Classifications

• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/18—Hardening; Quenching with or without subsequent tempering
  • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/26—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
• • 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 by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
  • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • 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
  • C21D2211/008—Martensite

Definitions

• the invention relates to a method and a device for setting specific combinations of properties in hot-rolled multiphase steels whose multiphase structure comprises at least 30% ferrite and at most 50% martensite, for example dual-phase and TRIP steels, which are on a conventional hot rolling mill, a thin slab Casting rolling mill or corresponding narrow and medium strip lines or a wire line are prepared with a standard analysis and a standard process management.
• Multi-phase steels have a significantly improved combination of strength and ductility compared to conventional steel grades and are therefore becoming more and more important, especially for the automotive industry.
• the most important steel groups for the automotive industry are dual-phase steels and TRIP steels.
• a characteristic feature of dual-phase steels is a low yield ratio, which is usually between 50 and 70%.
• HSLA steels high-strength low-alloy
• ie high-strength, low-alloy structural steels in addition to the lower yield strength at the same tensile strength level, significantly better elongation values are achieved.
• TRIP transformation induced plasticity
• steels with a texture of, for example, 40-70% ferrite, 15-40% bainite and 5-20% retained austenite is the transformation of the metastable retained austenite to martensite when external plastic deformation occurs.
• This transformation which is associated with an increase in volume and a plasticization of the ferritic matrix and is not carried by the austenite alone, but also by the surrounding structural constituents, results in a higher degree of solidification and leads overall to higher plastic strains.
• steels produced in this way have an extraordinary combination of high strength and high ductility, which makes them particularly suitable for use in the automotive industry.
• EP 1 396 549 A1 discloses a process in which a molten steel containing not only iron and unavoidable impurities but also at least one of Ti or Nb as an essential constituent and optionally one or more of elements max. 0.8% Cr, max. 0.8% Cu, max. 1, 0% Ni, is cast into thin slabs, which are annealed with a 850 to 1050 0 C amounting inlet temperature in an annealing furnace for an annealing time of 10 to 60 minutes at 1000 to 1200 0 C.
• the thin slabs are then hot rolled in the range of 750 to 1000 0 C and then to a coiling temperature of 300 to 530 0 C in two stages with a controlled cooling rate of the first stage of at least 150 K / s and a cooling pause of 4 bis Cooled for 8 seconds.
• the presence of Ti and / or Nb is important, since these elements remain in solution until the start of hot rolling and improve their subsequent separation, inter alia, the grain size of the hot strip, an increase in Austenitgehaltes and its stability.
• EP 1 394 279 B1 discloses a process for producing a low-carbon steel of high strength and high ductility with a tensile strength of greater than 800 MPa, a uniform elongation of greater than 5% and an elongation at break of greater than 20%.
• a steel with 0.20% C, 1, 60% Mn and admixtures of boron and a martensite phase content of greater than 90% After a cold rolling of greater than 20% of the total rolling an annealing treatment at a Temperature between 500 and 600 ° C, wherein a microstructure with an ultrafine, crystalline, granular ferrite structure of 100 to 300 nm is obtained with ferrite deposited in the iron carbides.
• the stated object is procedurally achieved with the characterizing features of claim 1, characterized in that following the cooling from the hot rolling or a later manufacturing step, for example in the manufacture of components, by a subsequent or intermediate annealing with variable annealing temperature and variable annealing time the desired combinations of strength and yield strength ratios can be set on the multiphase steels.
• An apparatus for carrying out the method is characterized by the features of claim 8.
• Advantageous embodiments of the invention are specified in the subclaims.
• the annealing treatment with a variable annealing temperature of ⁇ 600 0 C and a likewise variable annealing period of ⁇ 120 s leads so carried that the resulting microstructure of a ferritic base matrix and martensite or bainite with 10 to 50% of the area ratio.
• the annealing temperature primarily influences the level of yield strength by means of finely divided precipitates of carbides on the grain boundaries of the martensite or bainite, and the tensile strength level can be adjusted by the annealing time.
• the annealing treatment can be carried out offline in a continuous annealing device, independently of upstream or downstream process stages, or else online in the existing process line, for example in the course of strip galvanizing in the heating stage of a galvanizing line prior to insertion. run in the zinc bath, be performed.
• the annealing treatment it is furthermore possible for the annealing treatment to be carried out on already finished components (frame structures, wheels, connecting elements, etc.), with the result that these components are subsequently improved in their mechanical properties.
• the advantage of this procedure is that the forming of the component can be carried out on a good cold-formable material with a low yield ratio with good elongation and thus the tool wear is kept comparatively low.
• the strength of the components is increased to values that can otherwise be difficult to specify, because then the pressing force of the forming machines would not be sufficient.
• a zonal annealing treatment at localized points of a component is specifically possible according to the invention.
