EP0481575B1 - Procédé de fabrication de tôles soudables à haute résistance mécanique et leur application - Google Patents

Procédé de fabrication de tôles soudables à haute résistance mécanique et leur application Download PDF

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Publication number
EP0481575B1
EP0481575B1 EP91250279A EP91250279A EP0481575B1 EP 0481575 B1 EP0481575 B1 EP 0481575B1 EP 91250279 A EP91250279 A EP 91250279A EP 91250279 A EP91250279 A EP 91250279A EP 0481575 B1 EP0481575 B1 EP 0481575B1
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EP
European Patent Office
Prior art keywords
max
sheet
cooled
air
less
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP91250279A
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German (de)
English (en)
Other versions
EP0481575A3 (en
EP0481575A2 (fr
Inventor
Klaus Dr. Freier
Klaus Dr. Seifert
Walter Dr. Zimnik
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.)
Preussag Stahl AG
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Preussag Stahl AG
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Publication date
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Publication of EP0481575A2 publication Critical patent/EP0481575A2/fr
Publication of EP0481575A3 publication Critical patent/EP0481575A3/de
Application granted granted Critical
Publication of EP0481575B1 publication Critical patent/EP0481575B1/fr
Anticipated expiration legal-status Critical
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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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling

Definitions

  • the invention relates to a method for producing a high-strength weldable sheet and its use according to the preambles of claims 1 and 4.
  • Such steels are used for all types of welded structures.
  • Thermomechanically rolled, easily weldable steels which can also have a ferritic-pearlitic structure and a yield strength of up to 500 N / mm2, for example grade StE 480.7 TM, have the following composition (in% by weight) according to DE standard DIN 17172: 0 , 04-0.16% C; 0.55% Si; 1.10 to 1.90% Mn; Max. 0.035% P; Max. 0.025% S; Max. 0.20% V and Nb, balance iron.
  • Thick-walled sheets made of known steels with yield strength values above 500 N / mm2 receive their good ones Strength properties apart from the alloy additives, in particular Cr, Mo and higher Ni additions, by accelerated cooling with water directly at the rolling heat (Stahlrohr Handbuch, 10th edition, pp. 79-80, plates XLVII, XLVIII).
  • the invention is therefore based on the problem of proposing a method for producing a thick-walled sheet from high-strength weldable steel which makes it possible to use the advantages of a ferritic-pearlitic structure of the steel and in which water cooling can be dispensed with and a suitable advantageous one Specify use.
  • a steel produced by this special thermomechanical treatment and hardening at temperatures below the transition point A1 has Yield strengths of more than 500 N / mm2 and at the same time ferritic-pearlitic structure. This fine structure gives the steel unexpectedly high toughness values. In extensive tests, it was surprisingly found that it is possible to raise structural steels of this type without accelerated cooling with water by appropriate hardening to yield strength values of up to about 750 N / mm2.
  • the slab can be heated both from room temperature and after hot use to the metallurgically favorable temperature of greater than 1200 ° C. known to the person skilled in the art.
  • Ti is limited to 0.04% in order to positively influence the fine grain structure of the structure in the heat affected zone of welded component edges.
  • the Cu content is deliberately driven above the usual addition amounts in order to activate the strength-increasing effect of Cu by tempering treatment.
  • the potential strength of the steel produced according to the invention is thus exploited as far as possible.
  • the manufacturing process can also be used for steels with yield strengths of approximately 420-500 N / mm2.
  • the alloy additives can be reduced accordingly.
  • weldable structural steels of this strength are known, the method according to the invention saves the use of expensive annealing or cooling treatments.
  • the preferred tempering temperature is 560-600 ° C. In this area, the effect of Cu on the strength values of the steel is optimized. In addition, components in this temperature range usually become low-voltage after welding annealed so that stress relieving cannot adversely affect the metallurgical effect according to the invention.
