EP1565587B1 - Gebrauchsfertiges mechanisches teil aus stahl mit niedrigem kohlenstoffgehalt fur plastische verformung und herstellungsverfahren - Google Patents

Gebrauchsfertiges mechanisches teil aus stahl mit niedrigem kohlenstoffgehalt fur plastische verformung und herstellungsverfahren Download PDF

Info

Publication number
EP1565587B1
EP1565587B1 EP03796115A EP03796115A EP1565587B1 EP 1565587 B1 EP1565587 B1 EP 1565587B1 EP 03796115 A EP03796115 A EP 03796115A EP 03796115 A EP03796115 A EP 03796115A EP 1565587 B1 EP1565587 B1 EP 1565587B1
Authority
EP
European Patent Office
Prior art keywords
steel
hot
mechanical component
thermal treatment
rolled
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.)
Expired - Lifetime
Application number
EP03796115A
Other languages
English (en)
French (fr)
Other versions
EP1565587A1 (de
Inventor
Bernard Resiak
Mario Confente
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ArcelorMittal Gandrange SA
Original Assignee
ArcelorMittal Gandrange SA
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by ArcelorMittal Gandrange SA filed Critical ArcelorMittal Gandrange SA
Publication of EP1565587A1 publication Critical patent/EP1565587A1/de
Application granted granted Critical
Publication of EP1565587B1 publication Critical patent/EP1565587B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the invention relates to mechanical parts made of low carbon steel with high characteristics, such as the ball joints of land vehicle wheels, pivots, pins, suspension triangles, connecting rods, or other similar mechanical parts ready for use obtained by plastic deformation.
  • a long steel product (wire, bar ).
  • steels for plastic deformation must have properties of both deformability and strength. Thus, during the manufacture of mechanical parts to which some of them are intended, they must be able to withstand without significant changes in shape while sometimes sometimes having high mechanical characteristics. In fact, in some cases, the required characteristics of the parts obtained from these steels are close to those of class 10.9 according to ISO 898, namely a minimum breaking limit of 1000 MPa and a minimum yield strength of 900 MPa. In addition, these steels must have good machinability characteristics because a majority of applications require ultimate machining for final ribs.
  • the plastic deformation operations are on steel slugs from the cutting son or bars conventionally obtained by hot rolling of continuous casting products (billets or blooms).
  • cold plastic deformation Punching, forging
  • the plots are cold-formed to the press, if necessary after a globular annealing, and the parts obtained are then thermally treated by quenching and tempering.
  • the plots are heated first to a temperature of about 1000-1200 ° C, shaped hot and cooled.
  • the parts thus obtained are then thermally treated by quenching and tempering, the quenching being able to be done directly during the cooling after forging.
  • the cold stamping for example, it is already known, for example, to use steel shades of essentially bainitic structure (ie containing more than 50% of bainite), having a good compromise between deformability and final mechanical characteristics.
  • essentially bainitic structure ie containing more than 50% of bainite
  • these grades make it possible to obtain an essentially bainitic structure only on wires or rolled bars of relatively small diameter, rarely exceeding 8 mm. in fact. Beyond this, a degenerate or associated bainite with ferrite is obtained, which leads to a marked deterioration of the mechanical properties of the rolled products.
  • the structure is not well controlled, there is a risk of strong dispersion of the mechanical characteristics within the same ring or between several coiled wire rings or between several bars or within the same bar. the outcome of hot rolling.
  • bainitic structure that offers a good compromise between deformability and mechanical characteristics, at the same time as a good machinability.
  • the success of obtaining this bainitic structure is subject to the cooling constraints of the core steel, whether this cooling occurs before the plastic deformation or after. These constraints imposed on the cooling are so severe on the steel grades currently known and used that this bainitic structure may not be obtained directly in the hot rolling, or even after the forging operation, so that many mechanical parts must undergo a heat treatment after their shaping.
  • US-A-5 554233 relates to the manufacture of hot-rolled and cold-deformable bars for obtaining parts without the need for a heat treatment before or after the cold deformation.
  • the steel used comprises in particular from 0.10% to 0.14% of carbon and from 0.01% to 0.1% of molybdenum.
  • the objective of the invention is the provision of transformers with a low carbon steel grade capable of developing a bainitic or essentially bainitic structure, with low cooling stresses, for the manufacture of parts ready for use. use both cold press and hot forging.
