EP2009120B1 - Utilisation d'un alliage d'acier très solide destiné à la fabrication de tuyaux en acier très résistants et ayant une bonne déformabilité - Google Patents

Utilisation d'un alliage d'acier très solide destiné à la fabrication de tuyaux en acier très résistants et ayant une bonne déformabilité Download PDF

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Publication number
EP2009120B1
EP2009120B1 EP08011681.7A EP08011681A EP2009120B1 EP 2009120 B1 EP2009120 B1 EP 2009120B1 EP 08011681 A EP08011681 A EP 08011681A EP 2009120 B1 EP2009120 B1 EP 2009120B1
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EP
European Patent Office
Prior art keywords
strength
steel
less
alloy
mpa
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.)
Not-in-force
Application number
EP08011681.7A
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German (de)
English (en)
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EP2009120A2 (fr
EP2009120A3 (fr
Inventor
Uwe Dr.-Ing. Diekmann
Andreas Dr.-Ing. Frehn
Alexander Dr.-Ing. Redenius
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Benteler Deustchland GmbH
Benteler Automobiltechnik GmbH
Original Assignee
Benteler Deustchland GmbH
Benteler Automobiltechnik GmbH
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Publication of EP2009120A2 publication Critical patent/EP2009120A2/fr
Publication of EP2009120A3 publication Critical patent/EP2009120A3/fr
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the invention relates to the use of a steel alloy according to the features of patent claim 1.
  • micro-alloyed fine grain steels with ferritic-pearlitic structure for example steel StE 460.
  • this steel achieves breaking strengths of 650 - 750 MPa and elongation at break of approximately 20 - 25%.
  • the product of strength and elongation at break is usually about 16,000 - 18,000 [MPa *%].
  • This combination of properties allows a good cold workability, eg by pulling, pressing, thread rolling.
  • Classic become the properties of the StE 460 achieved by variations of 20MnV6 steel alloy.
  • the solid solution hardening by the alloying element manganese together with the precipitation of vanadium carbonitrides causes a comparatively high strength at a moderate cost.
  • the strength is adjusted by varying the carbon content generally in the range between 0.12 and 0.22%.
  • vanadium, titanium and niobium also play an important role as micro-alloying elements.
  • the micro-alloying elements are generally alloyed in small proportions of up to 0.2%, the amount and choice of the micro-alloying elements being dependent on thermoforming, eg hot-rolled strip production.
  • the structure of a classic StE 460 consists of a mixture of ferrite and pearlite and is generally formed by cooling in air after rolling or austenitizing.
  • An advantage of these steels is the property, by a so-called normalization, generally carried out in the form of austenitization and cooling in air, restore the initial structure and the initial properties even after a complex manufacturing history.
  • a further increase in the strength through additional alloying elements leads to increased costs and to a pronounced decrease in the elongation at break, so that the desired cold workability is not guaranteed.
  • additional heat treatment such as soft annealing before forming, this problem can be easily overcome.
  • this procedure is also associated with increased costs.
  • the described ferritic-pearlitic structure of the state of the art steel tubes has in addition to the only moderate ratio of strength and ductility additional disadvantages.
  • the microstructures ferrite-perlite are not evenly distributed but show a pronounced lineiness, which as a first consequence brings about a pronounced anisotropy of the properties and leads to undesirable effects during cold forming. For example, there are significant differences along and across the rolling direction.
  • Welded steel pipes are often produced by pressure welding.
  • the strip edges are heated by resistance heating (high-frequency or direct current) and then welded at high pressure with significant plastic deformation, without a molten phase is formed.
  • Such welding methods are therefore covered by the term solid state welding methods.
  • a great advantage of the welding process described is the extremely high welding speed, which is significantly higher than other methods, e.g. above that of the laser beam welding, and thus brings a superior cost-effectiveness.
  • pressure welding of ferritic-pearlitic steels however, the formation of the weld bead as a result of the necessary plastic deformation results in the effect that pearlite rows are deflected and reach the surface in the region of the weld zone.
  • brittle cementite lamellae of the pearlitic structure constituent form metallurgical notches, which in the worst case emerge perpendicular to the surface.
  • These fins can already be used during the following processing, e.g. Calibration of pipes for roundness, lead to cracks.
  • these notches mean that even with high static strength no high dynamic strength can be achieved. Consequently, pearlite-free structures are particularly suitable for producing high-strength press-welded steel tubes.