  • the sheets produced according to the invention in particular with thicknesses of greater than 15 mm to 50 mm and higher, can advantageously be used for offshore structures such as oil platforms, pipes and the like, since the high impact strength combined with a high yield strength and a relatively homogeneous hardness curve over the welding zone of components meet the extreme requirements for the swell strength of steels for such structures.
  • the sheets can also be used in commercial vehicle construction such as B. used in mobile cranes or in mining for support purposes.
  • a strip of 500 mm width was cut from each of the 2 sheets, divided into 5 sections and annealed in electrically heated laboratory annealing furnaces in the temperature range between 440 and 620 ° C. The individual examinations for the two sheet thicknesses will be discussed below.
  • the sheet A 1 was divided into 5 sections Q, R, S, T, U with the dimensions 500 x 400 mm and annealed at 5 tempering temperatures from 480 to 620 ° C. All tempering treatments required an annealing time of 1.5 hours.
  • tempering temperatures of 600 ° C approximately the same yield strength and tensile strength values can be determined. It is remarkable that in the above-mentioned tempering temperature range up to 600 ° C the very high yield strengths with values between 600 and 650 N / mm2 for the transverse samples are still associated with good elongation at break values over 24% and very good indentation values over 70%.
  • the notched impact strength-temperature profiles are shown in Table 4, lower area, as a function of the tempering temperature.
  • values for the transverse samples are still above 200 J / cm2 even at -40 ° C.
  • the samples left at 480 ° C are at the lower limit of a scattering band 620 ° C samples annealed as expected at the upper limit.
  • Ground specimens (not shown) were taken over the entire sheet thickness. They consistently showed the appearance of grain lines with coarser grains for all heat treatment conditions. While most of the structure was made up of extremely fine-grained crystallites of sizes 12 to 13, there were occasional lines with grain sizes 7 to 8. The structure consisted largely of acicular ferrite and pearlite.
  • the notched bar impact specimens also showed extremely high notched bar impact strengths, which were between 239 and 321 J / cm2 at the test temperature of -40 ° C. Even at -80 ° C at least 130 J / cm2 were measured.
  • a steel sheet B 1 of 40 mm thickness was produced from a steel melt B (Table 5) in the same way as in Example 1.
  • the yield strength was 736 N / mm2, the tensile strength 882 N / mm2 with an elongation at break of 20.2%.
  • the melt B showed random traces of Cr and Mo.
  • the sheet C 1 not produced according to the invention has only half the thickness of the sheet B 1, its values for the impact energy (Table 6) on the ISO-V cross-sample are about 20 to 40% lower than for sheet B 1. This shows clearly the effect of the invention.
  • sample sections were cut to length from the sheet A 2 produced according to the invention and these were welded to one another by manual arc welding and UP tandem welding after a V-seam preparation.
  • the samples were subjected to a Vickers hardness test across the weld seam, without first being stress-relieved.
  • Table 7 shows the hardness values for sample A 21.
  • the measured hardness values HV 10 are plotted on the ordinate for the measuring zones of base material (GW), heat affected zone (WEZ) and weld metal.
  • the upper curve in the table shows the Hardness curve at the top of the seam, the lower curve shows the hardness curve at the seam root.
  • the weld seam was created with manual arc welding.
  • Tables 8 and 10 show in an analogous manner the course of hardness over samples A 22, A 23, which, however, were generated by UP tandem welding.
  • Typical of the sheets produced according to the invention are unexpectedly small increases in hardness and decreases in hardness in the heat affected zone.
  • the hardening was a maximum of 20% compared to the hardness in the base material (sample A 23, seam root).
  • HZ heat affected zone
  • Table 11 shows the notched impact energy measured in the welding area for the three samples A 21, A 22, A 23 at the test temperatures + 20 ° C, -10 ° C, -40 ° C.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Laminated Bodies (AREA)
  • Lining Or Joining Of Plastics Or The Like (AREA)

