EP2569112A1 - Procédé de réalisation d'une pièce à partir d'une tôle d'acier au ferromanganèse - Google Patents

Procédé de réalisation d'une pièce à partir d'une tôle d'acier au ferromanganèse

Info

Publication number
EP2569112A1
EP2569112A1 EP11720423A EP11720423A EP2569112A1 EP 2569112 A1 EP2569112 A1 EP 2569112A1 EP 11720423 A EP11720423 A EP 11720423A EP 11720423 A EP11720423 A EP 11720423A EP 2569112 A1 EP2569112 A1 EP 2569112A1
Authority
EP
European Patent Office
Prior art keywords
sheet metal
metal workpiece
workpiece
calibration
temperature
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.)
Granted
Application number
EP11720423A
Other languages
German (de)
English (en)
Other versions
EP2569112B1 (fr
Inventor
Ludovic Samek
Martin Peruzzi
Enno Arenholz
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Stahl GmbH
Original Assignee
Voestalpine Stahl GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Voestalpine Stahl GmbH filed Critical Voestalpine Stahl GmbH
Publication of EP2569112A1 publication Critical patent/EP2569112A1/fr
Application granted granted Critical
Publication of EP2569112B1 publication Critical patent/EP2569112B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D31/00—Other methods for working sheet metal, metal tubes, metal profiles
    • 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
    • C21D1/30—Stress-relieving
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below

