EP0013331B1 - Procédé pour la fabrication de profilés et utilisation d'un acier à grain fin pour des profilés - Google Patents

Procédé pour la fabrication de profilés et utilisation d'un acier à grain fin pour des profilés Download PDF

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Publication number
EP0013331B1
EP0013331B1 EP79104823A EP79104823A EP0013331B1 EP 0013331 B1 EP0013331 B1 EP 0013331B1 EP 79104823 A EP79104823 A EP 79104823A EP 79104823 A EP79104823 A EP 79104823A EP 0013331 B1 EP0013331 B1 EP 0013331B1
Authority
EP
European Patent Office
Prior art keywords
temperature
profiles
cooling
profile
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.)
Expired
Application number
EP79104823A
Other languages
German (de)
English (en)
Other versions
EP0013331A1 (fr
Inventor
Heinz Gross
Friedhelm Retzlaff
Friedrich Reith
Karl Heinz Schlusnus
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.)
Hoesch Werke AG
Hoesch AG
Original Assignee
Hoesch Werke AG
Hoesch 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 Hoesch Werke AG, Hoesch AG filed Critical Hoesch Werke AG
Publication of EP0013331A1 publication Critical patent/EP0013331A1/fr
Application granted granted Critical
Publication of EP0013331B1 publication Critical patent/EP0013331B1/fr
Expired 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
    • C21D6/02—Hardening by precipitation
    • 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
    • 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
    • C21D2261/00—Machining or cutting being involved
    • 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

Definitions

  • the invention relates to a method according to the preamble of claim 1.
  • the aim is to use profiles with high strength values in the delivery state for use as construction parts when high component strengths are to be achieved with small weights, e.g. B. for vehicle parts, hydraulic cylinders, steel structural components or when high loads are inevitable in the design limitation of dimensions, such as. B. in oilfield pipes for drilling technology.
  • small weights e.g. B. for vehicle parts, hydraulic cylinders, steel structural components or when high loads are inevitable in the design limitation of dimensions, such as. B. in oilfield pipes for drilling technology.
  • the pipes to limit the yield strength of the profiles to about 500 N / mm 2 and the tensile strength to about 650 N / mm 2 . Accordingly, the pipes must be formed from strips or piercing soft grades with a yield strength of up to 500 N / mm 2 , welded and, if the demands on the yield strength are higher, liquid-hardened and tempered, ie tempered.
  • the invention has for its object to provide a method of the type mentioned, by means of which the disadvantages of the known methods avoided and in a relatively simple and therefore cost-effective manner while avoiding costly remuneration a manufacture of high-strength profiles, in particular closed tube profiles with a yield strength of more than 500 N / mm 2 , a tensile strength of more than 600 N / mm 2 and high toughness including the required mechanical welding.
  • a precipitation-hardenable fine-grained steel is preferably understood to mean a steel which has a composition of Remainder has iron and usual impurities and which has an ASTM grain size of finer 6 in the finished state.
  • the überalternde artificial aging of the precipitation hardenable fine-grain steel is done in which no grain refinement during cooling of preferably carried out above the A I -temperature at 850 to 750 ° C into a coil gehaspelten steel strip.
  • cooling is slowed down speed reached, through which finely divided excretions are avoided and coagulated excretions are achieved.
  • a corresponding microstructure is achieved according to the invention in sheet metal by furnace cooling, by means of which radiation and convection are prevented, from the rolling heat. With both the coiled steel strip and the steel sheet, it is essential that the slowed down cooling is carried out up to a temperature of 400 ° C., while the subsequent cooling down to room temperature is carried out in any way.
  • an open profile produced cold in this way is preferably welded to a closed tubular profile before further treatment.
  • the open or closed profiles produced according to the invention are subsequently subjected to precipitation hardening, which is also referred to as particle hardening and fine grain hardening, to dissolve the coarse precipitates by solution annealing above the A C3 temperature with subsequent cooling.
  • precipitation hardening which is also referred to as particle hardening and fine grain hardening
  • the type of cooling should be used to achieve the formation of finely divided carbides, nitrides and carbonitrides with simultaneous fine grain formation.
  • the temperature of the solution annealing is advantageously chosen to be the temperature at which the stretch reduction of the starting pipe is started, ie the piercing temperature. A separate solution annealing is then no longer required in these reduced-stretch pipes, since the cooling following the solution annealing takes place during the reduction in stretch or immediately afterwards.
  • tempering at a temperature of 500 to 600 ° C.
  • This tempering can advantageously also be carried out in such a way that the cooling following the solution annealing is interrupted and continued in the range from 500 to 600 ° C. at a reduced cooling rate.
  • a steel with a chemical composition of The rest of the iron and unavoidable impurities are coiled after the hot rolling to a strip, preferably hot wide strip without intermediate cooling after the last rolling pass at a temperature of about 750 ° C. and cooled to 400 ° C. in still air.
  • the natural heat storage capacity of the federal government is used for the aging hot aging, in which the precipitation and coagulation of the carbides, nitrides and carbonitrides take place largely completely, avoiding grain refinement. Further cooling to room temperature is done in any way.
  • the hot wide strip has a yield strength of 455 N / mm 2 and a tensile strength of 650 N / mm 2 after it has completely cooled to room temperature or has aged.
  • the hot wide strip is then cut into strips, trimmed as necessary and subsequently cold formed, in the present example in a continuous process formed into a slotted tube, which is welded to a tube with a diameter of 159 mm by means of a high-frequency welding device.
  • This tube is heated to a temperature of about 1030 ° C and rolled with this temperature as the piercing temperature in a stretch reduction process to the desired diameter of 60.3 mm.
  • the finished tube is cooled on a cooling bed in still air to room temperature.
  • the coarse carbides, nitrides and carbonitrides are dissolved in the steel while the tube is being heated or held to the rolling temperature and are finely distributed during cooling or after the rolling with simultaneous formation of fine grains.
  • the finished tube has a yield strength of 648 N / mm 2 and a tensile strength of 845 N / mm 2 .

