gun (FEG). A Tescan Mira 3 SEM was used at a 14kV power setting. This allows to detect particles as small as 0.5 pm. Using a FEG SEM setup allows to obtain stable images with an excellent resolution over a long period of time, which can be necessary for completing image analysis over broad areas - using a FEG SEM setup it is possible to acquire image fields during up to 48 hours which can be necessary for multi samples analysis. Furthermore, the inclusions were analysed using Energy Dispersive Spectrometry (EDS). A 120mm2 Broker EDS probe having large active surface was used in order to detect light elements (0, N) and to get a high count rate and thus allow a precise quantification. The phi-rho-Z method was used to obtain an accurate quantification.
The Automated Steel Cleanliness Analysis Tool (ASCAT) of the RJ Lee group is used to pilot the SEM & associated EDS, based on Computer Control Scanning Electron Microscopy technologies. Six individual samples can be analysed in the same batch. The sample surface is divided in three areas (Top skin, bottom skin, bulk, as described previously). Each area is divided in fields. In each field, inclusions are detected. In order to detect fine particles, the scanning pixel size is set to the very low value of 0.11 pm. This is in order to reduce matrix noise of SEM images. As will be seen, only Objects with diameters over 0.5 pm are actually taken into account. A first selection of objects, which will be termed particles, is made by selecting objects forming a solid and having a grey level, on a scale of 0 to 255, either below 150 or above 220 (the extreme values are excluded).
A zoom is then made on each individual particle to catch their morphological features and to perform an EDS analysis. A database of all particles is created using ASCAT and taking into account, for all acquired images, the chemical and morphological features of all analysed particles.
Out of the set of all analysed particles, only the ones having a size greater than 0.5 pm and an iron content below 80% are retained for the subsequent analysis and will be termed inclusions - the other particles are considered to be part of the matrix and not relevant for the subsequent analysis.
Using the information of the EDS probe, each inclusion is then classified in one of the following families: TiN, alumina, Complex oxides, Oxysulfide particles, MnS and others. For example, table 1 details the precise rules that were used by the inventors to classify MnS and TiN I Ti(C, N) inclusions. Oxygen quantification is made possible by high performance EDS detectors. The oxygen level is checked in order to separate TiN from TiO2 and MnS from complex oxysulfide inclusions. Table 1 - Criteria in weight % of Ti, M, S 0, Nb to classify inclusions
Figure imgf000011_0001
For each inclusion family the following characteristics are then calculated: -average diameter in microns,
-density in number of inclusions per mm2,
The clustering index calculation method is based on the DBSCAN (for Density-Based Spatial Clustering of Applications with Noise) algorithm, as detailed in the article “A density-based algorithm for discovering clusters in large spatial databases with noise”, Ester, Martin; Kriegel, Hans-Peter; Sander, Jorg; Xu, Xiaowei (1996), in Proceedings of the Second International Conference on Knowledge Discovery and Data Mining (KDD-96). AAAI Press, pp. 226-231.
The determination of the clustering index takes 2 parameters: Max_distance and Min_points. A cluster is characterized by the following features:
-it comprises only particles of the same type,
-in a given cluster, the inclusions are all at a distance inferior to Max_distance from at least one other inclusion,
-it comprises a number of individual inclusions equal to or greater than Min_points.
For the present invention, the inventors have found that a good detection of clusters is obtained with a maximum distance Max_distance of 30 pm and a minimum number of inclusions per cluster Min_points of 4.
The length L of a given cluster is computed in the following way: -the convex hull of the cluster is first determined using a known algorithm (see for example the chapter “Convex Hulls: Basic Algorithms” In: Computational Geometry, Preparata, F.P., Shamos, M.I., 1985, Texts and Monographs in Computer Science. Springer, New York, NY)
-The maximum Feret diameter of said convex hull, which will be termed Dmax, is then determined and the Feret diameter taken in the perpendicular direction to Dmax, which will be termed Dperp, is also determined. Information on Feret diameter measurement is available for example in “Particle Size Measurements: Fundamentals, Practice, Quality” Springer. Henk G. Merkus (1 January 2009).
-The length L of said cluster is calculated as
L = Dmax2 + Dperp2
For each type of inclusion an average length of all clusters L_average is computed.
The clusters density C_density of a given type of inclusion is the number of clusters per mm2.
