EP4038213A1 - Procédé de fabrication d'un élément en tôle d'acier au moins partiellement trempée et revenue et élément ainsi fabriqué - Google Patents

Procédé de fabrication d'un élément en tôle d'acier au moins partiellement trempée et revenue et élément ainsi fabriqué

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Publication number
EP4038213A1
EP4038213A1 EP20776138.8A EP20776138A EP4038213A1 EP 4038213 A1 EP4038213 A1 EP 4038213A1 EP 20776138 A EP20776138 A EP 20776138A EP 4038213 A1 EP4038213 A1 EP 4038213A1
Authority
EP
European Patent Office
Prior art keywords
area
sheet steel
steel component
partially
sheet
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
EP20776138.8A
Other languages
German (de)
English (en)
Inventor
Bernd Linke
Janko Banik
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel Europe AG
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 ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP4038213A1 publication Critical patent/EP4038213A1/fr
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • 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
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D2211/00—Microstructure comprising significant phases
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a method for producing an at least partially tempered sheet steel component, the method comprising the following steps:
  • the invention also relates to an at least partially tempered sheet steel component.
  • sheet steel components by means of hot forming has already established itself industrially, in particular for the production of body parts such as, for example, for the production of safety-relevant A-pillars, B-pillars or longitudinal and cross members.
  • These sheet steel components can be manufactured using both direct and indirect hot forming processes.
  • Flat blanks (direct) or already pre-formed or near-net-shape (cold) formed semi-finished products / parts (indirect) made from a steel sheet, in particular from a hardenable steel sheet, are heated to a temperature at which, depending on the composition of the steel sheet used, a Structural transformation occurs within the steel sheet.
  • Acl the structural transformation into austenite begins and when Ac3 or above Ac3 is reached, an essentially completely austenitic structure is present.
  • the warm (austenitized) sheet steel is placed in a forming tool and hot formed.
  • the still warm steel sheet is cooled in such a way, preferably within the forming tool, which is preferably actively cooled, so that the structure turns into a hard structure of martensite and / or bainite, preferably essentially of martensite, is converted.
  • cooling or quenching of the steel sheet within the forming tool or by the action of a (hardening) tool, which has the final contour of the sheet metal component to be produced is also called “press hardening”.
  • cooling / quenching can take place outside of a forming tool / hardening tool, in particular in a (cold) medium. around, for example in an oil bath, and is called “hardening”.
  • Heating and cooling curves for setting the required microstructure depend on the chemical composition of the hardenable steel sheet used and can be inferred or derived from so-called ZTA or ZTU diagrams.
  • press-hardened structural components have the disadvantage that they only have a very low elongation behavior due to the set hard structure.
  • Q + P process quenching and partitioning
  • a sheet steel is austenitized, hot-formed into a component and quenched in the process, and then without it the component cools to room temperature, tempering (partitioning) below the microstructure transition temperature of Acl, see, for example, the documents EP 2 546 375 B1, US 8 518 195 B2, DE 10 2013 010 946 B3.
  • crash energy should be absorbed by deformation.
  • the passenger cell must remain protected. This is achieved, among other things, by locally deforming or buckling certain areas in order to direct the macroscopic deformation. In the current state of the art, this is achieved in press-hardened components by annealing individual points, for example by means of a laser, which results in higher local formability and lower hardness in this area, see, for example, the document DE 10 2011 101 991 B3 .
  • the object is therefore to provide a method which allows the production of an at least partially tempered sheet steel component in such a way that the resulting sheet steel component has an improved property compared to the prior art and can be produced economically.
  • the object is achieved with a method for producing an at least partially tempered sheet steel component with the features of claim 1 and with an at least partially tempered sheet steel component with the features of claim 13.
  • the method according to the invention comprises the following steps: providing a sheet steel; at least partially austenitizing the steel sheet at a temperature of at least Acl; at least partial hardening of the austenitized steel sheet to form an at least partially hardened steel sheet component, the at least partially austenitized steel sheet being cooled to a temperature below Ms; at least partial tempering of the at least partially hardened sheet steel component at a temperature of less than Acl to produce an at least partially tempered sheet steel component, the at least partial tempering for producing the at least partially tempered sheet steel component being carried out at different temperatures in order to have areas on the at least partially tempered sheet steel component different properties.
  • the inventors have surprisingly found that an inexpensive sheet steel component with targeted properties can be produced and the disadvantages known from the prior art can be compensated, in particular by integrating the Q + P process into the hot forming and / or hardening process (quenching ) in combination with locally adapted heat treatment parameters during tempering (partitioning).
  • Such an at least partially tempered sheet steel component then has several areas with different properties that are set in terms of process technology by at least partially tempering the sheet steel component at different tempering temperatures (TP1, TP2, TP3, TP4).
  • the at least partial tempering to generate an area with a first property on the at least partially tempered sheet steel component at a first tempering temperature TP1 between 300 ° C and 470 ° C and to generate at least one further area with a further property in at least one at the following tempering temperatures TP2, TP3, TP4:
  • a (first) area with the first property is set on the at least partially tempered sheet steel component, a (first) tempering temperature TP1 between 300 ° C. and 470 ° C. being selected to generate the first area.
  • a (first) tempering temperature TP1 between 300 ° C. and 470 ° C. being selected to generate the first area.
  • S_RA stability criterion
  • the tempering temperature TP1 is selected in particular between 350 ° C and 470 ° C.
  • the tempering temperature TP1 is preferably selected between 400 ° C. and 460 ° C., stabilization of the retained austenite can be achieved particularly easily, preferably within less than 50 s.
  • At least one further area with a further property is set on the at least partially tempered sheet steel component during the at least partially tempered.
  • the first area with the first property is not locally restricted to just one area or only to a section on the at least partially tempered sheet steel component, but can also be present in several areas or sections of the at least partially tempered sheet steel component. This can also apply to the at least one further area with the at least one further property.
  • the at least one further area can include a third area with a third property, a third tempering temperature TP3> 470 ° C. being selected to generate the third area, so that a third area with reduced clarity can be achieved in a targeted manner due to the high tempering temperature.
  • the third tempering temperature TP3 can in particular be selected to be> 500 ° C. in order to also accelerate a desired decomposition of carbon-supersaturated residual austenite.