  • the object of the invention is the development of a low carbon steel grade specific to the manufacture of mechanical parts having a bainitic or essentially bainitic structure that can be obtained already with a low cooling rate at the core, which can go down to 1 ° C / s, and offering both good deformation and good machinability for the realization of these parts by cold or hot deformation, without heat treatment after shaping, said grade having high mechanical characteristics enabling said pieces to be in grades 8.8 to 12.9 according to ISO 898.
  • the invention thus relates to a mechanical part with high characteristics low carbon steel ready for use from the plastic processing of a long rolled steel product, according to claim 1.
  • the cold-deformed steel mechanical part defined above is characterized in that the long product from which it is derived by plastic transformation is a heat-treated laminated wire or bar by cooling in the hot rolling mill. at a cooling rate sufficient to confer a bainitic or essentially bainitic structure.
  • the mechanical part made of hot-forged steel defined above is characterized in that the long product from which it is derived by plastic transformation is a bar or a rolled wire whose billet of forge which has been extracted has been thermally treated by quenching under a sufficient cooling rate to give it a bainitic structure to the core, since a quenching temperature of the order of 1200 ° C and more to which the billet has undergoes a plastic transformation by forging bringing it to its desired final shape.
  • the heat treatment involved in the preparation of the mechanical part comprises a final phase of cooling at low speed, which can go down to about 1 ° C / s, at heart.
  • this cooling of the room is a mild cooling, in any case different from a cooling operation which would soak the steel, which in any case would be, in normal practice, followed by an income.
  • the mechanical part is made of a steel whose carbon content is between 0.06% and 0.10%.
  • the mechanical part is made of steel whose molybdenum content does not exceed 0.30%, and that of manganese is less than 1.80%.
  • the invention also relates to a method of manufacturing a mechanical part with high characteristics ready to use low carbon steel having a breaking strength of more than 800 MPa, which comprises the steps of claim 6.
  • the invention in its essential characteristics, consists in the definition of an analysis of low carbon steel based on niobium, boron and molybdenum, which is specific to mechanical parts with high characteristics and able to acquire a bainitic (or essentially bainitic) homogeneous structure in the mass of the room with few requirements for cooling.
  • This structure can indeed be obtained already from a low core cooling rate that can go down to about 1 ° C / s, a speed that can be achieved, as we know, directly in the hot rolling mill. even for wires and bars of diameter of the order of 20 mm and more depending on the installations.
  • the invention opens to the large diameters the production range of hot-rolled long products for cold-forging or cold-forging workshops, and, for those reserved for hot forging, it provides the economy of a additional final tempering-tempering heat treatment.
  • the limiting diameters are around 20 to 25 mm for the shades according to the invention.
  • bainitic structure will refer to a “bainitic or essentially bainitic structure”.
  • the carbon at these contents serves to obtain a bainitic structure having the required mechanical properties. It makes it possible to obtain good work hardening ability during cold plastic deformation. Its low content also makes it possible to avoid the formation of large carbides unfavorable to ductility without the need for a globulization treatment.
  • Niobium works synergistically with molybdenum and boron to expand the bainitic transformation domain. It increases boron hardenability by increasing the effective boron content in steel. Indeed, the formation of carbides Fe 23 (CB 6 ) (trapping boron and passive as to the hardenability of steel) is made more difficult by the action of niobium which stabilizes the austenite and delays the diffusion of carbon. Moreover, it makes it possible to increase the recrystallization temperature of the austenite which allows to obtain a finer bainitic structure during controlled rolling, and thus to increase the resilience of the parts.
  • Molybdenum is a carburigenic element that broadens the bainitic domain by retarding the germination of ferrite.
  • Molybdenum acts in synergy with boron and with niobium, whose role it reinforces.
  • manganese From 1.30 to 2.00%, and preferably between 1.60 and 1.80%, of manganese. This manganese then makes it possible to obtain sufficient quenchability, assists in the formation of bainite and makes it possible to obtain the desired mechanical characteristics.
