EP2103704B1 - Produit longitudinal laminé à chaud et son procédé de fabrication - Google Patents

Produit longitudinal laminé à chaud et son procédé de fabrication Download PDF

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Publication number
EP2103704B1
EP2103704B1 EP08004335A EP08004335A EP2103704B1 EP 2103704 B1 EP2103704 B1 EP 2103704B1 EP 08004335 A EP08004335 A EP 08004335A EP 08004335 A EP08004335 A EP 08004335A EP 2103704 B1 EP2103704 B1 EP 2103704B1
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EP
European Patent Office
Prior art keywords
hot
long product
content
product according
rolled long
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.)
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Application number
EP08004335A
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German (de)
English (en)
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EP2103704A1 (fr
Inventor
Hans Roelofs
Ulrich Urlau
Mirkka Lembke
Guido Olschewski
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Swiss Steel AG
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Swiss Steel AG
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 Swiss Steel AG filed Critical Swiss Steel AG
Priority to SI200830770T priority Critical patent/SI2103704T1/sl
Priority to ES08004335T priority patent/ES2391312T3/es
Priority to EP08004335A priority patent/EP2103704B1/fr
Priority to PL08004335T priority patent/PL2103704T3/pl
Publication of EP2103704A1 publication Critical patent/EP2103704A1/fr
Application granted granted Critical
Publication of EP2103704B1 publication Critical patent/EP2103704B1/fr
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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 hot-rolled long product according to the preamble of claim 1 and a method for its production.
  • tempered steels are generally used. With tempered steels it is possible to achieve tensile strengths of more than 1 000 MPa with simultaneous necking of more than 45%.
  • the necessary heat treatment heat treatment, quenching, tempering
  • expensive post-processing straightening, grinding
  • Pre-tempered steels have significant disadvantages in machining (long chips, low tool life). These processing disadvantages can be somewhat reduced by the addition of a maximum of 0.04 wt.% Sulfur. Higher levels of sulfur degrade the manufacturability and microscopic purity of these Al-alloyed steels.
  • the tempered steels are alloyed with at least 0.015% aluminum.
  • hard and abrasive Al 2 O 3 -containing oxide inclusions are produced during the cutting process, which have a negative effect on tool life.
  • these inclusions In order to achieve good machinability, these inclusions must be converted into less abrasive calcium aluminate inclusions by adding calcium in a complex metallurgical process.
  • ferritic-martensitic dual-phase steels were developed.
  • the structure of these steels is via a thermomechanical Treatment achieved during hot rolling.
  • good toughness properties can only be set as long as the stored martensite islands remain small enough.
  • the achievable tensile strength is thereby limited to below 1'000 MPa.
  • Steels for pipe production must be characterized in particular by good toughness and weldability. For this to be achieved, a low carbon content of less than 0.13 wt% is required.
  • the desired high-strength, tough structure is achieved by accelerated cooling from the rolling heat. In the temperature range of 800 to 500 ° C (range of conversion) cooling rates of 10 to 40 K / s are used.
  • the structure of these steels then consists of allotriomorphic ferrite and bainite (at least 20%).
  • the low carbon content of the accelerated cooling guarantees the avoidance of high martensite content, which enables good toughness properties.
  • the tensile strength is thereby limited to below 1'000 MPa.
  • US 2003 0084 965 discloses a machinable steel with 0.1-0.6 C, 0.01-2.0 Si, and 0.005-0.20 s.
  • EP 0845544 (C ⁇ 0.12%) describes a microalloyed bainitic steel which has a tensile strength of more than 1000 MPa at room temperature. To achieve these properties, the steel is austenitized again after rolling and then quenched at a cooling rate of 17 to 150 K / s. These cooling rates are well above the air cooled long products in conventional rolling mills.
  • An easily machinable bainitic-martensitic complex phase steel for the production of air-cooled conventionally hot-rolled long products in a size range of 5.0 to 70 mm is not yet available.
  • the material concept must be designed in such a way that the dimensional differences in the cooling rate of approx. 0.1 to 8.0 K / s do not lead to any significant fluctuations in the mechanical-technological properties of the final product.
  • the object of the invention is to provide an improved hot-rolled long product, with which in particular the above disadvantages are avoided.
  • Another object of the invention is to provide a process for producing a hot-rolled long product.
  • the alloying components are selected so that at usual cooling rates from the rolling heat of 0.1 to 8.0 K / s a bainitic-martensitic microstructure always results with a tensile strength level of 1'000 to 1400 MPa, without costly alloying elements and / or or special equipment for accelerated cooling from the rolling heat must be used.
  • the lower limit of the carbon content to 0.20% ensures, in combination with manganese and chromium, that only small amounts of ferrite are present in the microstructure. Ferrite levels above 10% affect both the strength level and impact strength of the product.
  • the upper limit of the carbon to 0.25% ensures that the tensile strength does not rise above 1400 MPa. Higher strength values degrade machinability in the downstream drawing or machining process. Higher carbon contents also promote the formation of carbides, which adversely affects ductility.