  • the at least one further area can include a fourth area with a fourth property, with a fourth tempering temperature TP4 to 300 ° C being selected to generate the fourth area, so that the tempering temperatures are very low compared to the other, resulting in a stabilization of retained austenite and a softening of the Martensites can be prevented.
  • the fourth tempering temperature TP4 can in particular be selected to be ⁇ 250 ° C, preferably ⁇ 200 ° C, preferably ⁇ 00 ° C, so that the fourth tempering temperature TP4 does not necessarily require a temperature increase after clearing in the fourth range, but rather a holding or lowering , depending on or depending on the temperature to which the at least partially hardened sheet steel component was cooled during the at least partial hardening, so that the austenite in the fourth area turns almost completely into martensite before the fourth tempering temperature TP4, in particular the holding temperature, is applied has converted, which can lead to a particularly homogeneous hardness distribution in the fourth area.
  • the fourth tempering temperature TP4 can be at least 0 ° C, in particular at least 20 ° C, preferably at least 25 ° C, preferably at least 30 ° C, more preferably at least 40 ° C, particularly preferably at least 50 ° C, for example to achieve a higher stretch limit than to reach temperatures below 0 ° C.
  • the steel sheet can be an essentially flat steel sheet or a preformed steel sheet with a constant thickness of up to 10.0 mm, in particular up to 6.0 mm, preferably up to 3.5 mm, preferably up to 2.0 mm.
  • the steel sheet has a thickness of at least 0.5 mm, in particular of at least 0.8 mm, preferably of at least 1.0 mm.
  • the steel sheet can be hot-rolled as well as cold-rolled. Alternatively, a Flat sheet steel or a preformed sheet steel with varying thickness (tailored rolled blank) can be provided.
  • sheet steel can also be understood as a “tailored product”, which consists of at least two, in particular cohesively, interconnected steel sheets with different thickness and / or quality, as a flat semi-finished product (sheet steel) or as a preformed part (sheet steel), as a “patchwork blank ”or“ tailored wel- ded blank ”.
  • the steel sheet can also be provided with a coating, a metallic coating based on aluminum or zinc preferably being used. This can be applied to the rolled or pre-cut steel sheet using a hot-dip, electrolytic or coil coating process.
  • the steel sheet is at least partially heated or austenitized to a temperature of at least Acl or above, in particular to at least Ac3 or above, to form austenite, preferably in a period of time which is sufficient to, in particular depending on the thickness of the Steel sheet to completely heat the steel sheet in thickness or to homogenize the carbon in the austenite in the steel sheet and / or if the steel sheet is provided with a metallic coating, essentially an alloying of the coating, which in particular a faster Ver workability in the forming process enables to guarantee.
  • the austenite content and the carbon content in the austenite depend on the austenitization duration, so that complete austenitization> Ac3 is preferred.
  • Hardening is to be understood as meaning that the steel sheet as a result of the targeted austenitization, as is carried out in direct and indirect hot forming for the production of a sheet steel component, the sheet steel component at least partially (partially / locally) a higher hardness or strength compared to the sheet steel provided having.
  • the at least partial hardening can take place in a tool (press hardening) or in a medium (hardening). If the at least partially austenitized steel sheet is cooled to a temperature below Ms, it can be ensured that the formation of a hard structure of austenite is at least partially forced into martensite, in particular by means of suitable cooling speeds.
  • the average cooling rate is in particular at least 10K / s, preferably at least 15K / s, preferably at least 20K / s, with cooling rates of 50 K / s up to 300 K / s also being possible.
  • the conversion to martensite would be completed when the Mf temperature is reached or not reached. According to the invention, this is not desired, so that in particular a temperature between Ms and Mf is chosen, which is preferably below the temperature at which preferably at least 50% of the austenite can convert into martensite.
  • Parameters such as Acl, Ac3, Ms, Mf, (critical) cooling rates etc. depend on the steel composition used and can be derived from so-called ZTU or ZTA diagrams.
  • the at least partial tempering is carried out immediately after hardening, so that the heat still present in the at least partially hardened sheet steel component can be used to heat the sheet steel component more quickly to the target temperatures during the at least partial tempering can, whereby the process can be operated more quickly and thus more economically.
  • Direct tempering also enables part of the austenite to be stabilized to such an extent that it is no longer converted into martensite in the further course of the process and is present as retained austenite in the final component.
  • one or more transition areas are set between the areas with different properties on the at least partially tempered sheet steel component, which transition areas have a harmonious transition of the properties between the areas with different properties.
  • a sudden or abrupt and thus failure-prone transition metallurgical notch
  • a steel sheet is provided with the following chemical composition in% by weight:
  • Si + AI> 0.5, with Si + 2 * AI ⁇ 5,
  • Mn 0.5 to 4, and optionally one or more of the following elements:
  • Carbon (C) performs several important functions.
  • C is a martensite former and therefore essential for setting a desired hardness in the at least partially hardened or at least partially tempered sheet steel component, so that at least a content of 0.08% by weight, in particular at least a content of 0.1% by weight .-%, preferably at least a content of 0.15 wt .-% is present in order to be able to stabilize the residual austenite with carbon.
  • the specified upper limit can avoid negative influences with regard to the toughness properties, the forming properties and the suitability for welding.
  • the C content can be set individually within the specified ranges.
  • silicon (Si) can act as an alternative or in addition to aluminum as a deoxidation element and can therefore be added with a content of a maximum of 3% by weight.
  • a content of at least 0.01% by weight is particularly important. used.
  • Si can also contribute to increasing the strength, so that a content of at least 0.1% by weight, preferably of at least 0.15% by weight, is preferably added. If too much Si is added to the steel, this can have a negative impact on the toughness properties, formability and weldability.
  • the content is therefore limited in particular to a maximum of 3% by weight, to improve the surface quality, preferably to a maximum of 1.6% by weight, preferably to a maximum of 1.4% by weight, in order to ensure wetting in the case of hot-dip finishing improve.
  • AI aluminum
  • silicon aluminum
  • AI can be added as an alloying element for deoxidation in contents of at least 0.01% by weight.
  • AI can be used to bind any nitrogen that may be present, so that optionally added boron can develop its strength-increasing effect.
  • a content of at least 0.02% by weight, preferably at least 0.1% by weight, is therefore added.
