EP3061838B1 - Produit longitudinal bainitique nu et son procédé de fabrication - Google Patents

Produit longitudinal bainitique nu et son procédé de fabrication Download PDF

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Publication number
EP3061838B1
EP3061838B1 EP16157945.3A EP16157945A EP3061838B1 EP 3061838 B1 EP3061838 B1 EP 3061838B1 EP 16157945 A EP16157945 A EP 16157945A EP 3061838 B1 EP3061838 B1 EP 3061838B1
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Prior art keywords
bainitic
blank
long product
steel
bis
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German (de)
English (en)
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EP3061838A1 (fr
Inventor
Mirkka Ingrid LEMBKE
Guido Olschewski
Heiko Haupt-Peter
Hans Roelofs
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Swiss Steel AG
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Swiss Steel AG
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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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/18—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2211/001—Austenite
    • 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
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a bare bainitic long product according to the preamble of claim 1 and uses thereof and a process for its preparation.
  • bainitic materials with a tensile strength of about 1 '300 MPa, for example, could increase the performance of common rails or injectors and thus of the entire internal combustion engine.
  • the WO 2009/090155 A1 describes such an application for a bainitic-ferritic material without TRIP effect.
  • EP 2103704 A1 describes such a product.
  • By the manufacturing process described therein can be dispensed with the addition of aluminum and titanium. This avoids the formation of abrasive oxide inclusions.
  • a high sulfur content of 0.04 to 0.25% additionally improves the machinability.
  • the sulfur forms with manganese sulfide inclusions, which on the one hand facilitate the chip breaking and on the other hand form a protective layer on the tool. Tool life and productivity are increased.
  • the manganese sulfides are also material weaknesses, which can cause cracks under dynamic load. This reduces the life expectancy of dynamically loaded components. Therefore, this steel can not be used for highly stressed safety components.
  • EP 1426453 A1 describes a forging of a bainitic steel, which should be suitable for machining.
  • the good machinability in this case also only by alloying with sulfur, tellurium, selenium, bismuth or lead (see there claims 6 and 7). Both the environmental compatibility and the suitability for highly stressed components is thereby limited.
  • WO 2011/124851 refers to components made by forging or machining long steel. It is therefore not drawn components, which are known to have a relatively low yield ratio.
  • the steels described therein have a low silicon content of at most 0.1% by weight.
  • EP 2103704 A1 describes a bainitic long product with a sulfur content of at least 0.04 wt .-%, wherein due to the manufacturing process, a ratio of yield strength to tensile strength of at most 0.82 is achieved.
  • WO 2011/124851 A2 describes a bainitic component with a yield strength to tensile strength ratio of 0.80 or less.
  • a bright bainitic long product with a bainitic microstructure that can be machined well in machining is currently not yet available for use in dynamically stressed components.
  • the object of the invention is to provide a bright bainitic long product, with which in particular the above disadvantages are avoided. Further objects of the invention relate to uses of the long product according to the invention. Yet another object of the invention is to provide a process for producing a bare bainitic long product.
  • the tensile test according to ISO 6892-1 is a standard procedure for characterizing the mechanical properties of a material. The associated terms are defined in the standard ISO 6892-1.
  • the yield strength Rp0.2 indicates which stress is present at a plastic strain of 0.2%. This parameter is used when there is no sharp transition between elastic and plastic material behavior.
  • the tensile strength Rm is the maximum stress in the measured stress-strain diagram. The tensile strength is reached the moment the sample starts to constrict (local taper of the sample cross-section).
  • the elongation at break A5 is the extension of the sample at the time of fracture, wherein the index 5 refers to the ratio of the initial measuring length L0 to the initial diameter d0.
  • the steel composition according to the invention can be machined significantly better at a constant predetermined tensile strength if the yield ratio Rp0.2 / Rm is above 0.87.
  • the significantly improved machinability manifests itself in significantly longer tool life.
  • the alloying components are selected such that, at conventional cooling rates from 0.1 to 8.0 K / s, a bainitic-martensitic microstructure always results with a tensile strength level of 900 to 1,200 MPa, without costly alloying elements and / or or special equipment for accelerated cooling from the rolling heat must be used.
  • the product In order to be able to adjust the properties according to the invention, the product must be drawn in the temperature range between room temperature and 600 ° C. and then tempered in a temperature range of 250 and 600 ° C.
  • the yield ratio Rp0.2 / Rm decreases, and according to the invention it is to be maintained above 0.87.
  • the yield ratio Rp0.2 / Rm usually falls below this value.
  • the yield ratio Rp0.2 / Rm is in the range of 0.87 to 0.94.