  • TRIP steels usually contain over 0.2% carbon, with the silicon content often exceeding 1.5%.
  • the microstructure of these steels has a ferritic-bainitic base matrix containing retained austenite constituents, which are converted to hard martensite during transformation of the steel.
  • the retained austenite is stabilized by alloying elements and a special heat treatment.
  • the advantage of the TRIP steel lies in the good forming properties at high strengths and high breaking strengths.
  • a TRIP steel has a high solidification capacity even with large changes in shape and a high energy absorption capacity, which is maintained even under dynamic load.
  • TRIP steels generally require a complex and technically difficult heat treatment to stabilize the desired amount of retained austenite to room temperature.
  • the TRIP heat treatment generally consists of accelerated cooling from the austenite region to prevent perlite formation and holding for a few minutes at temperatures just above the martensite start temperature. This heat treatment requires a complex process control and is difficult to implement reliably in conventional production facilities of plants for pipe production.
  • ferritic-bainitic steels (FB steels) which have strengths of 500-1,000 MPa and exhibit better properties in relation to the forming behavior than ferritic-pearlitic steels of the same strength.
  • FB steels ferritic-bainitic steels
  • the achievable plastic deformations at strengths above 700 MPa are still too low.
  • the production of ferritic-bainitic steels generally requires a so-called thermomechanical treatment, ie special rolling and cooling conditions. For this reason, conventional ferritic-bainitic steels are mainly available as hot-rolled strip.
  • TRIP steels and FB steels can not yet be normalized analogously to ferritic-pearlitic steels, since during normalization the necessary cooling conditions are not guaranteed.
  • the first three steels shown have a significantly higher carbon content and also differ in the other elements from the composition of the below presented and inventive alloys 1 to 4.
  • the presented TRIP steel (number 3) achieves comparable mechanical properties, for processing
  • Material characteristics of Docol 1000 DP, TRIP steel RA-K 42/80 and FB-W 600 are only available in strip material. Therefore, the table also indicates the A80 instead of the A5 elongation for the DP / TRIP and FB steel.
  • the A80 elongation is used for strip material due to sample geometry, as opposed to strip tensile.
  • a steel alloy for high strength cold rolled sheets.
  • the thin cold-rolled steel sheet is heated to a temperature between the Ac1 transformation point and the austenitizing temperature + 50 ° C, then cooled at a cooling rate between 5 and 150 ° C / s to a temperature range of at least 600 to 500 ° C. Subsequently, the temperature is maintained in a range of 350 to 500 ° C.
  • Such a steel sheet has good ductility properties and exhibits good values in terms of breaking strength and elongation at break, so that it has good crash properties when used in the automotive field.
  • the steel tube consists of an alloy of 0.02% carbon, 0.3% to 2.5% silicon, 0.10% to 3.0% manganese, 0.005% sulfur maximum, 0.15% phosphorus maximum, 0.005% bis 0.100% aluminum, at most 0.0050% nitrogen and at least one element from the following group with the following proportions: 0.001% to 0.200% titanium, 0.001% to 0.200% niobium, 0.001% to 0.200% vanadium and 0.0005% to 0.0030% boron, balance iron and unavoidable impurities.
  • the structure has a complex structure containing 5 to 20% retained austenite, with the remainder of the structure consisting of a structure of the following group: bainite, ferrite and perlite.
  • the steel tube is heated above the Ac1 transformation point to the Ac3 transformation point. The temperature is kept for 30 minutes or less. Subsequently, it is cooled at a cooling rate of at least 0.5 ° C / sec to a temperature between the MS transformation point + 100 ° C to the MS transformation point. Then, the temperature is maintained for 30 to 300 seconds. This is followed by air cooling to room temperature.
  • the invention is based on the object of demonstrating how steel pipes with high strength and good formability can be produced without costly heat treatment and without costly alloying concepts, wherein the elongation at break should at least equal the steel StE 460 and wherein the steel pipes have a breaking strength above 700 MPa should.
  • the solution of the problem of the invention is achieved by a new structure concept and its alloy implementation.
  • the new alloy concept is based on the avoidance of perlite and on the setting of a ferritic-bainitic structure with small amounts of lamellar retained austenite. As a result, favorable, low yield strength ratios are achieved for cold forming.
  • the product of breaking strength and elongation at break reaches very good values of more than 20,000 [MPa *%].
  • This microstructure is achieved by adapting the chemical composition to predefined cooling conditions of the steel tubes from the austenite region. The cooling conditions are described by a continuous cooling with cooling rates between 0.5 K / sec and 5 K / sec.