  • AI can also be used to reduce density. To avoid problems with casting technology, the content is limited to a maximum of 1% by weight, in particular to a maximum of 0.8% by weight.
  • Si and / or Al alloying are required, so that Si + Al> 0.5% by weight is alloyed. So that this is also guaranteed over a wide process window, Si + Al> 0.75% by weight in particular is alloyed. If Si + Al> 1.3% by weight is preferably added, the major part of the carbon can be partitioned into the carbon-supersaturated austenite and precipitation of cement can essentially be prevented.
  • the content of ferrite formers such as Si and Al which are readily soluble in the iron lattice, must be limited to Si + 2 * Al ⁇ 5% by weight.
  • an additional alloy in particular is restricted to Si + 2 * Al ⁇ 3% by weight.
  • Manganese (Mn) is an alloying element that contributes to hardenability. At the same time, Mn reduces the tendency for undesired formation of pearlite during cooling and lowers the critical cooling rate, whereby the hardenability is increased. In addition, Mn can be used to set S, in order to prevent the hot-rollability from being excessively impaired by an FeS eutectic, and / or to reduce the pearlite content, so that in particular a content of at least 0.5% by weight is present. Too high a Mn concentration, on the other hand, has a negative effect on the weldability, so that Mn is limited to a maximum of 4% by weight.
  • the content is particularly these are limited to a maximum of 3% by weight, preferably to a maximum of 2.5% by weight to improve the toughness properties.
  • a content of in particular at least 0.8% by weight, preferably of at least 1.0% by weight, is added. If the carbon-supersaturated retained austenite is to be stabilized for particularly long tempering times, Mn is preferably added with at least 1.7% by weight.
  • the steel sheet can optionally contain one or more alloy elements from the group (P, S,
  • Phosphorus (P) is an optional alloying element that can be adjusted in contents of up to 0.1% by weight to delay the formation of cementite and thus to stabilize the retained austenite. To ensure the desired delay and stabilization, contents of in particular at least 0.004% by weight, preferably at least 0.007% by weight, are set. However, P has a strong toughness-reducing effect and therefore has an unfavorable effect on formability. In addition, due to its very different activity in the melt and in the solidified steel, P can lead to severe segregation when the melt solidifies. Negative influences on the formability and / or weldability can be safely excluded if the content is limited to a maximum of 0.05% by weight in particular, and preferably to a maximum of 0.03% by weight to further reduce the segregation effects.
  • Sulfur (S) can be set as an optional alloy element in contents of up to 0.1% by weight in order to contribute to the ductility, for example, in a possible weld made on the sheet steel component, by precipitating it as sulphide with Mn and / or Fe a grain coarsening in the Austenite decreases after solidification.
  • a content of at least 0.0002% by weight, in particular at least 0.0005% by weight is set.
  • S in steel has a strong tendency to segregate and can negatively affect the formability or toughness as a result of the excessive formation of FeS, MnS or (Mn, Fe) S.
  • the content is therefore in particular to a maximum of 0.05% by weight, preferably to a maximum of 0.03% by weight, preferably to a maximum
  • N Nitrogen
  • N can be used as an optional alloying element in contents of up to 0.1% by weight to form nitride and / or improve hardenability.
  • N cannot be completely avoided in steel production due to the N-containing earth's atmosphere, but it can be very advantageous, depending on other alloying elements.
  • N can be just like C can be used to increase the martensite hardness, but weakens the grain boundaries less than C.
  • contents of at least at least 0.0005% by weight, preferably of at least 0.001% by weight, preferably of at least 0.002% by weight are set in particular.
  • N leads to the formation of coarse nitrides, which can have a negative effect on formability.
  • the content is therefore limited in particular to a maximum of 0.015% by weight, preferably to a maximum of 0.01% by weight, preferably to a maximum of 0.007% by weight. If Ti is present, in the case of Ti contents> 0.01% by weight, the N content should particularly preferably be set between 0.001% ⁇ N ⁇ 0.004%.
  • Chromium (Cr) can be added as an optional alloying element to adjust the hardness and strength, in particular with a content of at least 0.01% by weight, since, like C, it supports the conversion into austenite and also the formation of ferrite and pearlite during shearing can delay.
  • the upper limit is defined as 1.5% by weight. If the content is too high, the weldability and / or the toughness can be negatively influenced, so that the content is limited in particular to a maximum of 0.75% by weight, preferably to a maximum of 0.45% by weight.
  • contents of at least 0.01% by weight, preferably at least 0.1% by weight, preferably at least 0.15% by weight are added.
  • Molybdenum (Mo) as an optional alloying element can increase strength and hardness. Since it can contribute to increasing the effectiveness of Cr or can replace the use of this alloy element, it can optionally be used with a content of up to 1% by weight, in particular between 0.01 and 0.8% by weight, to achieve this the greatest possible hardness and preferably between 0.1 and 0.5% by weight to reduce carbon diffusion.
  • both Cr and / or Mo can be alloyed in addition to Mn.
  • Mn + Cr + 2 * Mo> 1% by weight.
  • Mn + Cr + 2 * Mo> 1.8% by weight.
  • titanium (Ti) can increase strength through the formation of carbides, Ni trides and / or carbonitrides and act as a micro-alloying element. Furthermore, the formation of a coarse austenite structure can be suppressed, in particular stabilize the retained austenite in dissolved form. Ti can also be used for grain refinement and / or nitrogen removal and, if boron is present, increase the effectiveness of boron. Since it can also contribute to increasing the effectiveness of Cr, it can optionally be added with a content of up to 0.2% by weight.
  • the content is limited in particular to a maximum of 0.15% by weight, to reliably avoid the formation of excessively large titanium nitrides, preferably to a maximum of 0.1% by weight, preferably to a maximum of 0.05% by weight.
  • a content of at least 0.005% by weight can be added.
  • contents of at least 0.01% by weight, preferably of at least 0.015% by weight can preferably be used.
  • boron (B) can segregate on the phase boundaries and prevent their movement. This can lead to a fine-grain structure, which can have beneficial effects on the mechanical properties.
  • B can lower the energy of austenite / austenite grain boundaries, so that the nucleation of ferrite can be suppressed during cooling.
  • Vanadium (V) and / or niobium (Nb) can be added as optional alloying elements individually or in combination for grain refinement, for residual austenite stabilization and / or for delaying hydrogen-induced cracking.