  • the upper limit of the carbon to 0.26% ensures that the tensile strength does not rise above 1'400 MPa. Higher strength values deteriorate the workability in the downstream drawing process or cutting process. Higher carbon contents also promote the formation of carbides, which adversely affects ductility.
  • Silicon suppresses the formation of hard and in machining abrasive Fe 3 C precipitates (cementite).
  • the chosen silicon concentration allows a one-hour annealing treatment at 400 ° C without coarse cementite precipitates can form (based on the description of the carbide-free bainite in WO 96/22396 ). Since silicon is an efficient solid solution in bainite, its content must be limited to at most 1.2 wt .-%, so as not to exceed the maximum desired tensile strength of 1 '400 MPa.
  • the lower limit in manganese to 1.20% by weight and chromium to 0.70% by weight ensures that a bainitic structure can be produced from the forming heat when the air cools down.
  • the manganese content must be limited to 1.70 wt .-%.
  • Chromium constricts the bainite area, which favors the formation of martensite. For this reason, the chromium content must be limited to 1.60 wt .-%.
  • molybdenum can be alloyed to suppress possible temper embrittlement.
  • the precipitation of iron carbides at the primary grain boundaries and a related loss of toughness can thus be prevented.
  • the molybdenum content is to be chosen as low as necessary and is therefore at most 0.3 wt .-%, in particular about 0.15 to 0.28 wt .-%.
  • Nickel improves notched impact strength and therefore has a negative impact on machinability. Therefore, the nickel content is limited to 0.30 wt%, more preferably about 0.05 to 0.1 wt%.
  • Sulfur is a steel pest. It forms manganese sulfide precipitates and weakens the microstructure. This has a negative effect on the fatigue strength of dynamically loaded components. For this reason, the sulfur content was limited to 0.03 wt .-%. Preferably, the sulfur content is 0.010 to 0.020 wt .-% and in particular about 0.015 wt .-%.
  • the addition of aluminum is not mandatory for the production of the product according to the invention and is therefore at most 0.01% by weight, in particular 0.005 to 0.009% by weight.
  • Phosphorus is a steel pest. It goes to the Austenitkorngrenzen and weakens the structure. This has a negative effect on the fatigue strength of dynamically loaded components. For this reason, the phosphorus content was limited to 0.03 wt .-% and is in particular 0.01 to 0.02 wt .-%.
  • Copper is a steel pest. At high copper contents, red brittleness occurs in hot forming. For this reason, the copper content is limited to 0.25 wt .-% and is in particular 0.1 to 0.2 wt .-%.
  • Hard oxide or nitride inclusions have a negative effect on the machinability above a certain size.
  • titanium titanium oxides and coarse titanium carbonitrides
  • aluminum hard Al 2 O 3 compounds
  • at Niobium and vanadium must also be assumed to have a negative effect.
  • the micro-alloying elements titanium, niobium and vanadium are therefore limited to 0.01 wt .-%.
  • Boron is usually alloyed with bainitic steels to suppress the formation of ferrite.
  • the nitrogen present in the steel must be bound with titanium. Since the addition of titanium is to be avoided, this alloy concept can not be used here. Boron will therefore be present only in traces to 0.001 wt .-%.
  • oxide inclusions should be set with an Al 2 O 3 content of ⁇ 50 wt .-%.
  • the metallurgical treatment according to claim 4 is carried out so that soft, glassy silicate inclusions arise with the following relative proportions by weight: 20 to 50% CaO, 25 to 65% SiO 2 and less than 30% Al 2 O 3 . The tool life of the tools used in machining is then significantly extended.
  • a heat treatment of up to 2 hours at 300 to 600 ° C. according to claim 7 may be expedient. Tensions introduced by strain hardening are thereby reduced.
  • the rods were shot peened to remove the iron oxide skin. Thereafter, the rods were either drawn at room temperature or in the temperature range between 350 and 450 ° C by a multi-stage die to the final dimension of ⁇ 40 mm and directed in a two-roll straightening machine. The final conductive heating at 350 resp. 500 ° C was used to reduce deformation-induced surface tensions.
  • the machinability of the manufactured variants was tested in a standard test at the ISF in Dortmund.
  • the test specimens used were double-turned and one-sided center bored rods with a length of 190 mm.
  • the experiments ran under Bechem Avantin 3309 emulsion with a concentration of about 6-8%.
  • the turning tool (CNMG120404-PF4215) was selected to allow the standard steel 42CrMo4 + QT (at Rm ⁇ 1'000 MPa) to have an industrially common machining time of 18 minutes without violating a wear mark width criterion of V Bmax ⁇ 300 ⁇ m.
  • the cutting speed was 200 m / min
  • Table 1 shows the steel compositions used for this comparison.
  • the composition of the existing oxide inclusions was analyzed by scanning electron microscopy using EDX.
  • the structural components of steel 1 were determined quantitatively in the scanning electron microscope (for bainite and ferrite) and in the X-ray diffractometer (for retained austenite). Within the measuring accuracy the differences of the three variants are small. The results are shown in Table 2 for the various heat treatments. For steel 2 there is a 100% compensation structure (tempered martensite). The steels 3 and 4, similar to steel 1, have a mixed structure of bainite, martensite and retained austenite.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Claims (8)