  • Titanium is used to fix nitrogen and thus protect boron. Without titanium, boron will lose its quenching power by reacting with nitrogen. Titanium also provides a fine austenitic grain which improves cold forming and ductility.
  • sulfur combines with manganese to form plastic and ductile manganese sulphides. It allows to obtain a good machinability. It is possible, if one wishes to further improve the machinability, to increase its content up to a maximum value of 0.1% but not beyond it if one wants to ensure good deformability Cold.
  • This steel also presents the inevitable impurities and residual elements resulting from its production, in particular the phosphorus whose content must remain less than 0.02% to guarantee good ductility during and after the setting in cold form, as well as copper and nickel, the content of which must be less than 0.30%.
  • This optimized composition allows the steel to have a very good plastic deformation ability at the same time as a good machinability. Indeed, this shade not only promotes obtaining bainite, but also reduces the risk of obtaining martensite, the presence of which can be a serious obstacle to a good machining operation.
  • An essential aspect of the invention is that the mechanical parts have a homogeneous bainitic structure in the mass at low core cooling rate of hot forged parts, or wires or bars from which they are cold-stamped, which can descend up to about 1 ° C / s.
  • the mechanical part is cold-forged (or cold-forged)
  • the bainitic structure is obtained before shaping.
  • the steel after deformation, then has a good ductility, measured by a necking much greater than 50%, a tensile strength greater than 650 MPa, and a mechanical strength greater than 800 MPa.
  • the part is indeed obtained by cold plastic deformation of the steel already having a bainitic structure.
  • a long half-product consisting of an analysis steel according to the invention is supplied which is hot-rolled, if necessary after reheating above 1100 ° C., in accordance with the usual hot-rolling practice. obtaining a rolled wire of 10 mm in diameter for example.
  • the wire removal temperature is less than 1000 ° C.
  • the laminated wire obtained is then cooled in air in the hot rolling itself in the usual manner ("Stelmor" process for example), at a low core speed which can go down to about 1 ° C./s. to obtain a homogeneous bainitic structure.
  • the laminated wire is then delivered (or deliverable) to the transformer as a crown.
  • the transformer receiving the crown unwinds the wire, raises it if necessary, before cutting it into pieces of the desired length.
  • Each piece is then subjected to a usual operation of cold plastic deformation to obtain the ready-to-use final part (ball joints, shafts, connecting rods, screws, etc.), after a nominal setting machining if necessary. .
  • the final mechanical characteristics will naturally be obtained by the work hardening resulting from the shaping.
  • the part is deformed under heat and the bainitic structure is obtained after this plastic deformation operation: a long half-product consisting of an analysis steel according to the invention is supplied. while hot until a rolled bar of 30 mm diameter for example. After cooling if necessary, the cut-to-length bar is available straight to the blacksmith with its ordinary metallographic structure naturally acquired during hot rolling.
  • the blacksmith who receives it delivers it in pieces and each piece is then brought to a temperature of about 1200 ° C before being subjected to a hot plastic deformation operation at the forge.
  • the parts are then cooled in the usual manner, in two stages, with a first controlled cooling to a temperature below 1000 ° C and a second cooling at low core cooling rate which can go down to 1 ° C / s about.
  • the end-of-rolling conditions do not have any particular importance on the obtaining of the metallurgical structure, since the bainite, which gives the part the essential of its properties of use, is reached. all in the end, after hot shaping and controlled cooling.
  • the mechanical parts according to the invention are obtained by plastic deformation of rolled products without additional tempering and tempering heat treatment.
  • the billet from the casting was hot rolled after reheating above 1100 ° C to form a 12 mm diameter wire.
  • the temperature of removal of the wire after rolling was 820 ° C.
  • the cooling rate of the wire in the hot end of rolling was of the order of 5 ° C / s.
  • a homogeneous bainitic structure is obtained on the whole of the wire, at the periphery as well as at the core.
  • the mechanical characteristics of the wire are as follows: Rm (MPa) Rp 0.2 (MPa) AT (%) Z (%) 857 683 17.4 71.4
  • the mechanical parts with high characteristics according to the invention are remarkable in that they make it possible in particular to save quenching and tempering treatments currently used in cold-forging or forging operations.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Forging (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)
  • Carbon And Carbon Compounds (AREA)