The cluster index C_index for a given type of inclusion is defined as the product of the average length of clusters by their density C_index = L_average *C_density. The cluster index is expressed in pm/mm2 The inventors have found that said cluster index allows to compare samples having different characteristics using a unique number and that it is well correlated to the bending behaviour of said samples.
The steel sheet according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the below described steps.
In the following description, the term ladle refers to the vessel used to contain the liquid steel during the refining process. The refining process is referred to as the step at which the final chemical composition and temperature of the melt is adjusted before casting the steel into its first solidified form (for example before casting it into slabs, which will subsequently be hot rolled).
In order to successfully control the inclusion population of the steel, the following process can for example be implemented:
-The liquid steel is tapped into the ladle from the previous steelmaking process step. For example, in the case of an electric arc furnace production route, said previous process step is the electric arc furnace process itself. For example, in the case of a Blast furnace and converter process (or in the case of a Direct Reduced Iron and convertor process), said previous process step is the converter.
-The Sulphur content of the liquid steel before the refining step is measured, for example by taking a sample of said liquid steel and analysing it using a spark spectrometer. Said sulphur content is for example measured by sampling directly the liquid steel in the ladle or by taking a sample when the liquid steel is being tapped into said ladle. Said sulphur content before the refining step, measured in weight%, will be termed S_start in the following description.
-Aluminium is added to the ladle at the beginning of the refining process in order to deoxidise the liquid steel. Said Al addition is for example performed at the same time as the steel is being tapped into the ladle - advantageously this allows to save time and therefore increase productivity and ensure that the liquid steel stays sufficiently hot. The amount of Al added in the liquid steel at the beginning of the refining process, expressed in kg of aluminium per ton of liquid steel (kg/ton), will be termed Al_added in the following description.
-In a subsequent optional step, for example if the liquid steel temperature is too low or if it is foreseen that the waiting time between the end of the refining step and the subsequent process (e.g. continuous casting) warrants it, the liquid steel is reheated by aluminothermic heating. This is performed by adding a determined amount of aluminium and jointly blowing into the liquid steel a determined amount of oxygen, corresponding to the stoichiometric ratio necessary to form AI2O3 with the added aluminium. The strongly exothermal reaction between Al and O2 allows to increase the temperature of the liquid steel. The amount of O2 injected during this optional step will be termed C>2_inj and is expressed in Normal cubic meters of O2 per ton of liquid steel (Nm3/ton). Since there is a direct stochiometric relationship between the C>2_inj and the associated Al injection for aluminothermic re-heating, said amount of injected Al for aluminothermy will not be considered separately in the current description. It should be noted that said injected Al for aluminothermy is distinct from the previously mentioned Al_added.
- The slag composition above the melt is adjusted by adding the appropriate amount of minerals in order to ensure that the ratio %CaO I %Al2Os of the slag is above 1 , that the amount of slag per ton of liquid steel is at least 10kg/ton of liquid steel and that the slag remains liquid in order to promote chemical exchanges with the steel, to be able to access the steel below the slag and to be able to tap the steel and I or the slag separately (the liquid state of the slag is verified visually and I or using thermodynamic rules based on its composition and temperature),
-In a subsequent step, the liquid steel is stirred by blowing an inert gas, for example by blowing Ar, within the liquid steel. This is done in order to promote the exchanges between the liquid steel and the slag, which will allow to lower the sulphur content of the liquid steel.
-In a further step, Ca is added to the ladle in order to globularise the inclusions present within the liquid steel. For example, Ca is added in the form of Silicon Calcium (SiCa) or in the form of Ferro-calcium (FeCa), or as pure Calcium. For example, said addition is performed by adding SiCa or FeCa to the ladle in the form of a cored wire - advantageously, this allows to easily control the amount of Ca added by controlling the length and the injection speed of cored wire inserted into the melt. The amount of Ca added in the liquid steel, measured in weight% within the liquid steel, will be termed Ca_added in the following description.
Considering the above described process, the inventors have found that a satisfactory level of inclusions to reach the desired bending anisotropy properties after hot stamping can be obtained by controlling the above described levels of measured Sulphur at the beginning of the refining process (S_start measured in wt%), Al addition at the beginning of the refining process (Al_added measured in kg/ton), Ca addition during the refining process (Ca-added measured in kg/ton) and volume of O2 blowing (C>2_inj measured in Nm3/ton) in order to verify that the combination below (which will be termed C1 in the rest of the description) stays below a given cut-off value:
Al_added + 0.1953*(S_start*1000 + O2_inj) - 9.367*Ca_added (C1 ) In effect, the specific cut-off value below which the combination C1 needs to be controlled will depend on the specific industrial setup which is used to produce the steel. It will depend on the production route in the steel shop, the geometric configuration of the ladles that are used to process the liquid steel, the equipment used to add the different additions, the oxygen blowing configuration etc.