  • These optional alloying elements like Ti, can be used as micro-alloying elements in order to form strength-increasing carbides, nitrides and / or carbonitrides.
  • V and / or Nb can be used in particular with contents of (each) at least 0.005% by weight, preferably of at least 0.01% by weight, preferably of at least 0.015% by weight.
  • the minimum content, individually or in total is particularly preferably at least 0.02% by weight.
  • V is limited to a maximum of 0.5% by weight, in particular to a maximum of 0.2% by weight, preferably to a maximum of 0.1% by weight, since higher contents have a detrimental effect on the material properties, in particular on the Toughness properties of the steel.
  • Nb is limited to a maximum of 0.2% by weight, in particular special to a maximum of 0.1% by weight, preferably to a maximum of 0.06% by weight, in order to obtain as fine and finely divided niobium carbides as possible or to be able to form niobium carbonitrides.
  • nickel (Ni) can stabilize the austenite and improve the hardenability, so that a content of up to 2% by weight can optionally be added.
  • a content of at least 0.02% by weight can be added.
  • contents of at least 0.05% by weight can preferably be added, and preferably of at least 0.1% by weight to increase the toughness.
  • the content is preferably limited to a maximum of 2% by weight, for cost reasons preferably to a maximum of 1.5% by weight, particularly preferably to a maximum of 0.8% by weight.
  • Copper (Cu) can be added as an optional alloying element to improve hardenability and precipitation hardening during tempering with a content of up to 2% by weight.
  • contents of at least 0.01% by weight, preferably of at least 0.05% by weight can be added.
  • the content is in particular limited to a maximum of 1% by weight, preferably to a maximum of 0.5% by weight, in order to avoid negative influences on the weldability and the toughness properties in the heat-affected zone of a possible weld made on the sheet steel component.
  • Tin (Sn) can be added as an optional alloying element with a content of up to 0.5% by weight in order to increase the toughness and suppress the precipitation of cementite on the grain boundaries.
  • a content of at least 0.001% by weight is added.
  • a content of at least 0.002% by weight is preferably added.
  • the upper limit is restricted in particular to a maximum of 0.4% by weight, preferably to a maximum of 0.25% by weight, preferably to a maximum of 0.1% by weight.
  • Calcium (Ca) can be used as an optional alloying element of the melt as a desulfurizing agent and for targeted sulfide influence in contents of up to 0.1% by weight, in particular up to a maximum of 0.05% by weight, preferably up to a maximum of 0.01% by weight , preferably up to a maximum of 0.005% by weight, which can lead to a changed plasticity of the sulfides during hot rolling.
  • the effects described can be effective from a content of in particular at least 0.0005% by weight, preferably of at least 0.001% by weight.
  • Magnesium (Mg) can be used as an optional alloying element as an alternative or in addition to Ca in the melt for targeted sulphide influence in contents of up to 0.1% by weight, in particular up to a maximum of 0.05% by weight, preferably up to a maximum of 0.01% by weight. %, preferably up to a maximum of 0.005% by weight, which can lead to a changed plasticity of the sulfides during hot rolling.
  • the effects described can be effective from a content of in particular at least 0.0005% by weight, preferably of at least 0.001% by weight.
  • Rare earth metals such as cerium, lanthanum, neodymium, praseodymium, yttrium and others, which are abbreviated individually or collectively with SEM, can be added as optional alloying elements in order to bind S, P and / or O and the formation of oxides and / or sulfides as well To reduce or avoid phosphorus segregations at grain boundaries and thus to increase the toughness. Furthermore, SEM can contribute to the refinement of excretions and / or inclusions. In order to achieve a recognizable effect, a content of at least 0.0005% by weight, preferably of at least 0.001% by weight, is added when using SEM.
  • the SEM content is limited to a maximum of 0.1% by weight, in particular to a maximum of 0.05% by weight, preferably to a maximum of 0.01% by weight, in order not to form too many additional excretions which the Can negatively affect toughness.
  • SEM is preferably added up to a maximum of 0.005% by weight.
  • alloying elements specified as optional can alternatively also be tolerated as impurities in contents below the specified minimum limits without influencing the properties of the steel, preferably not worsening them.
  • the steel sheet is hot-rolled and preferably cold-rolled, the steel sheet, in particular in addition to the above th chemical composition, preferably less than 10% ferrite grains with an equivalent diameter> 50 ⁇ m, in order to ensure a homogeneous carbon distribution after the at least partial austenitization.
  • This is particularly advantageous in order to be able to achieve a precise amount of martensite during quenching between M s and 50 ° C., for example. If the carbon content in the austenite is increased locally, the martensite formation shifts to lower temperatures, so that less martensite can form at this point at a previously defined quenching temperature. Correspondingly, more martensite can form in places with a lower carbon content.
  • Such local, non-controllable inhomogeneities in the amount of martensite formed are not desired, for example, but can be reduced or even avoided by fine carbon distribution prior to austenitization, described by less than 10% ferrite grains with an equivalent diameter> 50 ⁇ m, preferably> 30 ⁇ m .
  • the equivalent diameter of a ferrite grain corresponds to the diameter of a circle with the same area as the ferrite grain (in the section).
  • the at least partial hardening is carried out in a press hardening tool.
  • a press hardening tool By using a press hardening tool, a particularly dimensionally stable sheet steel component can be produced, since the at least partially austenitized steel sheet comes into contact with a shaping contour of the press hardening tool.
  • the press hardening tool is actively cooled and provides corresponding cooling speeds in order to be able to set a hard structure in the at least partially hardened sheet steel component (quenching).
  • the press hardening tool effects only a slight shaping in the context of a calibration and / or correction to the nominal size or final geometry of the sheet steel component to be produced.
  • This refinement preferably takes into account indirect hot forming, a steel sheet that has already been preformed or has been formed close to its final dimensions, which is hardened or press hardened after austenitization in the press hardening tool.
  • the at least partial hardening in indirect hot forming can also be hardened in a medium, in air or in a liquid medium, in particular with or without fixing the sheet steel component to be hardened.
  • the at least partially austenitized steel sheet is hot-formed in at least one hot-forming tool before the at least partial hardening.
  • the direct hot forming preferably takes into account the provision of an essentially flat steel sheet which, after austenitization, is hot formed in at least one hot forming tool.