  1. Ebauche de produit longitudinal bainitique renfermant, en pourcentage pondéral :
    0,16 à 0,26 % de carbone,
    0,60 à 1,20 % de silicium,
    1,20 à 1,70 % de manganèse,
    0,70 à 1,60 % de chrome,
    jusqu'à 0,20 % de nickel,
    jusqu'à 0,30 % de molybdène,
    jusqu'à 0,03 % de soufre,
    jusqu'à 0,01 % d'aluminium,
    jusqu'à 0,03 % de phosphore,
    jusqu'à 0,25 % de cuivre,
    jusqu'à 0,001 % de bore,
    jusqu'à 0,01 % de titane,
    jusqu'à 0,01 % de vanadium,
    jusqu'à 0,01 % de niobium,
    50 ppm à 0,015 % d'azote, et
    jusqu'à 0,01 % d'oxygène lié dans des inclusions d'oxyde,
    le complément étant constitué par du fer et des impuretés habituelles des aciers,
    les éléments de structure suivants étant présents :
    60 à 80 % de bainite,
    5 à 30 % de martensite,
    0,5 à 8 % de ferrite, et
    3 à 15 % d'austénite résiduelle, et
    l'essai de traction selon la norme ISO 6892-1 donnant les résultats suivants :
    une limite d'élasticité Rp0.2 = 950 à 1400 MPa,
    une résistance à la traction Rm = 1150 à 1400 MPa, et
    un allongement à la rupture A5 = 9,0 à 17,0 %,
    avec 0,87 < Rp0.2/Rm < 0,99.
  2. Ebauche de produit longitudinal bainitique conforme à la revendication 1,
    dans lequel :
    Rp0,2/Rm = 0,87 à 0,94.
  3. Ebauche de produit longitudinal bainitique conforme à la revendication 1 ou 2,
    caractérisé en ce qu'
    il renferme des inclusions d'oxyde renfermant moins de 50 % en poids d'Al2O3.
  4. Ebauche de produit longitudinal bainitique conforme à la revendication 3,
    dans laquelle les inclusions d'oxyde renferment les proportions pondérales suivantes : 20 à 50 % de CaO, 25 à 65 % de SiO2 et moins de 30% de Al2O3.
  5. Utilisation d'une ébauche de produit longitudinal bainitique conforme à l'une des revendications 1 à 4,
    pour l'usinage par enlèvement de copeaux.
  6. Utilisation d'une ébauche de produit longitudinal bainitique conforme à l'une des revendications 1 à 4,
    pour l'obtention de composants automobiles à charge dynamique, en particulier dans le domaine de l'injection diesel.
  7. Utilisation conforme à la revendication 5 ou 6,
    dans laquelle avant l'usinage par enlèvement de copeaux et/ou l'obtention des composants l'ébauche de produit longitudinal bainitique est soumise à un traitement thermique pendant jusqu'à deux heures à 300 à 600°C.
  8. Procédé d'obtention d'une ébauche de produit longitudinal bainitique conforme à l'une des revendications 1 à 4,
    comprenant les étapes suivantes consistant à :
    fabriquer un alliage d'acier renfermant les proportions pondérales suivantes :
    0,16 à 0,26 % de carbone,
    0,60 à 1,20 % de silicium,
    1,20 à 1,70 % de manganèse,
    0,70 à 1,60 % de chrome,
    jusqu'à 0,20 % de nickel,
    jusqu'à 0,30 % de molybdène,
    jusqu'à 0,03 % de soufre,
    jusqu'à 0,01 % d'aluminium,
    jusqu'à 0,03 % de phosphore,
    jusqu'à 0,25 % de cuivre,
    jusqu'à 0,001 % de bore,
    jusqu'à 0,01 % de titane,
    jusqu'à 0,01 % de vanadium,
    jusqu'à 0,01 % de niobium,
    50 ppm à 0,015 % d'azote, et
    jusqu'à 0,01 % d'oxygène lié dans des inclusions d'oxyde,
    le complément étant constitué par du fer et des impuretés habituelles dans les aciers,
    et effectuer une coulée pour obtenir un modèle de forme prédéfinie, chauffer à nouveau le modèle unitaire, le laminer à chaud pour obtenir un fil ou une barre, et le refroidir à une température inférieure à 400°C avec une vitesse de refroidissement de 0,1 à 8.0 K/s,
    - éliminer chimiquement ou mécaniquement la couche d'oxyde de fer externe,
    - étirer l'acier laminé avec un outil ayant un profil interne prédéfini à une température de 25 à 600°C,
    - effectuer un ajustage mécanique,
    - effectuer une détente à une température de 250 à 600°C.
EP16157945.3A 2015-02-27 2016-02-29 Produit longitudinal bainitique nu et son procédé de fabrication Active EP3061838B1 (fr)