  • Silicon affects the carbon activity and slows down the precipitation of carbides.
  • the selected silicon concentration allows a one-hour annealing treatment at 400 ° C without degrading the ductility due to carbide precipitations (based on the description of the carbide-free bainite in WO 96/22396 ). Since silicon is an efficient solid solution hardener in bainite, its content must be limited to 1.35% in order not to exceed the maximum desired tensile strength of 1400 MPa.
  • the manganese content is too high, the manganese segregations are pronounced and the microstructure becomes very inhomogeneous. For this reason, the "free”, ie not bound in manganese sulfides, manganese content ( ⁇ total manganese content - 1.72 Sulfur content) to 1.50%.
  • the so determined manganese content is not sufficient to achieve a bainitic-martensitic structure after air cooling from the rolling heat.
  • the product must also contain so much chromium that chromium content + (manganese content - 1.72 sulfur content)> 2.6% by weight applies. Together with a carbon content of at least 0.20%, a bainitic-martensitic microstructure with ⁇ 10% ferrite is ensured.
  • Molybdenum is said to prevent the precipitation of iron carbides at the primary grain boundaries and associated loss of toughness. For cost reasons, the molybdenum content should be as low as necessary: 0.1 to 0.5% molybdenum.
  • the steel should contain at least 0.04%, preferably 0.12 to 0.17% sulfur.
  • the sulfur combines with manganese to form manganese sulfide precipitates, thus improving both chip breaking and tool life. Since these precipitates also reduce the transverse toughness of the hot-rolled long product, the addition of sulfur should be limited to 0.25%.
  • the aluminum content should be limited to 0.01%.
  • oxide inclusions should be set with an Al 2 O 3 content of ⁇ 50%.
  • the metallurgical treatment is carried out so that soft, glassy silicate inclusions are formed with the following relative proportions by weight: 20 to 50% CaO, 35 to 65% SiO 2 and less than 25% Al 2 O 3 . The tool life of the tools used in machining is then significantly extended.
  • the good machinability of the hot-rolled long product produced according to the invention can be further improved according to claim 3 or 4 by the addition of 0.05 to 0.3% lead or 0.05 to 0.3% bismuth.
  • the austenite grain size before the structural transformation and the cooling rate during structural transformation in a temperature range between 800 and 500 ° C. are of crucial importance.
  • a fine austenite grain leads to a finer final structure with better toughness values.
  • the austenite grain after the last forming step according to claim 7 should not be greater than 50 ⁇ m.
  • the cooling rates should be between 0.1 and 8.0 K / s.
  • the upper value is given by the possibilities of conventional cooling of accelerated air.
  • the lower limit of 0.1 K / s is to ensure that no ferrite> 10% occur. Large bar dimensions that cool down inside the bar much slower than 0.1 K / s can not be produced with this technology.
  • a heat treatment for 0.5 to 2 hours at 300 to 500 ° C according to claim 8 may be useful.
  • the high silicon content of the product delays the rearrangement of carbon atoms in the microstructure. This is desirable to suppress the formation of coarse carbide precipitates.
  • also in connection with carbon known aging processes that begin immediately after the hot rolling slowed down. In particular, the maximum ductility of the structure sets in only after a few weeks. In cases where the rolled long product is to be further processed immediately, a heat treatment is therefore recommended.
  • a molten steel was poured and then rolled into bar steel in various dimensions.
  • the molten steel was produced by the electrical steel process with a secondary metallurgical treatment on a ladle and subsequent casting to 150 ⁇ 150 mm 2 sticks in a continuous casting plant.
  • the billets were then reheated in a walking beam oven to 1'150 to 1'200 ° C and then to bar steel in the dimensions 22 (cooling rate is about 1.5 K / s) and 52 mm (cooling rate is about 0.4 K / s) rolled.
  • the cooling of the rods after rolling was carried out in air.
  • the steel was made 0.22% to carbon 0.94% silicon 00:07% nickel 0.14% to molybdenum 00:15% sulfur 0.003% aluminum 0.012% phosphorus ⁇ 0.001% boron 0.011% titanium ⁇ 0.003% lead ⁇ 0.003% bismuth 0.013% nitrogen 1.60% manganese 1:34% Manganese - 1.72 Sulfur 1:54% chrome 2.88% Chromium + (manganese - 1.72 sulfur) and other impurities caused by melting.
  • the high sulfur content of 0.15% ensures good chip breaking and improves tool life.
  • the low aluminum content suppresses the formation of hard, abrasive, clay-containing oxide inclusions.
  • the metallographic micrographs at 200x magnification are in the Fig. 1 shown.
  • the microstructure is a very fine mixed structure.
  • the bainite and martensite fractions could not be reliably quantified.
  • the pictures as well as the obtained strength level show that the structure consists primarily (>> 50%) of bainite.
  • the structure of the 52 mm rod is slightly coarser than the structure of the 22 mm rod due to the low cooling rate from the rolling heat.
  • manganese sulphides which can serve as nucleating sites for ferrite formation
  • isolated ferrite grains can be recognized.
  • the ferrite content is extremely low ( ⁇ 10%).
  • the determination of the residual austenite quantity in the X-ray diffractometer showed 5.1 ⁇ 0.45% for the 22 mm rod and 4.4 ⁇ 1.34% for the 52 mm rod.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (8)