Claims (6)

  1. Gebrauchsfertiges mechanisches Stück aus Niedrig-Kohlenstoff-Stahl mit hohen Eigenschaften erhalten durch die plastische Transformation eines gewalzten langen Stahlerzeugnisses aufweisend die folgenden Eigenschaften:
    - die chemische Zusammensetzung des Stahls entspricht der folgenden Analyse, gegeben in Gewichts-Prozent basierend auf dem Eisen:
    0,02% ≤ C ≤ 0,10%
    0,04% ≤ Nb ≤ 0,10%
    0,001% ≤ B ≤ 0,005%
    0,10% ≤ Mo ≤ 0,35%
    1,3% ≤ Mn ≤ 2,0%
    0,10% ≤ Si ≤ 1,30%
    0,01% ≤ Al ≤ 0,08%
    N ≤ 0,015% mit Ti ≥ 3,5 x % N;
    eventuell von 0,001 bis 0,1% Schwefel,
    Rest das Eisen und die unvermeidbaren Rest-Unreinheiten, die aus der Stahl-Bearbeitung resultieren, darunter weniger als 0,02% P und weniger als 0,30% Cu und Ni,
    - wobei das lange Erzeugnis aus einem Halbprodukt erhalten wird, das entstanden ist durch stetiges Gießen und HeißWalzen im austenitischen Bereich, anschließend thermisch behandelt wird zum Erhalten einer bainitischen oder im Wesentlichen bainitischen Struktur und in Form gebracht wird, entweder mittels kalter plastischer Umformung nach der thermischen Behandlung oder mittels heißer plastischer Umformung während der thermischen Behandlung, um ihm seine endgültige Form zu geben mit einer Reißfestigkeit von über 800 Mpa, ohne thermische Behandlung nach diesem In-Form-Bringen.
  2. Mechanisches Stück aus Niedrig-Kohlenstoff-Stahl, kaltgeformt gemäß Anspruch 1, dadurch charakterisiert, dass das lange Erzeugnis, aus dem es durch plastische Umformung entstanden ist, ein gewalzter Draht oder einer gewalzter Stab ist, der thermisch behandelt ist mittels Abkühlen von der Walzhitze mit einer Abkühlgeschwindigkeit, die ausreicht, um ihm eine bainitische oder im Wesentlichen bainitische Struktur zu verleihen.
  3. Mechanisches Stück aus Niedrig-Kohlenstoff-Stahl, geschmiedet gemäß Anspruch 1, dadurch charakterisiert, dass das lange Erzeugnis, aus dem es durch plastische Umformung entstanden ist, ein gewalzter Draht oder einer gewalzter Stab ist, dessen Schmiederohling, der daraus extrahiert wurde, thermisch behandelt wurde durch Abschrecken mit einer Abkühlrate die ausreicht, um ihm bis zum Kern eine bainitische oder im Wesentlichen bainitische Struktur zu verleihen, ausgehend von einer Abschrecktemperatur von etwa 1200°C und mehr, bei der der Rohling einer plastischen Umformung durch Schmieden ausgesetzt wurde, die ihn in die gewünschte endgültige Form bringt.
  4. Mechanisches Stück aus Niedrig-Kohlenstoff-Stahl gemäß Anspruch 2 oder 3, dadurch charakterisiert, dass die thermische Behandlung, die sich während seiner Herstellung ereignet, eine letzte Abkühlphase mit geringer Geschwindigkeit, die auf bis zu 1°C/s im Kern heruntergehen kann, aufweist.