  • the hot forming can also be hot formed in two or more hot forming tools, depending on the complexity of the sheet steel component to be produced and / or depending on the cycle time.
  • the subsequent at least partial hardening can either additionally take place in the at least one hot forming tool by means of hot forming and press hardening or in at least one hot forming tool by means of hot forming and then in at least one press hardening tool.
  • the at least partially austenitized sheet steel in at least one hot forming tool by means of hot forming and then to harden it in a medium, in air or in a liquid medium, to form an at least partially hardened sheet steel component, in particular with or without fixing the one to be hardened Sheet steel component.
  • the at least partial tempering is carried out in at least one tempering tool which has at least two differently tempered areas / zones.
  • the at least one tempering tool is preferably constructed analogously to the hot forming tool and / or press hardening tool with contours that come into contact with the at least partially hardened sheet steel component and correspond to the final geometry of the sheet steel component to be at least partially tempered.
  • the tempering tool has at least one area (first zone) for setting the first area with the first property, which is operated with a tempering temperature TP1, and at least one further area (at least one further zone) for setting at least one of the second, third and / or fourth areas with at least the second, third and / or fourth property, this at least one further area (at least one further zone) in the tempering tool with at least one of the second, third and / or fourth tempering temperatures (TP2, TP3 and / or TP4 ) is operated.
  • the tempering tool can thus be temperature controlled differently, in particular actively temperature controlled differently.
  • the different tempering temperatures can also be set by locally different heat transfers and / or thermal conductivities in the tempering tool.
  • the at least partially hardened sheet steel component in at least one temperature control unit, which has at least two different temperature control zones for setting the different properties on the sheet steel component to be at least partially tempered.
  • the temperature control unit can be, for example, an oven with different temperature control zones, in particular with differently controllable heat sources.
  • a temperature of at least 0 ° C, in particular at least 20 ° C, preferably at least 25 ° C, preferably at least 30 ° C, more preferably at least 40 ° C, particularly preferably at least 50 ° C can prevail in at least one of the temperature control zones.
  • This temperature zone (s) cannot be actively tempered, for example.
  • the tempering duration depends on the tempering temperatures (TP1) and (TP2, TP3 and / or TP4), so that very different values are possible from ls to 3600s.
  • the at least partial starting is carried out in particular with a starting time between 5s and 100s, for a particularly time-efficient throughput with preferably a maximum starting time of 70s, preferably a maximum starting time of 50s.
  • the second teaching of the invention relates to an at least partially tempered sheet steel component which has areas with different properties, a first area with a first property containing a microstructure with retained austenite between 3% and ⁇ 35%, 35% to 97% martensite, up to 30% bainite and unavoidable structural components, and at least one further area with a further property, including at least one of the following properties:
  • Martensite can include both untempered and tempered as well as decarburized martensite.
  • Bainite if present, can include both lower and upper, as well as globular, as well as acicular bainite.
  • the at least partially tempered sheet steel component according to the invention always has a first area with a first property which ensures particularly good local deformability with high strength at the same time.
  • the at least partially tempered sheet steel component has at least one further area with at least one additional property, which is / are adjustable depending on the required properties.
  • the at least one further area can comprise a second area, a third area and / or a fourth area. Both the first area and the at least one further area can be present locally on the tempered sheet steel component in one or more sections.
  • the at least partially tempered sheet steel component can in particular have up to four different properties.
  • Remaining structural components can be present in the form of ferrite, pearlite, cementite.
  • the remaining structural components are in particular ⁇ 5%, preferably ⁇ 2%, preferably ⁇ 1%.
  • the specified structural components are determined by evaluating light or electron microscopic examinations and are therefore to be understood as area proportions in area%.
  • An exception to this is the structural component austenite or residual austenite, which is specified as a volume percentage in% by volume.
  • the first area with the first property which is present locally in one or more areas or sections of the at least partially tempered sheet steel component, has particularly good local deformability.
  • the first area with the first property contains a microstructure with retained austenite (A_RA) between 3% and ⁇ 35%, 35% to 97% martensite, up to 30% bainite and unavoidable structural components.
  • A_RA microstructure with retained austenite
  • the proportion of residual austenite with A_RA can contribute to local deformability, especially while maintaining a residual austenite stability value (S_RA), in that a low hardening exponent is achieved due to the very low hardening with increasing deformation / dislocation density, with local deformation occurring with a low increase in stress so that crack formation can be delayed by reaching a critical crack stress.
  • the retained austenite can lie lamellar between martensite lancets, which can inhibit crack propagation.
  • the presence of retained austenite can lead to an increase in dislocations in the surrounding martensite during the deformation tion can be reduced, whereby not only the deformation hardening is limited but also the hardness difference to the retained austenite. For example, this can delay the initiation of cracks.
  • the proportion of retained austenite should be limited to ⁇ 30%, preferably to ⁇ 25%, preferably to ⁇ 20%, so that the yield point in the at least partially tempered sheet steel component remains sufficiently high.
  • the optionally present second area with the second property has a higher resistance to deformation or buckling than the first area with the first property. This can be provided by a higher hardness and greater solidification compared to the first area. Due to the comparatively greater hardening, the deformation is shifted into less hardening areas, for example into the first area. In particular, due to a reduced stability (S_RA) compared to the first area, the retained austenite in the second area converts earlier due to stress and / or deformation to Marten sit, which leads to an increase in strength in the second area. As a result, the deformation shifts into the less solidified area, in particular into the first area. The somewhat more unstable retained austenite in the second area thus contributes to a deformation concentration in the first area.
  • S_RA reduced stability
  • the optionally available third area with the third property has a particularly low hardness and also solidification.
  • various functions can be mapped, in particular operations that follow after hardening, such as hole widening, can be improved; the trimming can be significantly simplified and the cutting quality improved; Welding can be made easier and the depth of the drop in hardness between the base material and the heat-affected zone of the weld seam can be significantly reduced; the provision of desired deformation points which can absorb energy at low speed in the event of a crash without further components, in particular the rest of the body, being plastically deformed, which means that the repair effort can be significantly reduced.
  • the third area contains a microstructure with a retained austenite fraction A_RA smaller than that of the first area and, if present, smaller than that of the second area.
  • the A_RA of the third area is at least 3% smaller than the A_RA of the first area, preferably less than 3% based on the A_RA of the third area (including 0).