  1. Produit longitudinal laminé à chaud comportant en proportion pondérale :
    0,20 à 0,25 % de carbone
    0,90 à 1,35 % de silicium
    jusqu'à 0,20 % de nickel
    jusqu'à 0,5 % de molybdine
    0,04 à 0,25 % de soufre
    jusqu'à 0,01 % d'aluminium
    jusqu'à 0,035 % de phosphore
    jusqu'à 0,0008 % de bore
    jusqu'à 0,02 % de titane
    jusqu'à 0,3 % de plomb
    jusqu'à 0,3 % de bismuth
    jusqu'à 1,93 % de manganèse
    jusqu'à 4,0 % de chrome
    jusqu'à 0,02 % d'azote, et
    jusqu'à 0,01 % d'azote lié dans des inclusions oxydées,
    le reste étant constitué par du fer et par des impuretés inévitables, étant précisé que
    (teneur en manganèse - 0,72 teneur en soufre) < à 1,50 % et
    teneur en chrome + (teneur en manganèse - 1,72 teneur en soufre) > à 2,6 % en poids,
    avec les composants de structure suivants :
    50 à 90 % de bainite
    jusqu'à 50 % de martensite
    jusqu'à 10 % de ferrite, et
    jusqu'à 10 % d'austenite résiduelle.
  2. Produit longitudinal laminé à chaud conforme à la revendication 1,
    caractérisé en ce qu'
    il renferme des inclusions oxydées avec moins de 50 % en poids d'Al2O3, ces inclusions oxydées étant de préférence situées dans les plages de proportions relatives suivantes : 20 à 50 % de CaO, 35 à 65 % de SiO2 et moins de 25 % d Al2O3.
  3. Produit longitudinal laminé à chaud conforme à la revendication 1 ou 2, ayant une teneur en plomb de 0,05 à 0,3 % en poids.
  4. Produit longitudinal laminé à chaud conforme à l'une des revendications 1 à 3, ayant une teneur en bismuth de 0,05 à 0,3 % en poids
  5. Produit longitudinal laminé à chaud conforme à l'une des revendications 1 à 4, ayant une résistance à la rupture par traction si Rm de 1000 à 1400 MPa.
  6. Utilisation d'un produit longitudinal conforme à l'une des revendications 1 à 5 pour l'usinage par enlèvement de copeaux.
  7. Procédé d'obtention d'un produit longitudinal laminé à chaud conforme à l'une des revendications 1 à 5, selon lequel
    - la granulométrie moyenne de l'austénite après la dernière étape de formage à chaud est inférieure à 50 µm,
    - le refroidissement de la chaleur de déformation s'effectue dans de l'air au repos ou en mouvement de sorte que la plage de température comprise entre 800 et 500°C est traversée avec un taux de refroidissement de 0,1 à 8,0 K/s.
  8. Procédé d'obtention d'un produit longitudinal laminé à chaud conforme à la revendication 7, selon lequel la maturation de la structure de l'acier après le laminage à chaud est accéléré par un traitement thermique complémentaire ultérieur pendant 0,5 à 2 heures à 300 à 500°C.
EP08004335A 2008-03-10 2008-03-10 Produit longitudinal laminé à chaud et son procédé de fabrication Active EP2103704B1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
SI200830770T SI2103704T1 (sl) 2008-03-10 2008-03-10 Vroče valjani dolg proizvod in postopek za njegovo izdelavo
ES08004335T ES2391312T3 (es) 2008-03-10 2008-03-10 Producto longitudinal laminado en caliente y procedimiento para su fabricación
EP08004335A EP2103704B1 (fr) 2008-03-10 2008-03-10 Produit longitudinal laminé à chaud et son procédé de fabrication
PL08004335T PL2103704T3 (pl) 2008-03-10 2008-03-10 Walcowany na gorąco długi produkt i sposób jego wytwarzania