  5. Mechanisches Stück aus Niedrig-Kohlenstoff-Stahl gemäß einem der Ansprüche 1 bis 4, dadurch charakterisiert, dass der Stahl, aus dem es zusammengesetzt ist, einen Gehalt von Molybdän hat, der 0,30% nicht überschreitet, und einen Gehalt von Mangan unter 1,80% hat.
  6. Verfahren zum Herstellen eines gebrauchsfertigen mechanischen Stücks aus Niedrig-Kohlenstoff-Stahl mit hohen Eigenschaften, das eine Reißfestigkeit von über 800 Mpa aufweist, dadurch charakterisiert, dass es die folgenden Schritte aufweist:
    - ausgehend von einem langen Halbprodukt dessen Zusammensetzung der folgenden Analyse entspricht, gegeben in Gewichts-Prozent basierend auf dem Eisen:
    0,02% ≤ C ≤ 0, 10%
    0,04% ≤ Nb ≤ 0,10%
    0,001% ≤ B ≤ 0,005%
    0,10% ≤ Mo ≤ 0,35%
    1,3% ≤ Mn ≤ 2,0%
    0,10% ≤ Si ≤ 1,30%
    0,01% ≤ Al ≤ 0,08 %
    N ≤ 0,015% mit Ti ≥ 3,5 x % N;
    eventuell von 0,001 bis 0,1% Schwefel,
    wobei der Rest das Eisen und die unvermeidbaren Rest-Unreinheiten, die aus der Stahl-Bearbeitung resultieren, darunter weniger als 0,02% P und weniger als 0,30% Cu und Ni, ist,
    man heiß-walzt ein langes Erzeugnis (Draht oder Stab), wobei die Ablagetemperatur des langen Erzeugnisses am Ende des Walzens unter 1000°C ist;
    - man behandelt danach das erhaltene lange gewalzte Produkt thermisch, wobei das thermische Behandeln eine letzte Abkühlphase mit geringer Geschwindigkeit, die auf bis zu 1°C/s etwa im Kern heruntergehen kann, aufweist, zum Erhalten einer bainitischen oder im Wesentlichen bainitischen Struktur und man verformt das lange Erzeugnis plastisch, um es in seine endgültige gewünschte Form zu bringen, wobei die plastische Verformung erreicht wird entweder mittels kalter plastischer Umformung nach der thermischen Behandlung oder mittels heißer plastischer Umformung während der thermischen Behandlung, um ihm seine endgültige Form zu geben mit einer Reißfestigkeit von über 800 Mpa, ohne thermische Behandlung nach diesem In-Form-Bringen.
EP03796115A 2002-11-27 2003-11-27 Gebrauchsfertiges mechanisches teil aus stahl mit niedrigem kohlenstoffgehalt fur plastische verformung und herstellungsverfahren Expired - Lifetime EP1565587B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0214838 2002-11-27
FR0214838A FR2847592B1 (fr) 2002-11-27 2002-11-27 Acier pour deformation a froid ou a chaud, piece mecanique prete a l'emploi realisable avec cet acier et son procede de fabrication
PCT/FR2003/003516 WO2004050935A1 (fr) 2002-11-27 2003-11-27 Piece mecanique prete a l'emploi en acier bas carbone pour deformation plastique et son procede de fabrication