  • the alloy concept prevents the formation of perlite in this cooling zone.
  • ferrite or bainitic ferrite and one or more residual phases are formed Residual phases which, depending on the cooling conditions, consist of lower bainite and martensite with lamellar retained austenite.
  • Residual phases which, depending on the cooling conditions, consist of lower bainite and martensite with lamellar retained austenite.
  • the steel is characterized by excellent formability in the cold state, as well as by a high breaking strength at high elongation at break, which is caused by the strong solidification due to the multi-phase character.
  • the pipes are intended to be cold formed in further processing.
  • the alloys show a basic ferritic structure with bainite, martensite and partially retained austenite, the grain sizes being 10-20 ⁇ m for the rolling conditions not optimized here. Occasionally it comes to the formation of fine and small pearlite nests, which are not arranged in a row. By improving the hot rolling conditions, the microstructures can be significantly improved and thus also the properties of the materials.
  • Alloy 3 after improved hot rolling conditions, i. from the standard production of seamless tubes measuring 36 x 3.6 mm with a final rolling temperature of 860 ° C. Alloy 3 was chosen as an example because it has a high strength.
  • the material characteristics of the alloy after hot rolling of seamless tubes Rp0.2 [MPa] Rm [MPa] A5 [%] Fracture Z [%] True Breaking Voltage [MPa] Alloy 3 545 960 24 55 1610
  • alloy 3 By lowering the final rolling temperatures, the grain size of alloy 3 was significantly reduced to about 5 ⁇ m and the microstructure was developed to be more homogeneous. The properties could be significantly improved. Noteworthy is the increase in yield strength and tensile strength with practically constant elongation at break and high uniform elongation. It is also noteworthy that a true fracture stress of 1200 - 1.600 MPa is achieved, which can be considered as untypical for steels with less than 0.1% carbon content. Alloy 3 achieves the strength and ductility of TRIP steels with significantly reduced C content and significantly simplified temperature-time guidance.
  • Tubes made of such a steel have a pearlite-free multi-phase structure and open up a variety of applications and uses, some of which are exemplified below.
  • hot-rolled steel alloy pipes Due to the excellent relationship between strength and ductility, hot-rolled steel alloy pipes have particular advantages in subsequent, predominantly cold, deformation processes, eg drawing, swaging, flow-forming, thread rolling, extrusion, compression, autofretting, bending.
  • the steel alloy can be used to produce ultra-high-strength and cost-effective cold-drawn steel tubes, eg, drill pipes, line pipes, diesel injection lines, cylinder tubes, airbag generator tubes, and side impact carbody tubes.
  • work hardening is used to achieve high strength.
  • Soft annealing before cold drawing is not required. Starting after cold drawing is optional depending on the desired Strength possible. Stresses in the range of well over 1,000 MPa up to 1,600 MPa are possible.
  • the alloy is distinguished by the fact that no pearlite line appears, so that the tubes react less sensitively to internal defects caused by pleats.
  • the tubes produced from the steel alloy are also particularly suitable for further processing by hydroforming.
  • the excellent deformation behavior of the steel alloy results in hydroforming advantages, since high component strengths can be achieved using the steel alloy.
  • the production of welded pipes from the alloy is also advantageously possible.
  • the alloy concept allows the production of hot strip and cold strip. Compared to conventional DP steels and TRIP steels, a comparatively simple temperature-time control is required.
  • the alloy can be normalized up to a plate thickness of 4 mm, ie Develops the target structure in case of air cooling.
  • the low carbon content results in only comparatively low hardness peaks in the welded seam of welded pipes. This is especially true in comparison to TRIP steels, which show a high degree of hardening with twice the carbon content. Due to the lack of pearlite brittleness, advantages arise in classical and very economical pressure welding.
  • the alloy concept also advantageously allows beam welding by means of laser beam or electron beam.
  • the advantage of Alloy concept is also here in the low carbon content and in the normalization capability of the pipes.
  • the steel alloy is suitable for the production of tubes for chassis applications in the automotive industry. Due to the good breaking strength-Umform zucchinis ratio more complex components are conceivable, which could not be produced with the previous steel grades or only with great technical and therefore benefited insomniaßem effort. In addition, the low carbon content in combination with the other alloying elements ensures good weldability.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials 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)