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Forging (AREA)
  • Electrochromic Elements, Electrophoresis, Or Variable Reflection Or Absorption Elements (AREA)
  • Diaphragms For Electromechanical Transducers (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Claims (9)

1. Procédé pour fabriquer des profilés ayant une limite apparente d'élasticité > 500 N/mm2, une résistance à la traction ≥600 N/mm2 et une grande ténacité à partir de bande ou de tôle d'acier laminé à chaud, caractérisé par la combinaison des opérations suivantes:
a) la bande ou la tôle d'acier, formée d'un acier à grain fin durcissable par précipitation, est vieillie à chaud avec survieillissement à partir de sa température à la sortie de la dernière passe de laminage, la température finale de laminage étant supérieure à la température Ai, jusqu'à environ 400°C, puis refroidie jusqu'à la température ambiante;
b) la bande ou la tôle d'acier est transformée à froid en un profilé ouvert;
c) le profilé est soumis à un recuit de mise en solution pour la mise en solution des précipitations grossières puis refroidi en vue de la formation de précipitations (carbures, nitrures, carbonitrures) finement divisées.
2. Procédé selon la revendication 1, caractérisé en ce que la bande d'acier enroulée en une bobine est vieillie à chaud avec survieillissement pendant le refroidissement.
3. Procédé selon la revendication 1, caractérisé en ce que la tôle d'acier est vieillie à chaud avec survieillissement par un refroidissement au four à partir de sa température de laminage.
4. Procédé selon une ou plusieurs des revendications 1 à 3, caractérisé en ce que le profilé ouvert est transformé par soudage en un profilé tubulaire fermé.
5. Procédé selon une ou plusieurs des revendications 1 à 4, caractérisé en ce que le profilé est soumis au recuit de mise en solution au-dessus de la température AC3.
6. Procédé selon une ou plusieurs des revendications 1 à 5, caractérisé en ce que le profilé tubulaire fermé est soumis à un laminage d'étirage-réduction, dont la température de début de laminage correspond à la température de recuit de mise en solution.
7. Procédé selon les revendications 1 à 6, caractérisé en ce que les profilés sont soumis à un revenue à une température de 500 à 600° C.
8. Procédé selon les revendications 1 à 7, caractérisé en ce que le refroidissement qui fait suite au recuit de mise en solution est interrompu et est poursuivi dans le domaine de 500 à 600" C avec une vitesse de refroidissement réduite.
9. Utilisation d'un acier à grain fin durcissable par précipitation comme matériau pour la fabrication de profilés soudés à la machine, en particulier de profilés à résistance élevée soudés à haute fréquence, en particulier de tubes, qui présentent, sans traitement, une limite apparente d'élasticité ≥500 N/mm2, une résistance à la traction ≥600 N/mm2 et une résilience élevée.
EP79104823A 1979-01-02 1979-12-01 Procédé pour la fabrication de profilés et utilisation d'un acier à grain fin pour des profilés Expired EP0013331B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE2900022 1979-01-02
DE2900022A DE2900022C3 (de) 1979-01-02 1979-01-02 Verfahren zum Herstellen von Profilen

