EP2480693B1 - Edelstahl mit lokalen variationen der mechanischen beständigkeit - Google Patents

Edelstahl mit lokalen variationen der mechanischen beständigkeit Download PDF

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Publication number
EP2480693B1
EP2480693B1 EP09740179.8A EP09740179A EP2480693B1 EP 2480693 B1 EP2480693 B1 EP 2480693B1 EP 09740179 A EP09740179 A EP 09740179A EP 2480693 B1 EP2480693 B1 EP 2480693B1
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EP
European Patent Office
Prior art keywords
sheet
mechanical resistance
steel sheet
martensitic
local
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Not-in-force
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EP09740179.8A
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English (en)
French (fr)
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EP2480693A1 (de
Inventor
Pierre-Olivier Santacreu
Aurélien PIC
Fabrice Pinard
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Aperam SA
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Aperam SA
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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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D1/06—Surface hardening
    • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

Definitions

  • the present invention relates to the forming of stainless steel sheets and more particularly those having high mechanical strengths.
  • Stainless steel sheets are widely used in the automotive, construction and general industrial sectors because of their excellent resistance to corrosion.
  • these sheets are generally shaped to be used, for example, in the form of profiles, square tubes, bumper beams, stretchers, door frames. These shaping are most often performed by folding, profiling and stamping.
  • DE102006059885 discloses a carbon steel component for a motor vehicle, having a surface with a structural variation in some areas, laser-treated to form a three-dimensional resistance-improving structure.
  • FR2864108 discloses a stainless steel sheet having high mechanical strength and good elongation, and whose properties are homogeneous.
  • the patent US5,735,163 thus describes a blank shaping process in which a local portion of the blank is cured before shaping. This hardening is generated by a high density energy supply. The resulting rise in temperature results in the transformation of the local microstructure into martensite or bainite, which locally increases the mechanical strength.
  • the formation of hardened lines parallel to the direction of the deformation makes it possible to avoid the breaking of indefinable shades.
  • the structural transformation related to the formation of martensite or bainite on the outer side of the blank to be bent generates a local compressive stress. During folding, this constraint partially cancels the extension stress generated by folding, thus limiting the springback.
  • this process solves only one of the problems mentioned above.
  • this process can not be applied to steels having a high mechanical strength, already sufficiently difficult to implement.
  • this process assumes the use of steels capable of undergoing a martensitic or bainitic phase transformation during annealing followed by quenching, which in fact limits its use to carbon-manganese steels.
  • the present invention aims to facilitate the forming of stainless steel sheets having a high mechanical strength. It has been designed and realized to overcome the defects presented previously and to obtain other advantages.
  • the invention firstly relates to a stainless steel sheet containing a minimum of 10.5% by weight of Cr and a maximum of 1.2% by weight of C, the microstructure of which is martensitic or austenitic. martensitic and comprises at least 2% by volume of martensite.
  • This sheet is essentially characterized in that it comprises at least one local portion of lower mechanical strength, having a martensite rate at least 10% lower than that of the remainder of said sheet; said local portion being at least partially of a thickness equal to that of said sheet.
  • a third object of the invention consists of a steel part obtainable by deformation of a steel sheet according to the invention or of a sheet obtained by the method according to the invention, said deformation taking place in at least one of said local portions of lower mechanical strength.
  • the terms 2H, C700 to C1300 (called hardened state), 1E, 1D, 2B, 2D, 2R, 2E (so-called annealed condition) refer in particular to the standards which define the production ranges and the technical delivery conditions of the steels concerned. (NF EN 10088-1 and -2 for stainless steels). C1500 will designate a range of manufacture of a 2H hardened nut ensuring a mechanical strength higher than 1500MPa.
  • the stainless steel sheets considered by the present invention are characterized by their mechanical strength. This is controlled on the one hand by the addition elements, but also by the heat treatments and the mechanical treatments that the sheet can undergo.
  • This composition features an austenitic stainless steel that solidifies to primary ferrite and contains a non-zero amount of work hardening martensite after deformation. Although predominantly austenite, conventional austenitic grades contain traces of residual ferrite from the solidification as well as traces of martensite resulting from rolling operations.
  • Heat treatment and mechanical treatment allow, in turn, to modify this mechanical strength in a certain proportion.
  • a homogeneous work hardening (production range 2H: C700 to C1500) on the entire sheet results in a partial transformation of the austenite to martensite and possibly a hardening of the austenite by densification. of the dislocation network.
  • This hardening achieves mechanical strengths well above 780 MPa, maximum value achievable on a stainless steel annealed type 1D, 1E, 2B, 2D, 2E, 2R.
  • the steel thus worked is of austeno-martensitic structure that is to say formed at ordinary temperature of a mixture of austenite and martensite, the volume fraction of martensite being at least 2%.
  • a localized heat treatment to the zones to be deformed causes a partial reversion of the martensite to austenite and possibly a softening of the austenite by reducing the number of dislocations.
  • This heat treatment makes it possible to lower the mechanical resistance of the sheet locally. A portion of lower mechanical strength is thus obtained.