  • the reduced residual austenite content can also reduce the amount of potentially formed stress and / or deformation-induced martensite, so that both the cutting process and local deformation operations, for example hole expansion, can be improved and thus the associated hardening can also be reduced.
  • the optionally available fourth area with the fourth property has a particularly high hardness and is especially designed for one or more areas or sections on an at least partially tempered sheet steel component in order to maintain the shape as faithfully as possible in the event of a crash with low elongation. Since the residual austenite component has no direct supporting effect in the structure due to its lower strength, a content of ⁇ 3% (including 0) should be set for the highest possible deformation resistance.
  • the first area with the first property on the sheet steel component according to the invention is designed to absorb crash energy in the event of a crash and to reduce it by deformation.
  • the first area with the first property and the at least one further area with the at least one further property can be determined by variables such as the residual austenite stability value, as given by a Si and / or Al-corrected lattice parameter (S_RA) , and / or a structural hardness value Hv_rC further characterize.
  • the first range has a value S_RA> 0.3590 nm, preferably> 0.3598 nm, particularly preferably> 0.3606 nm.
  • the residual austenite stability is reproduced by the Si and / or Al-corrected lattice parameters. This should be particularly high so that the hardening due to stress and / or deformation-induced martensite formation remains as low as possible.
  • the larger the lattice parameter the higher the proportion of alloying elements dissolved in the retained austenite lattice, where in particular C, Mn and optionally Cr can increase the retained austenite stability.
  • Si and Al are particularly effective ferrite formers, which also have an influence on the lattice parameters. Therefore, the retained austenite lattice parameter should be corrected for Si and Al, using the following formula:
  • S_RA is calculated in such a way as to compensate for the influence of the alloying element on both the lattice constant and the retained austenite stability.
  • the retained austenite lattice parameter (G_RA) is determined from the X-ray diffractogram recorded according to DIN 13925 "X-ray diffraction of polycrystalline and amorphous materials" using the Rietveld method.
  • the first area additionally or alternatively has a structural hardness value Hv_rC ⁇ 320 + 800 * (% C +% N) + 75 * (% Nb) A 0.5.
  • Various alloying elements add up to the hardness of the structure. While increases in strength due to carbon or precipitates hardly have any influence on the hardening during deformation, structural stresses lead to undesired hardening during deformation. If the above inequality is met, the grossest tensions in the structure are reduced.
  • Hv_rC is a measured hardness according to Vickers (Hvl).
  • Hvl Vickers
  • the tempering effect lower hardness than fully hardened (martensite depending on C and N) and hardened / grain refined (precipitations depending on Nb) is taken into account.
  • the condition requires a hardness that is less than the maximum hardness that could be achieved taking into account the chemical composition.
  • the optional second area with the second property has a value S_RA which is smaller than the S_RA of the first area.
  • S_RA is at least 0.0004 nm smaller than the S_RA of the first area . If the S_RA is preferably at least 0.0010 nm smaller than the S_RA of the first area, it is possible to achieve a high level of retained austenite conversion in the second area while at the same time minimizing the residual austenite conversion in the first area.
  • the optional second area with the second property alternatively or additionally has a value Hv_rC that is greater than the Hv_rC in the first area, so that the deformation mainly occurs in areas of lower hardness if only a first area and no third area is present, so rather takes place in the first area.
  • the Hv_rC is at least 10 Hv greater than the Hv_rC in the first area.
  • the Hv_rC of the second area is up to a maximum of 120 Hv, more preferably up to a maximum of 100 HV greater than the Hv_rC in the first area, preferably up to a maximum of 40 Hv greater than in the first area. It can thus be ensured that the deformation of the component in the event of a crash also extends to the second area before the first area fails critically.
  • the optional third area with the third property has a residual austenite content that is kept low, so that a specific residual austenite stability does not necessarily have to be set. If the residual austenite content in the third area is A_RA> 0, the value S_RA> 0.3595 nm, in particular S_RA> 0.3600 nm, is set in order to be able to essentially suppress the formation of martensite induced by stress and / or deformation.
  • the optional third area with the third property alternatively or additionally has a value Hv_rC that is at least 10 HV smaller than the Hv_rC in the first area, preferably at least 25 HV smaller than the Hv_rC in the first area, for improved hole expansion , preferably by at least 50 Hv smaller than the Hv_rC in the first area, in order to enable cutting edges of the highest quality and low cutting forces.
  • the optional fourth area with the fourth property has, if a residual austenite content A_RA between> 0% and ⁇ 3% is present, a value S_RA ⁇ 0.3595 nm, in particular S_RA ⁇ 0.3590 nm, in order to convert the residual austenite into martensite as quickly as possible to convert and thus contribute to deformation resistance.
  • the optional fourth area with the fourth property additionally or alternatively has a value Hv_rC which is at least 40 Hv greater than the Hv_rC of the first area in order to direct the deformation into other areas when the component is loaded.
  • the Hv_rC is at least 60 Hv, preferably at least 80 Hv, greater than the Hv_rC in the first area in order to keep the tempered sheet steel component as close as possible to its original shape in the event of a crash.
  • the Hv_rC of the fourth area is at least 10 Hv greater than the Hv_rC of the second area.
  • the at least partially tempered sheet steel component has one or more transition areas between the areas with different properties, the transition area or areas spacing the different areas apart from one another by a transverse extent of at least 5 mm in order to create a harmonic and to provide non-abrupt transition of the course of properties between the individual areas with different properties
  • the transverse extension is in particular at least 20 mm, preferably at least 50 mm.
  • the transverse extent of the transition area between the individual areas is, for example, a maximum of 400 mm, in particular a maximum of 250 mm, preferably a maximum of 150 mm, preferably a maximum of 100 mm.
  • the transverse extent of the transition area between the areas of different properties is particularly preferably between 10 mm and 50 mm, which is particularly advantageous for a component design and forecast quality of the usage properties.