Publications (2)

Publication Number Publication Date
EP0013331A1 EP0013331A1 (fr) 1980-07-23
EP0013331B1 true EP0013331B1 (fr) 1982-09-15

Family

ID=6059969

Family Applications (1)

Application Number Title Priority Date Filing Date
EP79104823A Expired EP0013331B1 (fr) 1979-01-02 1979-12-01 Procédé pour la fabrication de profilés et utilisation d'un acier à grain fin pour des profilés

Country Status (11)

Country Link
US (2) US4414042A (fr)
EP (1) EP0013331B1 (fr)
JP (1) JPS5591941A (fr)
CA (1) CA1125150A (fr)
DE (1) DE2900022C3 (fr)
ES (1) ES487392A1 (fr)
GR (1) GR66519B (fr)
MX (1) MX152698A (fr)
NO (1) NO151295C (fr)
RO (1) RO80871A (fr)
SU (1) SU1087078A3 (fr)

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3415590A1 (de) * 1984-04-24 1985-10-31 Mannesmann AG, 4000 Düsseldorf Verwendung eines stahls in schwefelwasserstoffhaltigen medien
JPS61272318A (ja) * 1985-05-28 1986-12-02 Nippon Steel Corp 高強度油井管用電縫鋼管の製造方法
DE3628711A1 (de) * 1986-08-23 1988-03-10 Kloeckner Stahl Gmbh Denitrierter, niedriglegierter, hochfester feinkornbaustahl
US5122199A (en) * 1991-07-12 1992-06-16 General Motors Corporation Copper brazed torque converter pump housing made from formable high strength microalloyed steel
SE517429C2 (sv) * 2000-10-19 2002-06-04 Accra Teknik Ab Förfarande,tillverkningsprocess och tillverkningslinje för tillverkning av härdbara metalldetaljer med öppet tvärsnitt
EP1437422A4 (fr) * 2001-06-14 2006-08-23 Jfe Steel Corp Tuyau en acier a haute formabilite, et procede de fabrication
US20080026241A1 (en) * 2006-07-25 2008-01-31 Algoma Tubes, Inc. Steel tubing with enhanced slot-ability characteristics for warm temperature service in casing liner applications and method of manufacturing the same
HUP1300743A2 (hu) * 2013-12-19 2015-06-29 Dunaujvarosi Foeiskola Technikai elrendezés és egységes elven alapuló eljárás többes fázisú és TRIP-acélok szabályozott hõmérsékletvezetésû meleghengerléssel történõ elõállítására
CN112410513A (zh) * 2020-10-14 2021-02-26 无锡市翰沃机械有限公司 一种高空车连接轴的制造方法

Family Cites Families (27)