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP08004335A EP2103704B1 (fr) 2008-03-10 2008-03-10 Produit longitudinal laminé à chaud et son procédé de fabrication

Publications (2)

Publication Number Publication Date
EP2103704A1 EP2103704A1 (fr) 2009-09-23
EP2103704B1 true EP2103704B1 (fr) 2012-07-11

Family

ID=39864799

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EP08004335A Active EP2103704B1 (fr) 2008-03-10 2008-03-10 Produit longitudinal laminé à chaud et son procédé de fabrication

Country Status (4)

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EP (1) EP2103704B1 (fr)
ES (1) ES2391312T3 (fr)
PL (1) PL2103704T3 (fr)
SI (1) SI2103704T1 (fr)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2453026A1 (fr) * 2010-11-10 2012-05-16 Swiss Steel AG Produit d'acier déformé à chaud et son procédé de fabrication
EP2489748B1 (fr) * 2011-02-18 2017-12-13 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication
EP3061837A1 (fr) 2015-02-27 2016-08-31 Swiss Steel AG Produit longitudinal bainitique nu et son procédé de fabrication
KR20190115024A (ko) 2017-03-01 2019-10-10 에이케이 스틸 프로퍼티즈 인코포레이티드 극도로 높은 강도를 갖는 프레스 경화 강
AT519669B1 (de) * 2017-06-07 2018-09-15 Voestalpine Schienen Gmbh Gleisteil und Verfahren zur Herstellung eines Gleisteils
WO2019180492A1 (fr) * 2018-03-23 2019-09-26 Arcelormittal Pièce forgée en acier bainitique et son procédé de fabrication

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2297094B (en) 1995-01-20 1998-09-23 British Steel Plc Improvements in and relating to Carbide-Free Bainitic Steels
WO1998023784A1 (fr) * 1996-11-25 1998-06-04 Sumitomo Metal Industries, Ltd. Acier d'excellente usinabilite et composant usine
US5922145A (en) * 1996-11-25 1999-07-13 Sumitomo Metal Industries, Ltd. Steel products excellent in machinability and machined steel parts
FR2756298B1 (fr) 1996-11-26 1998-12-24 Ascometal Sa Acier et procede pour la fabrication d'une piece de mecanique ayant une structure bainitique
JP3468239B2 (ja) * 2001-10-01 2003-11-17 住友金属工業株式会社 機械構造用鋼及びその製造方法
FR2847271B1 (fr) * 2002-11-19 2004-12-24 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR2847273B1 (fr) * 2002-11-19 2005-08-19 Usinor Piece d'acier de construction soudable et procede de fabrication
CN1210430C (zh) 2003-08-01 2005-07-13 清华大学 中低碳锰系空冷贝氏体钢
DE102005052069B4 (de) 2005-10-28 2015-07-09 Saarstahl Ag Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen

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Publication number Publication date
SI2103704T1 (sl) 2012-11-30
PL2103704T3 (pl) 2012-12-31
EP2103704A1 (fr) 2009-09-23
ES2391312T3 (es) 2012-11-23

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