Claims (2)

  1. Utilisation d'un alliage d'acier qui consiste, en parties en masse, en carbone (C) 0,06 - 0,10 silicium (Si) 1,2-1,8 manganèse (Mn) 1,4-2,2 chrome (Cr) 0,1 0,4 molybdène (Mo) 0,15 ou moins aluminium (Al) 0,05 ou moins vanadium (V) 0,15 ou moins azote (N) 0,02 ou moins niobium (Nb) 0,02 -0,06 cuivre (Cu) 0,2 ou moins nickel (Ni) 0,2 ou moins bore (B) 0,001 - 0,004 titane (Ti) 0,001 - 0,05 tungstène (W) 0,15 ou moins
    et en fer ainsi que des impuretés dues à la fusion comme reste, où à la somme de silicium (Si) + manganèse (Mn) + chrome (Cr) cuivre (Cu) est située dans une plage de 3 à 3,8 % et où l'alliage d'acier présente une structure multiphasique fine sensiblement sans perlite consistant en ferrite avec inclusion de bainite ainsi que martensite avec de l'austénite résiduelle, où il n'y a pas de répartition linéaire de perlite, où le produit de à la résistance à la rupture et de l'allongement à à la rupture dépasse 20000 [MPa*%], où à la résistance Rm à l'état non déformé est supérieure à 600 MPa pour la production de tubes d'acier sondés par soudage à l'état fondu et soudage à l'état solide, où les tubes d'acier possèdent une grande résistance et une bonne aptitude à la mise en forme.
  2. Utilisation d'un alliage d'acier selon à la revendication 1 pour à la production de tubes d'acier étirés à froid de grande résistance.
EP08011681.7A 2007-06-27 2008-06-27 Utilisation d'un alliage d'acier très solide destiné à la fabrication de tuyaux en acier très résistants et ayant une bonne déformabilité Not-in-force EP2009120B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE200710030207 DE102007030207A1 (de) 2007-06-27 2007-06-27 Verwendung einer hochfesten Stahllegierung zur Herstellung von Strahlrohren mit hoher Festigkeit und guter Umformbarkeit

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EP2009120A2 EP2009120A2 (fr) 2008-12-31
EP2009120A3 EP2009120A3 (fr) 2009-08-19
EP2009120B1 true EP2009120B1 (fr) 2013-05-01

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Publication number Priority date Publication date Assignee Title
EP2828540A1 (fr) * 2012-03-20 2015-01-28 Aktiebolaget SKF (publ) Procédé de fabrication d'un palier de roulement et palier de roulement
DE102013101276A1 (de) * 2013-02-08 2014-08-14 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines Kraftfahrzeugstabilisators
DE102014224469B4 (de) * 2014-11-28 2019-06-27 Bayern-Chemie Gesellschaft Für Flugchemische Antriebe Mbh Verfahren zum Herstellen einer, wenigstens einen metallenen Werkstoff aufweisenden Raumform, sowie Raumform
JP2018538440A (ja) * 2015-11-16 2018-12-27 ベントラー スティール ／ チューブ ゲーエムベーハー 高エネルギー吸収能力を備えた合金鋼及び鋼管製品
DE102015119839A1 (de) * 2015-11-17 2017-05-18 Benteler Steel/Tube Gmbh Stahllegierung mit hohem Energieaufnahmevermögen und Stahlrohrprodukt
DE102018133143A1 (de) * 2018-11-06 2020-05-07 Salzgitter Flachstahl Gmbh Innenhochdruck umgeformtes Bauteil aus Stahl und Verwendung eines Stahls für Vorprodukte zur Herstellung eines innenhochdruckumgeformten Bauteiles sowie Vorprodukt hierfür
DE102020102772A1 (de) 2020-02-04 2021-08-05 Benteler Steel/Tube Gmbh Gasgeneratorrohr und Gasgenerator für Airbagmodul
DE102022124366A1 (de) 2022-09-22 2024-03-28 Thyssenkrupp Steel Europe Ag Verfahren zur Herstellung eines warmgewalzten Stahlflachprodukts zum Einsatz in der Rohrfertigung

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JP3533844B2 (ja) * 1996-09-19 2004-05-31 Ｊｆｅスチール株式会社 液圧バルジ成形性に優れた電縫鋼管およびその製造方法
WO1998049362A1 (fr) * 1997-04-30 1998-11-05 Kawasaki Steel Corporation Acier presentant une ductilite et une resistance elevees et procede de production de ce materiau
JPH11279693A (ja) * 1998-03-27 1999-10-12 Nippon Steel Corp 焼付硬化性に優れた良加工性高強度熱延鋼板とその製造方法
JP4524850B2 (ja) * 2000-04-27 2010-08-18 Ｊｆｅスチール株式会社 延性および歪時効硬化特性に優れた高張力冷延鋼板および高張力冷延鋼板の製造方法
WO2002024968A1 (fr) * 2000-09-21 2002-03-28 Nippon Steel Corporation Tole d'acier presentant de bonnes caracteristiques de gel de forme et procede permettant de produire cette tole
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EP2050833A1 (fr) * 2006-07-05 2009-04-22 JFE Steel Corporation Tube en acier soudé de haute tension pour élément structural automobile et son procédé de fabrication

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EP2009120A2 (fr) 2008-12-31
DE102007030207A1 (de) 2009-01-02
EP2009120A3 (fr) 2009-08-19

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