In order to determine the relationship between these parameters for a given industrial equipment and production route, it is recommended to apply the following method:
-Several heats are performed using the chemical composition ranges described previously.
-Said heats are processed using different refining process parameters, in particular different levels of measured Sulphur at the beginning of the refining process, Al addition at the beginning of the refining process, Ca addition during the refining process and volume of O2 blowing. The ranges of tested refining process parameters are chosen so as to be representative of the industrial variation of these parameters. For example, a set of 6 different heats with 6 different sets of refining process parameters is chosen. For example, a set of 8 different heats with 8 different sets of refining process parameters is chosen.
-Said heats are processed according to the below described industrial route and the inclusion population of the steels are characterized using the abovedescribed method.
-The sum of the clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel sheets and the associated refining process parameters are then recorded. The combination C1 of said refining process parameters is computed. As a general trend, it will be seen that the higher said combination C1 is, the higher the sum of the clustering indexes will be.
-Using the above-described set of data associating clustering index and refining process parameters, a cut-off value is determined below which the sum of clustering indexes of MnS and TiN / Ti(C, N) inclusions in the bulk portion of the steel sheets is lower than 300pm/mm2. Said cut-off value of combination C1 will determine how to control the refining process for the specific industrial installation that is being considered. By controlling C1 below said cut-off value, it will be possible to produce steel sheets having a sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion below 300pm/mm2 and thus to reach the associated excellent bending anisotropy of less than or equal to 7°.
For example, in the case of the specific industrial installations upon which the inventors performed experiments, said cut-off value is equal to 1.80.
After the liquid steel refining step, the method for manufacturing the steel sheet according to the present invention preferably comprises the following steps:
-continuous casting of the liquid steel into a semi-product suitable to be hot- rolled. During the casting step particular care should be taken to avoid oxygen pickup and therefore higher inclusions level in the semi-product. For example, in the case of a continuous casting process in which the semi-products are slabs produced in a continuous sequence by casting in a mold the product of multiple heats poured into a tundish, specific refractories and linings can be used in the tundish, specific allocation rules can be used for first of sequence slabs and transient slabs between two different heats, etc.
-The semi product is then optionally reheated at a temperature comprised from 1150°C to 1300°C.
-The steel sheet is then hot rolled at a finish hot rolling temperature comprised from 800°C to 950°C.
-The hot-rolled steel is then cooled and coiled at a temperature Tcoii lower than 670°C, and optionally pickled to remove oxidation.
-The coiled steel sheet is then optionally cold rolled to obtain a cold rolled steel sheet. The cold-rolling reduction ratio preferably ranges from 20% to 80%. Below 20%, the recrystallization during subsequent heat-treatment is not favored, which may impair the ductility of the steel sheet. Above 80%, there is a risk of edge cracking during cold rolling.
-In an embodiment of the invention the steel sheet is heated in an annealing furnace to a soaking temperature comprised from 700°C to 850°C and maintained at said soaking temperature for a soaking time comprised from 10 seconds to 20 minutes.
-In an embodiment of the invention, the thus annealed steel sheet is cooled to a temperature range from 400°C to 700°C and further coated with a metallic coating. Said metallic coating is for example an aluminum based metallic coating comprising at least 50% of aluminum in weight. Said metallic coating is for example a zinc based metallic coating comprising at least 50% of zinc in weight.
-In an embodiment of the invention, the steel sheet is then cooled to room temperature.
In summary, the above-described process comprises preferably the following successive steps:
-Producing a liquid steel having the above-described chemical composition, wherein during the liquid steel refining phase the levels of measured Sulphur at the beginning of the refining process, Al addition at the beginning of the refining process, Ca addition during the refining process and volume of O2 blowing is controlled to verify that the combination Al_added + 0.1953*(S_start *1000 + C>2_inj) - 9.367*Ca_added (C1 ) stays below a predetermined cut-off value. Said cut-off value having been determined for the specific industrial equipment which is being used so that when C1 is below the cut-off value, the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel is below 300pm/mm2.