Publications (2)

Publication Number Publication Date
EP1565587A1 EP1565587A1 (de) 2005-08-24
EP1565587B1 true EP1565587B1 (de) 2010-01-27

Family

ID=32241638

Family Applications (1)

Application Number Title Priority Date Filing Date
EP03796115A Expired - Lifetime EP1565587B1 (de) 2002-11-27 2003-11-27 Gebrauchsfertiges mechanisches teil aus stahl mit niedrigem kohlenstoffgehalt fur plastische verformung und herstellungsverfahren

Country Status (9)

Country Link
US (1) US20070051434A1 (de)
EP (1) EP1565587B1 (de)
JP (1) JP5036967B2 (de)
AT (1) ATE456685T1 (de)
AU (1) AU2003298375A1 (de)
DE (1) DE60331163D1 (de)
ES (1) ES2338227T3 (de)
FR (1) FR2847592B1 (de)
WO (1) WO2004050935A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010112611A1 (de) * 2009-04-03 2010-10-07 Swiss Steel Ag Bainitische stähle für pkw und leichte nkw kugelzapfen

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20080090574A (ko) 2004-07-21 2008-10-08 신닛뽄세이테쯔 카부시키카이샤 용접 열영향부의 저온 인성이 우수한 용접 구조용 강 및 그제조 방법
FR2931166B1 (fr) * 2008-05-15 2010-12-31 Arcelormittal Gandrange Acier pour forge a chaud a hautes caracteristiques mecaniques des pieces produites
EP2199422A1 (de) * 2008-12-15 2010-06-23 Swiss Steel AG Kohlenstoffarmer, ausscheidungsgehärteter Stahl für Kaltstauchanwendungen
DE102019106937A1 (de) * 2019-03-19 2020-09-24 Benteler Automobiltechnik Gmbh Mehrschenkliger Lenker für eine Radaufhängung in einem Fahrzeug

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3592633A (en) * 1968-01-22 1971-07-13 Nippon Kokan Kk High strength low alloy steel possessing sufficient weldability containing small amounts of nb,ti,and b
JPS5877528A (ja) * 1981-10-31 1983-05-10 Nippon Steel Corp 低温靭性の優れた高張力鋼の製造法
GB8603500D0 (en) * 1986-02-13 1986-03-19 Hunting Oilfield Services Ltd Steel alloys
CA2135255C (en) * 1994-05-26 2000-05-16 William E. Heitmann Cold deformable, high strength, hot rolled bar and method for producing same
AU680590B2 (en) * 1995-01-26 1997-07-31 Nippon Steel Corporation Weldable high-tensile steel excellent in low-temperature toughness
DE69821954T2 (de) * 1997-07-28 2004-12-09 Exxonmobil Upstream Research Co., Houston Ultra-hochfeste, schweissbare, borenthaltende stähle mit ausgezeichneter zähigkeit
US6315946B1 (en) * 1999-10-21 2001-11-13 The United States Of America As Represented By The Secretary Of The Navy Ultra low carbon bainitic weathering steel

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010112611A1 (de) * 2009-04-03 2010-10-07 Swiss Steel Ag Bainitische stähle für pkw und leichte nkw kugelzapfen

Also Published As

Publication number Publication date
EP1565587A1 (de) 2005-08-24
US20070051434A1 (en) 2007-03-08
FR2847592B1 (fr) 2007-05-25
ES2338227T3 (es) 2010-05-05
WO2004050935A1 (fr) 2004-06-17
ATE456685T1 (de) 2010-02-15
JP2006508248A (ja) 2006-03-09
FR2847592A1 (fr) 2004-05-28
DE60331163D1 (de) 2010-03-18
JP5036967B2 (ja) 2012-09-26
AU2003298375A1 (en) 2004-06-23