Definitions

  • the invention relates to a method for producing a component from an iron-manganese steel sheet.
  • Iron-manganese steels are lightweight steels that can have high strength and high ductility at the same time. This makes iron-manganese steels a material with great potential in vehicle construction. A high material strength allows a reduction of the body weight, where ⁇ by the fuel consumption can be reduced. High extensibility and stability of the steels is important both for the production of the body parts by deep-drawing processes and for their crash behavior. For example, structure and / or safety parts such as
  • Door impact beams, A- and B-pillars, bumpers or longitudinal and transverse beams can realize complex component geometries and at the same time achieve the weight targets and safety requirements.
  • Hot forming Conventional hot forming processes are carried out at high temperatures of about 900 ° C or above. Hot working reduces both springback of the formed component and strain hardening in formed areas. Thus, with the hot forming technique complex deep drawn parts can be produced without appreciable spring-back in one go.
  • a disadvantage of hot forming is the high process temperatures and the material-dependent reduction in the strength of the component after the cooling process, caused by the hot forming.
  • hot forming is often combined with hardening technology. This is based on the known possibility of strengthening of steel materials by martensite formation. Upon curing an austenitic structure is generated by a heating of the component on the so-called hardness ⁇ temperature above Ac3, which is subsequently converted by rapid cooling TENSIT completely in Mar-. Condition for the full Mar- TENSIT conversion is that a critical Abkühlge ⁇ speed is exceeded. For this purpose, it requires cooled pressing tools that allow a sufficiently rapid cooling of the workpiece by contact of the hot workpiece surface with the cold tool surface.
  • An object of the invention is based can be seen to provide a method with which the production of formed parts made of iron-manganese steel sheet with good mechanical properties is made possible cost.
  • the method should be the Manufacture of formed sheet metal workpieces with complex component geometry and favorable material properties even in formed component areas.
  • the problem underlying the invention is solved by the features of claim 1.
  • Advantageous embodiments and refinements are specified in the dependent claims.
  • Sheet metal workpiece is calibrated in a calibration tool.
  • elevated temperatures can be achieved that a cold work hardening occurred in the cold forming is degraded again in the formed areas.
  • homogenization of the mechanical properties over the entire component can thereby be achieved. Further advantages of the inventive method is to se ⁇ hen that embrittlement than the calibration of the heated component both the risk of delayed cracking by hydrogen-also the resilience of the component after removal from the calibration are substantially reduced.
  • the degree of degradation of strain hardening in the reformed part regions can be controlled by the choice of temperature. At high temperatures, the strength of the molded areas are even lowered below the strength in not or we ⁇ niger heavily deformed areas. In order to avoid excessive degradation of work hardening, a temperature between 600 ° C and 680 ° C may be advantageous.
  • a temperature between 600 ° C and 680 ° C may be advantageous.
  • the initial temperature may be Tempe ⁇ during calibration also in the specified range between 500 ° C and 700 ° C.
  • a cooling of the formed sheet metal workpiece takes place in a held or fixed state.
  • the residence time of the sheet metal workpiece in the furnace can be so ge be ⁇ selected so that a homogeneous heating of the sheet metal workpiece is ensured, taking into account that with increasing thickness of the sheet metal workpiece .rwei- se an extension of the time duration for the warming-up operation to be estimated is.
  • the heating temperature of the converted shaped sheet metal workpiece of importance For the reduction of strain hardening in formed sections of the sheet metal workpiece, the heating temperature of the converted shaped sheet metal workpiece of importance.
  • it can be adjusted so that the Kaltver ⁇ fortification in the reshaped portions of the (transformed)
  • Blechwerk Spanish by the calibration by at least 70%, in particular at least 80%, is degraded.
  • the Erracer ⁇ mung temperature of the sheet metal workpiece can be adjusted so that the calibrated sheet workpiece over its entire geometry of a maximum fluctuation range of the tensile strength of
  • Fig. 1 is a schematic representation of a sequence of
  • Fig. 2 is a graph in which the hardness of a formed component is plotted against a distance from the Umformort.
  • the component may be, for example, a body component for vehicle construction.
  • the chassis ⁇ riebauteil may have a complex part geometry. It may be a structural and / or safety part, which may be required to meet special security requirements at Be ⁇ lastungsfall (crash).
  • the component may be an A or B pillar, a side pillar Impact protection zhari in doors, a sill, a frame part, a bumper, a cross member for floor and roof or to act on a front or rear side member.
  • the component consists of an iron-manganese (FeMn) steel.
  • FeMn components are known in the vehicle and may have a manganese ⁇ content of about 12 to 35 wt%.
  • TWIP, TRIP / TWIP and TRIPLEX steels as well as mixed forms of these steels can be used.
  • TWining steels are austenitic steels. They are characterized by a high manganese content (for example over 25%) and relatively high alloying additions of aluminum and silicon. In cold plastic deformation, intensive twin formation takes place, which solidifies the steel. TWIP steels have a high elongation at break. They are therefore particularly suitable for the production of structural or safety components in accident-relevant areas of the body.
  • TRIP / TWIP steels are combinations of TWIP and TRIP steels (TRANSformation Induced Plasticity).
  • TRIP steels are ⁇ be essentially of a plurality of phases of iron-carbon alloys, namely ferrite, bainite and carbon-rich residual austenite.
  • the TRIP effect is based on the deformation-induced transformation of residual austenite into the high-strength martensitic phase (CC martensite).
  • CC martensite high-strength martensitic phase
  • TRIP / TWIP steels a double TRIP effect occurs because the austenitic structure is first converted into the hexagonal and then into the ku ⁇ bisch centered martensite. Due to the two martensitic transformations TRIP / TWIP steels have a double expansion reserve.
  • TRIPLEX steels consist of a multiphase microstructure of 0C ferrite and ⁇ -austenite mixed crystals with a martensitic s-phase
  • combinations of said steels may be used in embodiments of the invention.
  • the list of examples of the above steel is not from ⁇ closing, other FeMn steels can likewise for the invention if used.
  • Fig. 1 shows schematically an embodiment of a method according to the invention, wherein also optional Ver ⁇ drive steps are shown.
  • the starting point of procedural rensablaufs a coil of steel strip 1 as example ⁇ example is made in a steel mill and to a customer (eg vehicle manufacturer or supplier) is shipped.
  • the FeMn strip steel may be, for example, a cold-rolled and annealed steel. However, it is also possible to use a hot-rolled steel.
  • the manufacturing process of FeMn strip steel in the steel plant should be designed from ⁇ that a good cold formability of the steel is guaranteed.
  • the steel strip is then cut, for example, in the vehicle manufacturer or supplier in FeMn boards 2. The cutting takes place in a cutting station.
  • One or more boards 2 are then placed in a cold forming tool 3 and cold formed.
  • the temperatures in the cold forming tool can be in the usual range, for example at about 70 ° C to 80 ° C. Furnaces are not used to realize these temperatures.
  • the residence time of the workpiece in the cold forming tool 3 is typically without any significant influence on the workpiece properties.
  • locally different strengths are achieved depending on the component geometry. The greater the local degree of deformation, the higher the corresponding strength value. This effect is also called cold work hardening. It can strong Kaltverfesti ⁇ conditions occur up to about 1800 MPa. The tensile strength of the
  • MPa are, the yield strength, for example, R p0 .2 ⁇ 600 MPa and the elongation at break A of the starting material may be, for example, 40% or more (A> 40%).
  • the Kaltumformwerkmaschine 3 can be implemented in the form ei ⁇ ner deep drawing press.
  • This crop may be the final crop of the
  • any necessary punching or the creation of a hole pattern in the cold forming tool 3 can be made. Ie, after the cold forming a component with fully ready meals imputed component shape in terms of material removing Prozes ⁇ se may already exist.
  • the residence time may be minutes in the oven 10, where 5 min used for the achievement of homogeneous Temperaturvertei ⁇ lung and another 5 min for holding the component at this homogeneous temperature.
  • a radiation furnace can be used or it can be provided furnaces that supply the workpiece in another way energy.
  • a convective heating, an inductive heating or an infrared heating, as well as combinations of said mechanisms may be used.
  • the heated to the target temperature between 500 ° C and 700 ° C, formed workpiece is then removed from the oven 4, placed in a calibration tool 5 and fixed there in the desired shape and cooled.
  • the temperature of the workpiece at the beginning of the calibration process may also be lower than the temperature of the workpiece during removal from the furnace, it may in particular be between 400 ° C and 700 ° C.
  • the calibration tool 5 may be, for example act a sizing press. Calibration ensures the dimensional accuracy of the workpiece.
  • the surface geometry of the pressing surfaces of the tool corresponds to the final shape of the workpiece or is very close to the final shape, since the calibration in the calibration tool significantly reduces springback. By holding the workpiece in the calibration tool in the desired shape thus the workpiece is given the final shape.
  • the cooling of the workpiece takes place in the calibration tool 5 when the workpiece is fixed, ie when the workpiece surfaces abut the tool surfaces.
  • the heat dissipation takes place via the tool.
  • the cooling rate may be, for example unge ⁇ ferry 30 ° C / s, however, is likely to be critical since Toggle DERS than the press hardening no critical Abkühlgeschwindig ⁇ ness must be exceeded.
  • the Ab ⁇ cooling rate may be less than 50 ° C / s, which is achievable without size ⁇ ren tool technical effort and in many cases allows sufficient short cycle times. Higher cooling rates, for example in the range from 50 ° C / s to 150 ° C / s, are also possible.
  • the calibration tool 5 may have a cooling device (eg water cooling).
  • a cooling device eg water cooling
  • Another possibility is to realize the furnace 4 and the calibration tool 5 in one and the same ⁇ press station, ie to provide a calibration tool 5, which is coupled to a furnace.
  • coated FeMn steels can be used for the process.
  • the sheet metal workpiece can be coated with an organic and / or inorganic or metallic coating, in particular an alloy based on zinc or aluminum.
  • the coating can be done before cold forming or at another time, eg after calibration.
  • a cathodic corrosion protection is effected for example by a galvanizing.
  • the coating can be carried out electrolytically or by a hot-dip method before the cold-forming step 3 (for example, already at the steel manufacturer on the coil 1) or after the cold-forming step 3 and before heating in the furnace 4.
  • a mixed crystal layer forms between the FeMn steel and the Zn coating in the case of a Zn coating, which ensures good adhesion of the Zn layer on the component.
  • Fig. 2 relates to further embodiments of the hand at ⁇ Fig.
  • Fig. 2 shows for the cold-drawn, not him ⁇ warmed cups work hardening in the range of
  • the hot calibration according to the invention leads to the reduction of strain hardening in the wells.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Health & Medical Sciences (AREA)
  • Child & Adolescent Psychology (AREA)
  • Heat Treatment Of Articles (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

