EP2103704A1 - 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
EP2103704A1
EP2103704A1 EP08004335A EP08004335A EP2103704A1 EP 2103704 A1 EP2103704 A1 EP 2103704A1 EP 08004335 A EP08004335 A EP 08004335A EP 08004335 A EP08004335 A EP 08004335A EP 2103704 A1 EP2103704 A1 EP 2103704A1
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EP
European Patent Office
Prior art keywords
content
hot
long product
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.)
Granted
Application number
EP08004335A
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German (de)
English (en)
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EP2103704B1 (fr
Inventor
Hans Roelofs
Ulrich Urlau
Mirkka Lembke
Guido Olschewski
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.)
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 PL08004335T priority Critical patent/PL2103704T3/pl
Priority to ES08004335T priority patent/ES2391312T3/es
Priority to EP08004335A priority patent/EP2103704B1/fr
Priority to SI200830770T priority patent/SI2103704T1/sl
Publication of EP2103704A1 publication Critical patent/EP2103704A1/fr
Application granted granted Critical
Publication of EP2103704B1 publication Critical patent/EP2103704B1/fr
Active legal-status Critical Current
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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 by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties 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, which have a detrimental 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.
  • 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 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 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 steel bars of 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% 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)
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
PL08004335T PL2103704T3 (pl) 2008-03-10 2008-03-10 Walcowany na gorąco długi produkt i sposób jego wytwarzania
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
SI200830770T SI2103704T1 (sl) 2008-03-10 2008-03-10 Vroče valjani dolg proizvod in postopek za njegovo izdelavo

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

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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)

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

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2453027A1 (fr) * 2010-11-10 2012-05-16 Swiss Steel AG Produit déformé à chaud et son procédé de fabrication
EP2489748A1 (fr) * 2011-02-18 2012-08-22 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
WO2018223160A1 (fr) * 2017-06-07 2018-12-13 Voestalpine Schienen Gmbh Partie de voie ferrée et procédé de fabrication d'une partie de voie ferrée
WO2019180492A1 (fr) * 2018-03-23 2019-09-26 Arcelormittal Pièce forgée en acier bainitique et son procédé de fabrication
US11913099B2 (en) 2017-03-01 2024-02-27 Cleveland-Cliffs Steel Properties Inc. Press hardened steel with extremely high strength and method for production

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1996022396A1 (fr) 1995-01-20 1996-07-25 British Steel Plc Perfectionnements apportes aux aciers bainitiques exempts de carbure, et procedes de production d'aciers de ce type
EP0845544A1 (fr) 1996-11-26 1998-06-03 Ascometal Produit sidérurgique en acier ayant une structure bainitique et procédé pour la fabrication du produit sidérurgique
EP0903418A1 (fr) * 1996-11-25 1999-03-24 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
US20030084965A1 (en) * 2001-10-01 2003-05-08 Sumitomo Metal Industries, Ltd. Steel for machine structural use and method of producing same
CN1477226A (zh) 2003-08-01 2004-02-25 清华大学 中低碳锰系空冷贝氏体钢
US20060144483A1 (en) * 2002-11-19 2006-07-06 Jean Beguinot Method for making an abrasion-resistant steel plate and plate obtained
US20060162825A1 (en) * 2002-11-19 2006-07-27 Usinor Weldable steel building component and method for making same
DE102005052069A1 (de) 2005-10-28 2007-05-03 Saarstahl Ag Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1996022396A1 (fr) 1995-01-20 1996-07-25 British Steel Plc Perfectionnements apportes aux aciers bainitiques exempts de carbure, et procedes de production d'aciers de ce type
EP0903418A1 (fr) * 1996-11-25 1999-03-24 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
EP0845544A1 (fr) 1996-11-26 1998-06-03 Ascometal Produit sidérurgique en acier ayant une structure bainitique et procédé pour la fabrication du produit sidérurgique
US20030084965A1 (en) * 2001-10-01 2003-05-08 Sumitomo Metal Industries, Ltd. Steel for machine structural use and method of producing same
US20060144483A1 (en) * 2002-11-19 2006-07-06 Jean Beguinot Method for making an abrasion-resistant steel plate and plate obtained
US20060162825A1 (en) * 2002-11-19 2006-07-27 Usinor Weldable steel building component and method for making same
CN1477226A (zh) 2003-08-01 2004-02-25 清华大学 中低碳锰系空冷贝氏体钢
DE102005052069A1 (de) 2005-10-28 2007-05-03 Saarstahl Ag Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen

Cited By (18)

* 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
EP2453027A1 (fr) * 2010-11-10 2012-05-16 Swiss Steel AG Produit déformé à chaud et son procédé de fabrication
EP2489748A1 (fr) * 2011-02-18 2012-08-22 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
WO2012110165A1 (fr) * 2011-02-18 2012-08-23 Thyssenkrupp Steel Europe Ag Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et procédé de fabrication correspondant
CN103380217A (zh) * 2011-02-18 2013-10-30 蒂森克虏伯钢铁欧洲股份公司 由复相钢制成的热轧钢板产品及其制造方法
CN103380217B (zh) * 2011-02-18 2015-09-23 蒂森克虏伯钢铁欧洲股份公司 由复相钢制成的热轧钢板产品及其制造方法
EP3061837A1 (fr) 2015-02-27 2016-08-31 Swiss Steel AG Produit longitudinal bainitique nu et son procédé de fabrication
EP3061838A1 (fr) 2015-02-27 2016-08-31 Swiss Steel AG Produit longitudinal bainitique nu et son procédé de fabrication
US11913099B2 (en) 2017-03-01 2024-02-27 Cleveland-Cliffs Steel Properties Inc. Press hardened steel with extremely high strength and method for production
WO2018223160A1 (fr) * 2017-06-07 2018-12-13 Voestalpine Schienen Gmbh Partie de voie ferrée et procédé de fabrication d'une partie de voie ferrée
CN110691856A (zh) * 2017-06-07 2020-01-14 沃斯特阿尔派因钢轨有限责任公司 轨道部件和用于制造轨道部件的方法
US20200199703A1 (en) * 2017-06-07 2020-06-25 Voestalpine Schienen Gmbh Track part and method for producing a track part
CN110691856B (zh) * 2017-06-07 2023-05-02 沃斯特阿尔派因钢轨有限责任公司 轨道部件和用于制造轨道部件的方法
WO2019180563A1 (fr) * 2018-03-23 2019-09-26 Arcelormittal Pièce forgée en acier bainitique et son procédé de fabrication
CN111836908A (zh) * 2018-03-23 2020-10-27 安赛乐米塔尔公司 贝氏体钢的锻造部件及其制造方法
JP2021517609A (ja) * 2018-03-23 2021-07-26 アルセロールミタル ベイナイト鋼の鍛造部品及びその製造方法
RU2763027C1 (ru) * 2018-03-23 2021-12-24 Арселормиттал Кованая деталь из бейнитной стали и способ ее изготовления
WO2019180492A1 (fr) * 2018-03-23 2019-09-26 Arcelormittal Pièce forgée en acier bainitique et son procédé de fabrication

Also Published As

Publication number Publication date
PL2103704T3 (pl) 2012-12-31
EP2103704B1 (fr) 2012-07-11
SI2103704T1 (sl) 2012-11-30
ES2391312T3 (es) 2012-11-23

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