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Publication number Priority date Publication date Assignee Title
US2222263A (en) * 1940-03-02 1940-11-19 South Chester Tube Company Method of heat treatment for pipes
DE1184509B (de) * 1960-01-21 1964-12-31 Hoesch Ag Die Verwendung von Stahlblechen oder -baendern zur Herstellung von insbesondere schraubennahtgeschweissten Rohren
DE1234995B (de) * 1961-04-27 1967-02-23 Thyssen Roehrenwerke Ag Verwendung von Staehlen, die in der Ferrit-Perlit-Stufe umwandeln
AT260980B (de) * 1964-02-18 1968-04-10 Indugas Ges Fuer Ind Gasverwen Vorrichtung für die Erwärmung oder Wärmebehandlung von Rohren
US3725049A (en) * 1966-03-11 1973-04-03 Nippon Steel Corp Semi-skilled high tensile strength steels
US3673007A (en) * 1968-11-29 1972-06-27 Japan Steel Works Ltd Method for manufacturing a high toughness steel without subjecting it to heat treatment
US3666452A (en) * 1969-07-16 1972-05-30 Jones & Laughlin Steel Corp High-strength low-alloy steels
DE1936589B2 (de) * 1969-07-18 1971-01-14 Thyssen Huette Ag Die Verwendung eines vollberuhigten Stahles fuer geschweisste und/oder kaltumgeformte Bauteile und Konstruktionen aus Blech oder Band
US3726723A (en) * 1970-05-11 1973-04-10 American Metal Climax Inc Hot-rolled low alloy steels
CA952415A (en) * 1970-05-20 1974-08-06 Eiji Miyoshi Process and apparatus for manufacture of strong tough steel plates
IT955174B (it) * 1971-04-20 1973-09-29 Nippon Kokan Kk Acciaio di tipo ad affinazione non termica ad elevata resistenza dota to di eccellente lavorabilita a freddo
DE2133744B2 (de) * 1971-07-07 1973-07-12 August Thyssen-Hütte AG, 4100 Duisburg Die verwendung eines vollberuhigten stahles fuer gegenstaende aus warmgewalztem band
SU428022A1 (ru) * 1972-01-04 1974-05-15 Способ термической обработки труб из низколегированной стали
US3849209A (en) * 1972-02-01 1974-11-19 Nippon Steel Corp Manufacturing method of high tension, high toughness steel
US4145235A (en) * 1972-12-28 1979-03-20 Nippon Steel Corporation Process for producing cold rolled steel sheet and strip having improved cold formabilities
US3925111A (en) * 1972-12-31 1975-12-09 Nippon Steel Corp High tensile strength and steel and method for manufacturing same
SU456840A2 (ru) * 1973-02-26 1975-01-15 Предприятие П/Я М-5481 Способ термомеханической обработки изделий
JPS56488B2 (fr) * 1973-03-19 1981-01-08
SE392483C (sv) * 1973-08-31 1985-10-14 Smedjebackens Valsverk Ab Finkornstal
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DE2844331A1 (de) * 1977-10-14 1979-04-19 Centre Rech Metallurgique Verfahren zur behandlung rohrfoermiger stahlprofile
DE2750867C2 (de) * 1977-11-14 1983-10-20 Benteler-Werke Ag Werk Neuhaus, 4790 Paderborn Verwendung einer Stahllegierung für Rohre zur Türverstärkung

Also Published As

Publication number Publication date
EP0013331A1 (fr) 1980-07-23
CA1125150A (fr) 1982-06-08
NO151295B (no) 1984-12-03
US4414042A (en) 1983-11-08
JPS5591941A (en) 1980-07-11
NO151295C (no) 1985-03-13
NO794340L (no) 1980-07-03
GR66519B (fr) 1981-03-24
DE2900022C3 (de) 1981-12-03
SU1087078A3 (ru) 1984-04-15
ES487392A1 (es) 1980-09-16
MX152698A (es) 1985-10-15
RO80871A (fr) 1983-02-01
DE2900022A1 (de) 1980-07-03
DE2900022B2 (de) 1981-02-26
US4732623A (en) 1988-03-22

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