Claims (5)

  1. Procédé de fabrication d'une tôle d'acier à paroi épaisse, ayant une structure ferritique-perlitique, une limite d'étirage supérieure à 500 N/mm² avec en même temps une ténacité élevée et une bonne aptitude au soudage, à partir d'une brame coulée en continu ayant la composition en % en poids :
    0,04 à 0,10 % de C
    0,25 à 0,50 % de Si
    1,40 à 2,00 % de Mn
    max. 0,02 % de P
    max. 0,01 % de S
    0,015 à 0,08 % d'Al
    max. 0,01 % de N
    0,60 à 1,60 % de Ni
    0,60 à 1,60 % de Cu
    0,06 à 0,10 % de V
    0,03 à 0,05 % de Nb
    0,01 à 0,04 % de Ti
    le reste étant constitué par du fer et les impuretés inévitables, dans lequel la brame est chauffée à des températures supérieures à 1200°C, refroidie dans l'air à moins de 1000°C de température de surface, puis laminée thermomécaniquement sans pause de laminage avec une température de fin de laminage d'environ 750 à 650°C, la tôle étant ensuite refroidie dans l'air immobile ou en empilement jusqu'à une température inférieure à 200°C, puis, après un réchauffage à environ 420 à 610°C, à nouveau refroidie dans l'air jusqu'à la température ambiante.
  2. Procédé de fabrication d'une tôle d'acier à paroi épaisse, ayant une structure ferritique-perlitique, une limite d'étirage de 420 à 500 N/mm² avec en même temps une ténacité élevée et une bonne aptitude au soudage, à partir d'une brame coulée en continu ayant la composition en % en poids :
    0,02 à 0,05 % de C
    0,05 à 0,30 % de Si
    1,00 à 1,40 % de Mn
    max. 0,02 % de P
    max. 0,01 % de S
    0,015 à 0,08 % d'Al
    max. 0,01 % de N
    0,30 à 0,60 % de Ni
    0,20 à 0,60 % de Cu
    0,04 à 0,06 % de V
    0,01 à 0,03 % de Nb
    0,01 à 0,04 % de Ti
    le reste étant constitué par du fer et les impuretés inévitables,
    dans lequel la brame est chauffée à des températures supérieures à 1200°C, refroidie dans l'air à moins de 1000°C de température de surface, puis laminée thermomécaniquement sans pause de laminage avec une température de fin de laminage d'environ 750 à 650°C, la tôle étant ensuite refroidie dans l'air immobile ou en empilement jusqu'à une température inférieure à 200°C, puis, après un réchauffage à environ 420 à 610°C, à nouveau refroidie dans l'air jusqu'à la température ambiante.
  3. Procédé selon la revendication 1 ou 2, caractérisé par un traitement de revenu avec un chauffage de la tôle à une température de 560 à 600°C.
  4. Utilisation d'une tôle obtenue conformément à l'une des revendications 1 à 3, ayant une épaisseur de plus de 15 mm pour des constructions soudées de résistance élevée pour bâtiments en mer et constructions de véhicules utilitaires.
  5. Elément de construction obtenu par soudage à l'arc, en tôles ayant une épaisseur supérieure à 15 mm, se composant d'acier ayant une structure ferritique-perlitique, une ténacité élevée et une bonne aptitude au soudage, et réalisées à partir d'une brame coulée en continu avec la composition (en % en poids) :
    0,02 à 0,10 % de C
    0,05 à 0,50 % de Si
    1,00 à 2,00 % de Mn
    max. 0,02 % de P
    max. 0,01 % de S
    0,015 à 0,08 % d'Al
    max. 0,01 % de N
    0,30 à 1,60 % de Ni
    0,20 à 1,60 % de Cu
    0,04 à 0,10 % de V
    0,01 à 0,05 % de Nb
    0,01 à 0,04 % de Ti
    le reste étant constitué par du fer et les impuretés inévitables, brame qui est chauffée à des températures supérieures à 1200°C, refroidie dans l'air à moins de 1000°C de température de surface, puis laminée thermomécaniquement sans pause de laminage avec une température de fin de laminage d'environ 750 à 650°C, la tôle étant ensuite refroidie dans l'air immobile ou en empilement jusqu'à une température inférieure à 200°C, puis, après un réchauffage à environ 420 à 610°C, à nouveau refroidie dans l'air jusqu'à la température ambiance, l'élément de construction présentant un profil de dureté transversalement au cordon de soudure de métal de base à métal de base avec des valeurs de dureté dont les minima et les maxima diffèrent entre eux de moins de 20 %.
EP91250279A 1990-10-19 1991-10-11 Procédé de fabrication de tôles soudables à haute résistance mécanique et leur application Expired - Lifetime EP0481575B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE4033700A DE4033700C1 (fr) 1990-10-19 1990-10-19
DE4033700 1990-10-19

Publications (3)

Publication Number Publication Date
EP0481575A2 EP0481575A2 (fr) 1992-04-22
EP0481575A3 EP0481575A3 (en) 1992-08-26
EP0481575B1 true EP0481575B1 (fr) 1995-06-28

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Family Applications (1)

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EP91250279A Expired - Lifetime EP0481575B1 (fr) 1990-10-19 1991-10-11 Procédé de fabrication de tôles soudables à haute résistance mécanique et leur application

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EP (1) EP0481575B1 (fr)
AT (1) ATE124464T1 (fr)
DE (2) DE4033700C1 (fr)
ES (1) ES2074651T3 (fr)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7727342B2 (en) 2002-02-12 2010-06-01 The Timken Company Low carbon microalloyed steel
CN105132805B (zh) * 2015-09-15 2017-03-15 攀钢集团攀枝花钢铁研究院有限公司 一种含钒焊接结构用钢及其制备方法
DE102018132816A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten profilierten Warmbanderzeugnissen
DE102018132908A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten Warmbanderzeugnissen
CN114438415A (zh) * 2022-01-26 2022-05-06 宝武集团鄂城钢铁有限公司 一种36kg级特厚低温高韧性船板钢及其生产方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3070180D1 (en) * 1979-12-06 1985-03-28 Salzgitter Peine Stahlwerke Hot rolled strip or plate of denitrided steel and process for its production
CS330783A2 (en) * 1982-07-09 1984-06-18 Mannesmann Ag Zpusob vyroby plechu s jemnozrnnou strukturou z nizce legovane oceli pro vyrobu trub velkeho prumeru
CA1207639A (fr) * 1983-03-17 1986-07-15 Rodney J. Jesseman Tole epaisse en alliage d'acier, et sa fabrication
DE3818879C1 (fr) * 1988-06-01 1989-11-16 Mannesmann Ag, 4000 Duesseldorf, De
JPH0794687B2 (ja) * 1989-03-29 1995-10-11 新日本製鐵株式会社 高溶接性、耐応力腐食割れ性および低温靭性にすぐれたｈｔ８０鋼の製造方法

Also Published As

Publication number Publication date
DE59105852D1 (de) 1995-08-03
ES2074651T3 (es) 1995-09-16
ATE124464T1 (de) 1995-07-15
EP0481575A3 (en) 1992-08-26
EP0481575A2 (fr) 1992-04-22
DE4033700C1 (fr) 1992-02-06

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