  • Figure 1 a schematic flow chart of an embodiment of the method according to the invention according to a first embodiment
  • Figure 2 a schematic flow chart of an embodiment of the method according to the invention according to a second embodiment
  • Figure 3 a schematic flow chart of an embodiment of the method according to the invention according to a third embodiment
  • Figure 4 a schematic flow chart of an embodiment of the method according to the invention according to a fourth embodiment
  • Figure 5 a schematic flow chart of an embodiment of the method according to the invention according to a fifth embodiment
  • FIG. 6 a schematic flow chart of an embodiment of the method according to the invention according to a sixth embodiment
  • FIG. 7 a schematic perspective view of a tempered sheet steel component according to a first exemplary embodiment
  • FIG. 8 a schematic perspective view of a tempered sheet steel component according to a second exemplary embodiment
  • FIG. 9 a schematic perspective view of a tempered sheet steel component according to a third exemplary embodiment.
  • FIGS. 1 to 6 schematic flow charts of different configurations of the method according to the invention are shown.
  • the device (0) denotes a device or device for forming a steel sheet, in which the steel sheet is shaped or reshaped, in particular shaped close to the final dimensions, preferably cold shaped or reshaped, in order to provide a preformed steel sheet for the further process.
  • the device (I) comprises means for shaping the steel sheets.
  • the device (0) can be designed in the form of one or more tools.
  • the device (I) denotes a device or device for at least partial austenitizing of a steel sheet provided, in which the steel sheet is austenitized to a temperature of at least Acl, in particular of at least Ac3 or above Ac3.
  • the device (I) comprises means for at least partially heating the steel sheets provided.
  • the steel sheet provided can also be completely heated or austenitized.
  • the device (I) can be designed in the form of an oven, for example in the form of a continuous oven.
  • (II) denotes a device or device for at least partially hardening an at least partially austenitized steel sheet, in which the at least partially austenitized steel sheet is hardened to an at least partially hardened steel sheet component, the at least partially austenitized steel sheet to a temperature below Ms is cooled.
  • the device (II) comprises means for active cooling of the at least partially austenitized steel sheets, which, for example, comprises at least one tool and / or a medium for hardening.
  • the at least one tool can be designed as a press hardening tool (II.1), as a hot forming and press hardening tool (11.2), as a hot forming, press hardening and tempering tool (11.2, III) or as a press hardening and tempering tool (II.1, III) .
  • the at least one tool can furthermore have additional functions, for example comprise means for trimming and / or punching (IV).
  • (III) denotes a device or device for at least partially tempering an at least partially hardened sheet steel component, in which the at least partially hardened sheet steel component is tempered to form an at least partially tempered sheet steel component, the at least partially hardened sheet steel component to a temperature of less than Acl is left on.
  • the device (III) comprises means for actively tempering the at least partially hardened sheet steel components, which for example includes at least one tool and / or a medium for tempering, different temperature zones being provided in order to different areas (2) on the sheet steel component (1) to be at least partially tempered , 3, 4, 5) with different properties.
  • the at least one tool can be designed as a tempering tool (III.1) separately or integrated in a tool, in particular for hot forming and / or press hardening (II.1, 11.2).
  • the at least one tool can furthermore have additional functions, for example comprise means for trimming and / or punching (IV).
  • the device (IV) denotes a device or device for reworking an at least partially tempered sheet steel component, in which the at least partly tempered sheet steel component is reworked, in particular cut and / or perforated.
  • the device (IV) comprises means for processing the at least partially tempered sheet steel components. If the device (IV) comprises means for trimming and / or punching, it can be thermal means, for example in the form of a laser, or mechanical means, for example one or more cutting and / or punching tools.
  • the device (IV) can be designed separately or integrated in a tool, in particular for hot forming and / or press hardening (II.1, 11.2) or tempering (III).
  • FIG. 1 shows four separate devices (I, II, III, IV) in which the method according to the invention for producing a tempered sheet steel component (1) according to the invention can be implemented.
  • a flat steel sheet is provided and completely austenitized in a furnace (I) to a temperature above Ac3.
  • the austenitized steel sheet is then removed from the furnace (I) and transferred using suitable transfer means to a hot forming and press hardening tool (11.2), in which the austenitized steel sheet is hot formed and cooled to a temperature below Ms and thus hardened into a steel sheet component .
  • the hardened sheet steel component is then transferred to a tempering tool (III) by means of suitable transfer means, in which the hardened sheet steel component at different temperatures becomes a tempered sheet steel component (1) Areas (2, 3, 4, 5) is tempered with different properties.
  • the tempered sheet steel component (1) can then be transferred to a tool (IV) for trimming and / or punching, for example by means of a laser with suitable transfer means. After the trimming and / or perforation in the tool (IV), the ready-made, tempered sheet steel component (1) can be removed.
  • the devices (III, IV) are combined in one device or in one tool in comparison to the first embodiment in FIG. 1.
  • the tempering tool (III) has the additional function of additionally mechanically processing or reworking the sheet steel component to be tempered, in particular cutting and / or punching, for example via cutting and / or punching tools additionally integrated or arranged in or on the tempering tool (III) or punching tools (IV).
  • the devices (II, III, IV) are combined in one device, such as, for example, a transfer press, or in one tool.
  • the hot forming and press hardening tool (11.2) is also the tempering tool (III) and also has cutting and / or punching tools (IV). It can also be implemented in such a way that the devices (II, III, IV) are installed separately or at least partially separately from one another in one device.
  • the devices (II, III) are combined in one device or in a tool.
  • the tool includes a hot forming, press hardening and tempering tool (11.2, III).
  • the device (IV) for reworking is designed separately.
  • the fifth embodiment in Figure 5 also shows four separate devices (0, 1, II, III), in contrast to the first four embodiments, in which a substantially flat sheet steel in the form of a plate is provided and then austenitized, here and also in the sixth embodiment, a preformed steel sheet is provided for austenitizing. Since the preformed steel sheet preferably already has a geometry close to its final dimensions, no hot forming is necessary either, so that the hardening is carried out in a press hardening tool (II.1) in the device (II). Post-processing in a further device, not shown, is conceivable if necessary.
  • the devices (II, III) are combined in one device in one tool.
  • the tool includes a press hardening and tempering tool (II.1, III).
  • the device (IV) for reworking is designed separately.
  • melts A, B and C with the chemical composition specified in Table 1 were cast into a strand in a continuous caster and each divided into slabs.
  • the slabs were then heated through in a walking beam furnace at temperatures above 1100 ° C. and hot-rolled in a hot strip mill to form a hot strip with a diameter of 3.2 mm.
  • the hot strips were conditioned and then cold-rolled to form 1.5 mm cold strips.
