EP0481575A2 - 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
EP0481575A2
EP0481575A2 EP19910250279 EP91250279A EP0481575A2 EP 0481575 A2 EP0481575 A2 EP 0481575A2 EP 19910250279 EP19910250279 EP 19910250279 EP 91250279 A EP91250279 A EP 91250279A EP 0481575 A2 EP0481575 A2 EP 0481575A2
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EP
European Patent Office
Prior art keywords
max
sheet
cooled
air
steel
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
EP19910250279
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German (de)
English (en)
Other versions
EP0481575A3 (en
EP0481575B1 (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
Application filed by Preussag Stahl AG filed Critical Preussag Stahl AG
Publication of EP0481575A2 publication Critical patent/EP0481575A2/fr
Publication of EP0481575A3 publication Critical patent/EP0481575A3/de
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Publication of EP0481575B1 publication Critical patent/EP0481575B1/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
    • 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, e.g. 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 in addition to the alloy additives, in particular Cr, Mo and higher Ni additions, through accelerated cooling with water directly at the rolling heat (Stahlrohran admir, 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 means of appropriate hardening to yield strength values of up to approximately 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.
  • the invention it is particularly important to consciously set the C content lower than the desired strength values according to the previously customary dimensioning.
  • the use of Mo is also avoided and the aim is to reduce Nb as much as possible in order to improve the toughness properties of the sheet produced according to the invention.
  • 0.06-0.10% V is added as a substitute.
  • 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 the stress relieving annealing cannot adversely affect the metallurgical effect according to the invention.
  • the sheets produced in accordance with 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 of 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.
  • Table 3 The results of all tensile tests are shown in Table 3.
  • Table 4 in the upper part provides an overview of the course of the yield strength (R e ) and tensile strength (R m ) depending on the tempering temperature.
  • 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 of over 200 J / cm2 are found for the cross samples even at -40 ° C.
  • the samples left at 480 ° C are at the lower limit of a scattering band 620 ° C annealed samples 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 about 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 with a thickness of 25 mm, 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 being subjected to a stress-relieved heat treatment beforehand.
  • 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 on the top of the seam, the lower curve shows the hardness curve on 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 produced 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 hardness 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)
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 true EP0481575A2 (fr) 1992-04-22
EP0481575A3 EP0481575A3 (en) 1992-08-26
EP0481575B1 EP0481575B1 (fr) 1995-06-28

Family

ID=6416886

Family Applications (1)

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

Country Status (4)

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

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2003069008A1 (fr) * 2002-02-12 2003-08-21 The Timken Company Acier microallie a faible teneur en carbone
CN105132805A (zh) * 2015-09-15 2015-12-09 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
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

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102018132908A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten Warmbanderzeugnissen
DE102018132816A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten profilierten Warmbanderzeugnissen

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0030309A2 (fr) * 1979-12-06 1981-06-17 Preussag Stahl Aktiengesellschaft Feuillard à chaud ou tôle forte en acier dénitruré et procédé pour sa fabrication
EP0098564A1 (fr) * 1982-07-09 1984-01-18 MANNESMANN Aktiengesellschaft Procédé de fabrication de tôles soudables à grain fin pour grands tubes
EP0123406A2 (fr) * 1983-03-17 1984-10-31 Armco Inc. Plaque en acier faiblement allié et procédé de production
EP0345206A1 (fr) * 1988-06-01 1989-12-06 MANNESMANN Aktiengesellschaft Procédé de fabrication de tôles fortes
DE4009971A1 (de) * 1989-03-29 1990-10-04 Nippon Steel Corp Verfahren zum herstellen hochfesten stahls mit verbesserter schweissbarkeit und niedertemperaturzaehigkeit

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0030309A2 (fr) * 1979-12-06 1981-06-17 Preussag Stahl Aktiengesellschaft Feuillard à chaud ou tôle forte en acier dénitruré et procédé pour sa fabrication
EP0098564A1 (fr) * 1982-07-09 1984-01-18 MANNESMANN Aktiengesellschaft Procédé de fabrication de tôles soudables à grain fin pour grands tubes
EP0123406A2 (fr) * 1983-03-17 1984-10-31 Armco Inc. Plaque en acier faiblement allié et procédé de production
EP0345206A1 (fr) * 1988-06-01 1989-12-06 MANNESMANN Aktiengesellschaft Procédé de fabrication de tôles fortes
DE4009971A1 (de) * 1989-03-29 1990-10-04 Nippon Steel Corp Verfahren zum herstellen hochfesten stahls mit verbesserter schweissbarkeit und niedertemperaturzaehigkeit

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2003069008A1 (fr) * 2002-02-12 2003-08-21 The Timken Company Acier microallie a faible teneur en carbone
US7727342B2 (en) 2002-02-12 2010-06-01 The Timken Company Low carbon microalloyed steel
CN105132805A (zh) * 2015-09-15 2015-12-09 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
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
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

Also Published As

Publication number Publication date
ATE124464T1 (de) 1995-07-15
EP0481575A3 (en) 1992-08-26
DE59105852D1 (de) 1995-08-03
DE4033700C1 (fr) 1992-02-06
EP0481575B1 (fr) 1995-06-28
ES2074651T3 (es) 1995-09-16

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