-casting said liquid steel to obtain a semi-product able to be hot-rolled, -optionally reheating the semi-product at a temperature Treheat comprised from 1100°C to 1300°C,
-hot rolling the semi-product at a finish hot rolling temperature comprised from 800°C to 950°C
-coiling the hot rolled steel sheet at a coiling temperature Tcoii lower than 670°C to obtain a coiled steel sheet,
-optionally pickling the coiled steel sheet,
-optionally cold rolling the coiled steel sheet with a reduction ratio ranging from 20% to 80% to obtain a cold rolled steel sheet
-optionally heating the hot rolled steel sheet or the cold rolled steel sheet up to a soaking temperature comprised from 700°C to 850°C and maintaining the steel sheet at said temperature for a soaking time comprised from 10 seconds to 20 minutes, to obtain an annealed steel sheet, -optionally cooling said annealed steel sheet to a temperature range from 400°C to 700°C,
-optionally coating the annealed steel sheet with a metallic coating -optionally cooling the coated steel sheet to room temperature.
The press part manufacturing process and ensuing pressed part characteristics will now be detailed.
A steel blank is cut out of the steel sheet according to the invention and heated in an austenitizing furnace. Preferably, the steel blank is heated to a temperature comprised from 880°C to 950°C during 10 seconds to 15 minutes to obtain a heated steel blank. The heated blank is then transferred to a forming press before being hot formed and die-quenched to obtain a pressed part.
Optionally, the hot stamped part is further submitted to a paint baking step in which the part is heated to a temperature between 150°C and 250°C for a duration of 10 minutes to 2 hours.
The microstructure of the pressed part comprises in surface fraction on any analysed cross-section, more than 95% of martensite and less than 5% of bainite + ferrite. Furthermore, the pressed part according to the invention comprises a bulk portion and a top and bottom skin layer, wherein the skin layers occupy the outermost 10% of the thickness on either side of the bulk. Said bulk portion has a sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions below 300pm/mm2.
The pressed part according to the invention has a tensile strength above 1300MPa, preferably above 1350MPa, preferably above 1400MPa, and a bending angle anisotropy less than or equal to 7°. Such a high tensile strength and low bending anisotropy confer to said part a very good mechanical resistance, especially in the case of a crash and further allows to have very predictable and uniform behaviours in all directions. These characteristics afford a very good energy absorption capacity and anti-intrusion capacity in all direction, thereby increasing the safety of the vehicle.
The invention will be now illustrated by the following examples, which are by no way limitative. 8 different samples were tested coming from 8 different heats A, B, C, D, E, F, G and H of steel produced using an industrial production route. Samples 11 , I2, I3 and I4 are according to the invention, samples R1 , R2, R3 and R4 are reference samples.
All the produced samples have followed the same industrial production process in the steel shop. All samples have been coated after annealing using an AlSi based coating containing 8 - 12wt% Si, 2 - 4wt% Fe, the balance being Al.
Table 2 - Sample composition
The tested compositions are gathered in the following table wherein the element contents are expressed in weight percent, the remainder of the composition being iron and unavoidable impurities resulting from the elaboration process:
Figure imgf000019_0001
Table 3 - Steel shop process parameters and sum of clustering indexes of MnS and TiN / Ti(C,N) inclusions in the bulk portion of the steel
The following process parameters were applied in the steel shop and the following sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel was observed - the underlined values are not according to the invention:
Figure imgf000020_0001
*C1 = Al_added + 0.1953*(S_start*1000 + O2_inj) - 9.367*Ca_added
As can be seen, in the tested industrial conditions, the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel can be controlled to below 300 pm/mm2 by ensuring that the refining process parameters are appropriately controlled to keep C1 equal to or lower than 1.80. As previously explained, this cut-off value of 1.80 is specific to the industrial setup on which the trials were performed and the appropriate cut-off factor for a given industrial setup will need to be determined, for example by following the above-described methodology.
Table 4 - further process conditions
The following process parameters were applied along the production route:
Figure imgf000021_0001
Table 5 - microstructure, bending angles and tensile strength
The following microstructures (in surface fraction), bending angles, bending angle anisotropies and tensile strength were measured on the samples, the underlined values are not according to the invention:
Figure imgf000021_0002
Table 5 shows that the samples according to the invention have a tensile strength above 1300MPa (both in RD and TD) while having a bending anisotropy which is below 7°. On the other hand, the reference samples, while having comparable tensile strength levels above 1300MPa, have a bending anisotropy which is above 7°. The inventors have found that this very good bending anisotropy is correlated to the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel, as can be seen in table 3. A higher sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions in the bulk portion of the steel results in a higher bending anisotropy. A cut-off value of 300 pm/mm2, allows to control the bending anisotropy to below 7°. With this very low level of bending anisotropy, the behavior of the hot stamped part will be very homogeneous when submitted to loads coming from any direction. This very stable behavior of the hot stamped part under load allows for a simplified design of parts, for example in the case of automotive parts and ensures very good, robust and stable crash worthiness of the hot stamped part.