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EP15156898.7A EP3061837A1 (fr) 2015-02-27 2015-02-27 Produit longitudinal bainitique nu et son procédé de fabrication
EP16157945.3A EP3061838B1 (fr) 2015-02-27 2016-02-29 Produit longitudinal bainitique nu et son procédé de fabrication

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JP2022115307A (ja) * 2021-01-28 2022-08-09 横浜ゴム株式会社 ホース用金属ワイヤの仕様決定方法およびホース
FR3123659A1 (fr) 2021-06-02 2022-12-09 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication

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GB2297094B (en) 1995-01-20 1998-09-23 British Steel Plc Improvements in and relating to Carbide-Free Bainitic Steels
ITFI20010136A1 (it) 2001-07-18 2003-01-18 Eos S R L Fibre,filati e tessuti anti-fiamma,loro preparazione ed uso per la produzione di manufatti anti-fiamma,anti-calore e coibentanti
FR2847910B1 (fr) 2002-12-03 2006-06-02 Ascometal Sa Procede de fabrication d'une piece forgee en acier et piece ainsi obtenue.
JP4716359B2 (ja) * 2005-03-30 2011-07-06 株式会社神戸製鋼所 均一伸びに優れた高強度冷延鋼板およびその製造方法
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EP2103704B1 (fr) 2008-03-10 2012-07-11 Swiss Steel AG Produit longitudinal laminé à chaud et son procédé de fabrication
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EP3061837A1 (fr) 2016-08-31

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