  • the cold strips produced from melts A and C were conventionally coated with an aluminum-silicon coating, whereas the cold strip produced from melt B remained uncoated.
  • Seven steel sheets each were cut out of the cold strip produced from melt A and C as well as from the cold strip made from melt B and subjected to cold forming in a device (0), each being provided in the form of a preformed steel sheet.
  • the total of 21 steel sheets provided were austenitized in an oven (I) completely above Ac3 at an oven temperature of 920 ° C. for a period of 300 s, see Table 2.
  • the austenitized steel sheets were which is transferred to a press hardening tool (II.1) with a transfer time of 7s, in which the austenitized steel sheets are cooled or quenched and thus hardened to form sheet steel components.
  • the temperature of the press hardening tool (II.1) for the AS-coated steel sheets was a uniform 224 ° C. and for the uncoated steel sheets a uniform 240 ° C., the holding time of the press hardening tool (II.1) being 6s in each case.
  • the measured removal temperatures of the hardened sheet steel components are shown in Table 2.
  • the tempering tool (III) had four different temperature-controlled zones in order to be able to set areas (2, 3, 4, 5) with up to four different properties on the sheet steel component (1) to be treated.
  • the set temperatures in the respective zones of the tempering tool (III), as well as the measured tempering temperatures TP1 to TP4 in the corresponding areas (2, 3, 4, 5) with different properties on the tempered sheet steel components (1) when removed from the tempering tool (III), as well as the corresponding holding times of the tempering tool (III) for setting the different properties can be found in table 2.
  • the tempered sheet steel components (1) according to embodiment 1, 6 and 7 are shown by way of example in FIGS. 7, 8 and 9 as a schematic perspective view.
  • sheet steel components can be produced which are only partially austenitized, only partially hardened and only partially tempered.
  • FIG. 7 shows a tempered sheet steel component (1) with a first area (2) with a first property and a fourth area (5) with a fourth property, with a transition area (1.1) defining the two areas (2, 5) Distance in the transverse extent (Q) separates from each other, the transverse extent (Q) being at least 10 mm.
  • FIG. 8 shows a tempered sheet steel component (1) with three first areas (2) with a first property, two third areas (4) with a third property and a fourth area (5) with a fourth property, with transition areas (1.1) being different Zones (2, 4, 5) separate from each other at a defined distance in the transverse direction (Q).
  • the three first areas (2) are present in sections on the tempered sheet steel component (1), with two third areas (4) being present between the three first areas (1).
  • the fourth area (5) defines an end section on the tempered sheet steel component (1).
  • FIG. 9 shows a tempered sheet steel component (1) with two first areas (2) with a first property, a second area (3) with a second property, two third areas (4) with a third property and one fourth area (5) with a fourth property, wherein transition areas (1.1) separate the different areas (2, 3, 4, 5) each Weil with a defined distance in the transverse direction (Q).
  • the transition area (1.1) between the first third area (4) and the second first area (2) is wider in its transverse extent (Q) compared to the other transition areas (1.1).
  • Table 3 provides a detailed overview of the different properties that had arisen in the respective areas (2, 3, 4, 5) on the tempered sheet steel components (1) through the inventive method, as indicated in Table 2.
  • the tempering temperatures relate to the temperature in the corresponding areas (2, 3, 4, 5) on the tempered sheet steel component (1) at or shortly after Removal from the tempering tool (III). They cannot and do not have to correspond to the mold temperatures in the zones that are in contact with the areas (2, 3, 4, 5).
  • Hv_rC Vickers hardness (Hvl)
  • A_RA, G_RA Both parameters were determined from the X-ray diffractogram recorded according to DIN 13925 "X-ray diffractometry of polycrystalline and amorphous materials" using the Rietveld method.
  • T_WkzA Tool temperature press hardening tool
  • T_Abs Temperature of the component when it is removed from the press hardening tool
  • T_WkzX Temperature of the tempering tool in the tool area X (X: l-4)
  • TPX component temperature in the area in contact with tool area X of the tempering tool
  • Hv_rC Vickers hardness (Hvl)
  • A_RA Share of retained austenite in the structure (% by volume)
  • G_RA lattice constant of the retained austenite
  • the inventive method inexpensive sheet steel components can be produced with targeted properties, in particular body parts such as A-pillars, B-pillars or longitudinal and cross members, but also combinations thereof, for Example a door ring.
  • the method according to the invention is applicable not only to monolithic, thick, constant steel sheets, but also to monolithic, thickness-varying steel sheets (tailored rolled blanks).
  • the method according to the invention can also be applied generally to tailored products, for example at least two steel sheets connected to one another in the form of “patchwork blanks” or “tailer welded blanks” with different thicknesses and / or qualities.

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

Abstract

L'invention concerne un procédé de fabrication d'un élément en tôle d'acier au moins partiellement trempée et revenue, le procédé consistant en les étapes suivantes : fourniture d'une tôle d'acier, austénitisation au moins partielle de la tôle d'acier à une température au moins égale à Ac1, durcissement au moins partiel de la tôle d'acier au moins partiellement austénitisée pour obtenir un élément en tôle d'acier au moins partiellement durci, la tôle d'acier au moins partiellement austénitisée étant refroidie à une température inférieure à Ms, recuit au moins partiel de l'élément en tôle d'acier au moins partiellement durci à une température inférieure à Ac1 pour produire un élément en tôle d'acier au moins partiellement trempée et revenue. L'invention concerne en outre un élément en tôle d'acier au moins partiellement trempée et revenue.
EP20776138.8A 2019-09-30 2020-09-22 Procédé de fabrication d'un élément en tôle d'acier au moins partiellement trempée et revenue et élément ainsi fabriqué Pending EP4038213A1 (fr)

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DE102019215053.5A DE102019215053A1 (de) 2019-09-30 2019-09-30 Verfahren zur Herstellung eines zumindest teilweise vergüteten Stahlblechbauteils und zumindest teilweise vergütetes Stahlblechbauteil
PCT/EP2020/076399 WO2021063747A1 (fr) 2019-09-30 2020-09-22 Procédé de fabrication d'un élément en tôle d'acier au moins partiellement trempée et revenue et élément ainsi fabriqué

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CN114450423A (zh) 2022-05-06
CN114450423B (zh) 2023-12-05

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