Claims

1. A steel sheet made of a steel having a composition comprising, by weight percent:
C : 0.2 - 0.4 %
Mn : 0.8 - 2.0%
Si : 0.1 - 0.5 %
Al : 0.01 - 0.1 %
Ti: 0.01 - 0.1 %
B: 0.0005 - 0.005 %
P < 0.040 %
Ca < 0.01 %
S < 0.006 %
N < 0.01 %
And comprising optionally:
Cr < 0.4%
Mo < 0.3%
Nb < 0.1 %
V < 0.3 %
Wherein Cr + Mo + Nb + V < 0.5% the remainder of the composition being iron and unavoidable impurities resulting from the elaboration process, said steel sheet having a microstructure in surface fraction comprising from 75% to 90% of ferrite, the rest being comprised of FesC and hard phases such as martensite and bainite, said steel sheet comprising from the bulk to the surface of the steel sheet:
- a bulk
- such bulk being topped by a skin layer occupying the outermost 10% of the thickness on either side of the bulk, said bulk comprising an inclusion population wherein the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions is less than or equal to 300pm/mm2.
2. A steel sheet according to claim 1 , wherein the steel sheet is coated with a metallic coating comprising at least 50% of Al in weight.
3. A steel sheet according to claim 1 , wherein the steel sheet is coated with a metallic coating comprising at least 50% of Zn in weight.
4. A steel sheet according to any one of claims 1 to 3, wherein the chemical composition further respects the following condition, all elements being expressed in weight %:
(S-Ca*32/40) + (30*Ti*N) < 0.0045.
5. A press hardened steel part, the steel part having a composition comprising, by weight percent:
C : 0.2 - 0.4 %
Mn : 0.8 - 2.0%
Si : 0.1 - 0.5 %
Al : 0.01 - 0.1 %
Ti: 0.01 - 0.1 %
B: 0.0005 - 0.005 %
P < 0.040 %
Ca < 0.01 %
S < 0.006 %
N < 0.01 %
And comprising optionally:
Cr < 0.4%
Mo < 0.3%
Nb < 0.1 %
V < 0.3 %
Wherein Cr + Mo + Nb + V < 0.5% the remainder of the composition being iron and unavoidable impurities resulting from the elaboration process, said steel part having a microstructure comprising, in surface fraction, more than 95% of martensite and up to 5% of bainite or ferrite said steel part comprising from the bulk to the surface of the steel part:
- a bulk
- such bulk being topped by a skin layer occupying the outermost 10% of the thickness on either side of the bulk, said bulk comprising an inclusion population wherein the sum of clustering indexes of MnS and TiN I Ti(C,N) inclusions is less than or equal to 300pm/mm2.
6. A press hardened steel part according to claim 5, wherein the chemical composition further respects the following condition, all elements being expressed in weight %: (S-Ca*32/40) + (30*Ti*N) < 0.0045.
7. A press hardened steel part according to claim 5 or 6, wherein the press hardened steel part has a tensile strength TS of at least 1300 MPa and a bending angle anisotropy less than or equal to 7°.
8. A process for manufacturing a press hardened steel part according to any one of claims 5 to 7, comprising the following successive steps:
- providing a steel sheet according to any one of claims 1 to 3,
- cutting said steel sheet to a predetermined shape, so as to obtain a steel blank,
- heating the steel blank to a temperature from 880°C to 950°C during 10 seconds to 15 minutes to obtain a heated steel blank,
- transferring the heated blank to a forming press,
- hot-forming the heated blank in the forming press to obtain a formed part,
- die-quenching the formed part.
9. A process according to claim 7 further comprising a paint baking step, in which the hot-stamped part is heated to a temperature between 150°C and 250°C for a duration of 10 minutes to 2 hours.
PCT/IB2023/056848 2023-06-30 2023-06-30 Steel sheet and high strength press hardened steel part having excellent bending anisotropy and method of manufacturing the same Ceased WO2025003736A1 (en)

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