  • This mechanical resistance can be lowered up to 500 MPa, the minimum achievable on annealed austenitic stainless steel.
  • This heat treatment can be performed without this list being exhaustive, by laser, by induction, by electron beam or by welding with the wheel.
  • the thermal cycle includes in particular a temperature rise above the transformation start temperature of martensite to austenite, called reversion temperature of martensite.
  • This temperature is a function of the grade of steel considered but within the scope of the invention, and to cover all the austenitic grades, the reversion temperature is higher than 550 ° C.
  • the durations of the heat treatment, heating, maintenance and cooling are a function of the grade of the sheet, its thickness and the method used: they must be determined beforehand and must allow a minimum decrease of 10% of the volume fraction of martensite and possibly the dislocation density. This minimal decrease makes it possible to overcome the local variations inherent in the cold-working process. A partial melting of the steel on the surface of the sheet and on a thickness not exceeding 0,5e is admissible.
  • the heat treated area is quenched by self-cooling, the heat being transmitted to the surrounding areas. This phenomenon eliminates the control of quenching parameters for obtaining a sheet according to the invention.
  • a stainless steel sheet according to the invention can be shaped according to the usual techniques well known to those skilled in the art, among which may be mentioned as examples folding, profiling, stamping. During this shaping, the portion of lower mechanical strength, which encompasses the deformed zone undergoes hardening. A partial transformation of the austenite into martensite and possibly a hardening of the austenite by densification of the dislocation network make it possible to recover at least partially the initial microstructure of this portion of the sheet.
  • a steel piece, shaped at the level of at least one of the lower strength portions of a steel sheet according to the invention is characterized by the presence, in the vicinity of the neutral fiber, of a zone having a martensite rate lower than that of the sheet.
  • the detection of this zone can be made by measurement of residual stresses or by measurement of the martensite fraction.
  • neutral fiber is meant the set of points which, in case of application of a global deformation, do not undergo local deformation.
  • the local portions of lesser mechanical strength may not be shaped and serve as preferential zones of deformation during dynamic loading, typically at deformation rate of between 1 and 1000s -1 as the crash.
  • the measurement of the martensite ratio is performed by a local measurement of the magnetic induction - using a ferritescope. This measurement gives an average percentage by volume of martensite on the thickness of the sheet.
  • This indirect measurement assumes the use of a corrective factor depending on the grade of steel considered. In the case of 1.4318 (301LN) or 1.4310 (301) stainless steel, the corrective factor is 1.7.
  • a direct measurement by sigmametry (saturation magnetic induction) is also possible, although more restrictive to implement.
  • a sheet 1 of stainless steel according to the invention is treated locally so as to obtain four linear portions 3 of lower mechanical strength.
  • the sheet 1 described above is folded at the level of the portions 3 of least mechanical strength so as to obtain the profiled steel piece 2.
  • a sheet 11 of stainless steel according to the invention is treated locally so as to obtain linear portions 13 of lesser mechanical strength.
  • the sheet 11 described above is folded at four portions 13 of least mechanical strength so as to obtain the profiled steel piece 12.
  • the portions 13 of least strength unformatted have a provision guiding the deformation of the workpiece profiled steel 12 during a crash-type dynamic solicitation.
  • a sheet 21 of stainless steel according to the invention is treated locally so as to obtain a portion 23 of lower mechanical strength.
  • the sheet 21 described above is stamped at the portion 23 of least mechanical strength so as to obtain the piece of steel 22.
  • a stainless steel sheet 31 according to the invention treated locally so as to obtain portions 33 of lesser mechanical strength is profiled by means of a profiling line 34 so as to obtain a piece of profiled steel 32.
  • a steel coil 46 is unwound and undergoes a local heat treatment by means of a laser 45 so as to obtain a sheet 41 of stainless steel according to the invention having four linear portions 43 of lesser mechanical strength.
  • a stainless steel sheet 51 according to the invention undergoes a local heat treatment by means of a laser 55 so as to obtain four linear portions 53 of lesser mechanical strength.
  • a hardened stainless steel 1.4318 (301LN) is used such that its mechanical strength Rm (conventional stress maximum tensile strength) of at least 1000 MPa (state C1000 of the manufacturing range 2H according to EN 10088/2).
  • Rm conventional stress maximum tensile strength
  • the thickness of the sheet is 0.8 mm and the metal contains about 45% by volume of martensite and 55% by volume of austenite.
  • a localized heat treatment is carried out using a CO 2 type laser of 4kW.
  • the power in this case is 20%
  • the displacement of the source is 0.85m / min (1m / min also tested)
  • the focal point is located 25mm above the upper surface of the sheet.
  • the laser treatment makes it possible to obtain, along the treatment line, an annealed structure in which the percentage of martensite passes to a content of less than 10% and even 1.5% in the center, close to the annealed state of this metal, that is to say before hardening (state 2B).
  • the structure of the treated line comprises an austenitic melted zone limited in width L_zf at 2-4 times the thickness of the sheet and depth P_zf less than 50% of the thickness of the sheet as well as a heat affected zone of a width L_zat between 3 and 6 times the thickness of the sheet.
  • This area underwent an almost total reversion of martensite.
  • the set of two identified areas constitutes the portion of least mechanical strength.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Forging (AREA)
  • Bending Of Plates, Rods, And Pipes (AREA)