Similar Documents

Publication Publication Date Title
EP0851038B2 (de) Stahl und Verfahren zur Formung eines Stahlwerkstückes durch kalte plastische Verarbeitung
JP5458048B2 (ja) 肌焼鋼およびその製造方法、並びに肌焼鋼を用いた機械構造部品
EP1728883A1 (de) Hochfester bolzen mit hervorragender beständigkeit gegenüber verzögertem bruch und relaxationsbeständigkeit
EP0717116B1 (de) Verfahren zum Herstellen eines Werkstückes aus Maschinenbaustahl und nach diesem Verfahren hergestelltes Werkstück
EP0209437B1 (de) Leicht legierter, geschmiedeter Stahlzylinder zum Kaltwalzen
US9896750B2 (en) Steel wire rod having high strength and ductility and method for producing same
EP0093218B1 (de) Schrauben und Bolzen aus Stahl mit hoher Festigkeit und Verfahren zur Herstellung
CA2147979C (en) Cold formed high-strength steel parts
JPH10251804A (ja) 高強度ばね用鋼
EP1565587B1 (de) Gebrauchsfertiges mechanisches teil aus stahl mit niedrigem kohlenstoffgehalt fur plastische verformung und herstellungsverfahren
FR2543461A1 (fr) Procede pour fabriquer des tubes d'acier sans soudure
EP2134882B1 (de) Mikrolegierter stahl mit guter beständigkeit gegenüber wasserstoff zur kaltumformung von maschinenteilen mit hohen eigenschaften
JP5523288B2 (ja) 高強度中空ばね用シームレス鋼管
CN104204258A (zh) 高强度弹簧用中空无缝管
EP0550294B1 (de) Rohfabrikate grosser Länge für Herstellungsverfahren durch Kaltumformen, insbesondere für Kaltstauchen von formgebend bearbeitete Erzeugnisse wie Bolzen, und Verfahren zur Herstellung dieser kaltgeformten Gegenstände
EP0845544A1 (de) Stahlprodukt aus bainitischem Stahl sowie Verfahren zur Herstellung des Stahlproduktes
WO2005100618A2 (fr) Piece mecanique de taille moyenne ou petite issue de la forge ou de la frappe
EP0092629B1 (de) Verfahren zur Herstellung von Stäben und Röhren aus Stählen mit hohen mechanischen Eigenschaften
JP4976985B2 (ja) 低温ねじれ特性に優れた線材・棒鋼の製造方法
JPH0673502A (ja) 伸線加工性に優れた高炭素鋼線材または鋼線およびその製造方法
WO1985004906A1 (fr) Procede de fabrication de barres ou de fil machine en acier et produits correspondants
KR20230159706A (ko) 기계 구조 부품용 강선 및 그 제조 방법
CH404203A (fr) Alliage à base de fer, nickel, chrome, aluminium, et procédé de fabrication de cet alliage

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20050423

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL LT LV MK

DAX Request for extension of the european patent (deleted)
17Q First examination report despatched

Effective date: 20070724

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: ARCERLORMITTAL GANDRANGE

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 60331163

Country of ref document: DE

Date of ref document: 20100318

Kind code of ref document: P

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2338227

Country of ref document: ES

Kind code of ref document: T3

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20100127

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100527

REG Reference to a national code

Ref country code: IE

Ref legal event code: FD4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100428

Ref country code: IE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100427

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20101028

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100127

BERE Be: lapsed

Owner name: ARCELORMITTAL GANDRANGE

Effective date: 20101130

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101130

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101130

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101130

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100728

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 13

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 14

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 15

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20221021

Year of fee payment: 20

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: TR

Payment date: 20221101

Year of fee payment: 20

Ref country code: MC

Payment date: 20221025

Year of fee payment: 20

Ref country code: LU

Payment date: 20221020

Year of fee payment: 20

Ref country code: IT

Payment date: 20221020

Year of fee payment: 20

Ref country code: GB

Payment date: 20221021

Year of fee payment: 20

Ref country code: ES

Payment date: 20221201

Year of fee payment: 20

Ref country code: DE

Payment date: 20220616

Year of fee payment: 20

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 60331163

Country of ref document: DE

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20231204

REG Reference to a national code

Ref country code: GB

Ref legal event code: PE20

Expiry date: 20231126

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20231126

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20231128

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20231126

Ref country code: ES

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20231128