• the aim here is the partial replacement of welded tailor blanks. Tailor blanks are used to weld steels of higher strength at specific points of components in order to set desired component stiffnesses. However, this welding could be dispensed with if, instead, a zonal annealing treatment is then carried out at the points in question.
• a device for setting specific combinations of properties in hot-rolled multiphase steels by an annealing treatment is inventively characterized by a arranged at a freely selectable location within the production onsstrom or production line thermal plant in which an annealing to an annealing temperature of ⁇ 600 0 C. and is feasible up to an annealing time of ⁇ 120 s.
• This thermal installation can be a continuous heating device in which the annealing of components, for example, is carried out offline, or it is arranged online in an existing process line, for example in the course of strip galvanizing, in the heating stage of a galvanizing line prior to entry into the zinc bath.
• Dual phase steels exhibit partially anisotropic toughness properties in the rolling direction and transversely thereto.
• this anisotropy is made of the properties in both directions made uniform (isotropic properties).
• the untreated hot strip (annealing time 0 s) has a significantly different development of the elongation at break in roll longitudinal and transverse rolling direction. Due to the short annealing treatment (annealing time 1 min.), The tensile strength decreases slightly, but the values for the elongation at break altogether rise to a higher level:
• Fig. 3 is a flow chart of the annealing of components.
• FIGS. 1 to 3 show, in the form of flow patterns, the individual process steps required for the inventive annealing of strip material (FIG. 1), wire material (FIG. 2) and components (FIG Procedure path is marked with numbered directional arrows.
• Strip material FIG. 1
• wire material FIGG. 2
• components FIGS. 1 to 3
• FIGS. 1 to 3 show, in the form of flow patterns, the individual process steps required for the inventive annealing of strip material (FIG. 1), wire material (FIG. 2) and components (FIG Procedure path is marked with numbered directional arrows.
• Common to all the flow charts listed is that as a starting point, first a hot rolling takes place, followed by a controlled cooling from the hot rolling to achieve a multi-phase structure. The other possible process steps and the time of the annealing carried out in the various materials are described below.
• FIG. 1 shows possible process paths 1, 2 for an annealing treatment of strip material before further processing.
• an annealing treatment 30 is carried out after the hot rolling 10 and the controlled cooling 20 and subsequently the strip material is fed to the finished product 80 for further processing.
• the annealing treatment 30 can be carried out online, for which purpose a corresponding continuous furnace is to be arranged in the existing process line.
• a band bonding 40 of the hot strip takes place, so that before that a continuous annealing treatment 30 can be carried out online in the heating stage of the galvanizing line.
• the further processing then takes place to the finished product 80 of the strip material.
• FIG. 2 shows possible process paths 1, 2, 3 for an annealing treatment of wire material.
• the annealing treatment 30 which can be done online here as in the strip material.
• the heat treatment 30 is then followed directly by the further processing to the finished product 80.
• the pressing 50 of connecting elements takes place before the wire material is fed to the finished product 80 for further processing.
• this pressing 50 of connecting elements can be carried out already before the annealing treatment 30, as the method 3 shows.
• the resulting process steps arranged one behind the other are then: hot rolling 10, controlled cooling 20, pressing 50 of connecting elements, annealing treatment 30 and finally the further processing to the finished product 80.
• FIG. 3 shows possible process paths 1, 2, 3 for an annealing treatment of components, wherein for all three process paths after the controlled cooling 20, a further process step first takes place with the production of a blank 60.
• the production of components with adjusted mechanical properties takes place after the production of the blank 60, the pressing of the components 70.
• the entire component is then subjected to an annealing treatment 30 and then fed to the finished product 80 for further processing.
• process route 3 in process route 3 the production of components with a subsequent local change of the mechanical properties is carried out by a zonal annealing treatment 35 of the pressed component, whereby the pressing of the components 70 can advantageously be carried out on the still untreated blank. After this zonal annealing treatment 35, the component which is locally changed in its mechanical strength can then be supplied to the finished product 80 for further processing.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Crystallography & Structural Chemistry (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Thermal Sciences (AREA)
• Physics & Mathematics (AREA)
• Heat Treatment Of Sheet Steel (AREA)
• Heat Treatment Of Strip Materials And Filament Materials (AREA)
• Coating With Molten Metal (AREA)
• Metal Rolling (AREA)

Applications Claiming Priority (2)

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• 2006
  • 2006-01-10 DE DE102006001198A patent/DE102006001198A1/de not_active Withdrawn
  • 2006-12-11 EP EP06829499A patent/EP1974064A1/de not_active Withdrawn
  • 2006-12-11 RU RU2008109221/02A patent/RU2379359C2/ru not_active IP Right Cessation
  • 2006-12-11 UA UAA200804988A patent/UA90348C2/ru unknown
  • 2006-12-11 US US11/992,856 patent/US20090151821A1/en not_active Abandoned
  • 2006-12-11 CA CA002636287A patent/CA2636287A1/en not_active Abandoned
  • 2006-12-11 CN CN2006800508559A patent/CN101415846B/zh not_active Expired - Fee Related
  • 2006-12-11 WO PCT/EP2006/011909 patent/WO2007079876A1/de active Application Filing
  • 2006-12-11 BR BRPI0620929-7A patent/BRPI0620929A2/pt not_active IP Right Cessation
  • 2006-12-11 JP JP2008549775A patent/JP2009522452A/ja active Pending

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