L'invention concerne un procédé permettant de réaliser une pièce à partir d'une tôle d'acier au ferromanganèse (1), selon lequel une pièce à usiner en tôle (2) est soumise à un formage à froid dans un outil de formage (3). La pièce à usiner en tôle mise en forme est chauffée (4) à une température comprise entre 500 °C et 700 °C et est calibrée dans un outil de calibrage (5).
EP11720423.0A 2010-05-12 2011-05-06 Procédé de réalisation d'une pièce à partir d'une tôle d'acier au ferromanganèse Active EP2569112B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE201010020373 DE102010020373A1 (de) 2010-05-12 2010-05-12 Verfahren zur Herstellung eines Bauteils aus einem Eisen-Mangan-Stahlblech
PCT/EP2011/057280 WO2011141367A1 (fr) 2010-05-12 2011-05-06 Procédé de réalisation d'une pièce à partir d'une tôle d'acier au ferromanganèse

Publications (2)

Publication Number Publication Date
EP2569112A1 true EP2569112A1 (fr) 2013-03-20
EP2569112B1 EP2569112B1 (fr) 2019-10-23

Family

ID=44276268

Family Applications (1)

Application Number Title Priority Date Filing Date
EP11720423.0A Active EP2569112B1 (fr) 2010-05-12 2011-05-06 Procédé de réalisation d'une pièce à partir d'une tôle d'acier au ferromanganèse

Country Status (7)

Country Link
US (1) US9138797B2 (fr)
EP (1) EP2569112B1 (fr)
KR (1) KR101567132B1 (fr)
CN (1) CN103003002B (fr)
DE (1) DE102010020373A1 (fr)
ES (1) ES2764790T3 (fr)
WO (1) WO2011141367A1 (fr)

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WO2024199639A1 (fr) * 2023-03-28 2024-10-03 Voestalpine Metal Forming Gmbh Procédé de production d'éléments en acier trempé

Also Published As

Publication number Publication date
ES2764790T3 (es) 2020-06-04
US20130125607A1 (en) 2013-05-23
CN103003002B (zh) 2016-03-30
KR20130036250A (ko) 2013-04-11
DE102010020373A1 (de) 2011-11-17
US9138797B2 (en) 2015-09-22
CN103003002A (zh) 2013-03-27
KR101567132B1 (ko) 2015-11-06
WO2011141367A1 (fr) 2011-11-17
EP2569112B1 (fr) 2019-10-23

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