Claims (12)

  1. Blech aus rostfreiem Stahl, enthaltend zumindest 10,5 Gewichts-% Cr und maximal 1,2 Gewichts-% C, dessen Mikrostruktur martensitisch oder austenitisch-martensitisch ist und das aufweist zumindest 2 Volumen-% Martensit, dadurch gekennzeichnet, dass es aufweist mindestens einen lokalen Abschnitt mit geringerer mechanischer Festigkeit, der einen Martensit-Gehalt hat, der um wenigstens 10% kleiner ist als jener des Rests des besagten Blechs, wobei der lokale Abschnitt zumindest teilweise eine Dicke hat, die gleich jener des besagten Blechs ist.
  2. Blech aus Stahl gemäß Anspruch 1 mit Dicke e, dessen besagter lokaler Abschnitt eine Breite zwischen e und 25e an der Oberfläche des besagten Blechs hat.
  3. Blech aus Stahl gemäß irgendeinem der Ansprüche 1 oder 2, dessen mechanische Bruch-Festigkeit außerhalb des besagten lokalen Bereichs größer oder gleich 850MPa ist.
  4. Blech aus Stahl gemäß irgendeinem der Ansprüche 1 bis 3, dessen lokaler Abschnitt mit geringerer mechanischer Festigkeit erlangt ist:
    - entweder durch thermische lokale Behandlung eines martensitischen oder austenitischen-martensitischen rostfreien Stahlblechs mit homogener mechanischer Festigkeit,
    - oder durch differentielle Kaltverformung eines austenitischen oder austenitischen-martensitischen rostfreien Stahlblechs mit homogener mechanischer Festigkeit.
  5. Blech aus Stahl gemäß irgendeinem der Ansprüche 1 bis 4, dessen lokaler Abschnitt mit geringerer mechanischer Festigkeit einen Martensit-Gehalt hat, der wenigstens zweimal kleiner ist als jener des Rests des Blechs.
  6. Blech aus Stahl gemäß Anspruch 4, dessen besagter lokaler Abschnitt mit geringerer mechanischer Festigkeit einen Martensit-Gehalt hat, der wenigstens viermal kleiner ist als jener des Rests des Blechs.
  7. Verfahren zur Herstellung eines Blechs aus Stahl gemäß irgendeinem der Ansprüche 1 bis 6, aufweisend die Schritte, gemäß denen:
    - man ein Blech aus austenitischem, martensitischem oder austenitischem-martensitischem Stahl bereitstellt, wobei der besagte Stahl ein rostfreier Stahl ist, der zumindest 10,5 Gewichts-% Cr und maximal 1,2 Gewichts-% C enthält,
    - man gegebenenfalls das besagte Blech ganz oder teilweise kaltverformt, sodass die Mikrostruktur zumindest 2 Volumen-% Martensit aufweist,
    - man das besagte Blech behandelt, um zumindest einen lokalen Abschnitt mit geringerer mechanischer Festigkeit zu erlangen, der einen Martensit-Gehalt hat, der um wenigstens 10% kleiner ist als jener des Rests des besagten Blechs, wobei der besagte lokale Abschnitt zumindest teilweise eine Dicke hat, die gleich jener des besagten Blechs aus Stahl ist.
  8. Verfahren gemäß Anspruch 7, wobei der besagte lokale Abschnitt mit geringerer mechanischer Festigkeit erlangt ist:
    - entweder durch thermische lokale Behandlung eines martensitischen oder austenitischen-martensitischen rostfreien Stahlblechs mit homogener mechanischer Festigkeit, wobei die thermische Behandlung aus einer thermischen Anhebung via Laser, via Induktion, via Elektronenstrahl oder via Nahtschweißung resultiert,
    - oder durch differentielle Kaltverformung eines austenitischen oder austenitischen-martensitischen rostfreien Stahlblechs mit homogener mechanischer Festigkeit.
  9. Stahl-Bauteil, das erlangt werden kann durch Verformung eines Blechs aus Stahl gemäß irgendeinem der Ansprüche 1 bis 6 oder eines Blechs, das erlangt ist durch das Verfahren gemäß irgendeinem der Ansprüche 7 bis 8, wobei die besagte Verformung vorliegt in wenigstens einem der besagten lokalen Abschnitte mit geringerer mechanischer Festigkeit.
  10. Stahl-Bauteil gemäß Anspruch 9, erlangt durch Biegen, Profilierung oder Tiefziehen des wenigstens einen der lokalen Abschnitte mit geringerer mechanischer Festigkeit.
  11. Stahl-Bauteil, das erlangt werden kann durch Schneiden eines Blechs aus Stahl gemäß irgendeinem der Ansprüche 1 bis 6 oder eines Blechs, das erlangt ist durch das Verfahren gemäß irgendeinem der vorhergehenden Ansprüche 7 bis 8.
  12. Verwendung eines Bauteils gemäß irgendeinem der Ansprüche 9 bis 11 zur Herstellung von metallischen Strukturen, die widerstandfähig sind gegen dynamische Beanspruchungen.
EP09740179.8A 2009-09-21 2009-09-21 Edelstahl mit lokalen variationen der mechanischen beständigkeit Not-in-force EP2480693B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
SI200931904T SI2480693T1 (sl) 2009-09-21 2009-09-21 Nerjavno jeklo z lokalnimi spremembami mehanske odpornosti

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/FR2009/001110 WO2011033180A1 (fr) 2009-09-21 2009-09-21 Acier inoxydable à variations locales de résistance mécanique

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EP2480693A1 EP2480693A1 (de) 2012-08-01
EP2480693B1 true EP2480693B1 (de) 2018-09-12

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US (1) US20120237387A1 (de)
EP (1) EP2480693B1 (de)
JP (1) JP2013505364A (de)
KR (1) KR20120095364A (de)
CN (1) CN102741432B (de)
BR (1) BR112012006324A2 (de)
ES (1) ES2704643T3 (de)
MX (1) MX2012003385A (de)
SI (1) SI2480693T1 (de)
WO (1) WO2011033180A1 (de)

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WO2020115531A1 (fr) * 2018-12-06 2020-06-11 Aperam Acier inoxydable, produits réalisés en cet acier et leurs procédés de fabrication

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Publication number Publication date
JP2013505364A (ja) 2013-02-14
ES2704643T3 (es) 2019-03-19
SI2480693T1 (sl) 2019-04-30
BR112012006324A2 (pt) 2020-08-11
CN102741432B (zh) 2013-11-13
CN102741432A (zh) 2012-10-17
WO2011033180A1 (fr) 2011-03-24
MX2012003385A (es) 2012-07-25
US20120237387A1 (en) 2012-09-20
EP2480693A1 (de) 2012-08-01
KR20120095364A (ko) 2012-08-28

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