EP0030309B1 - Feuillard à chaud ou tôle forte en acier dénitruré et procédé pour sa fabrication - Google Patents

Feuillard à chaud ou tôle forte en acier dénitruré et procédé pour sa fabrication Download PDF

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Publication number
EP0030309B1
EP0030309B1 EP80107296A EP80107296A EP0030309B1 EP 0030309 B1 EP0030309 B1 EP 0030309B1 EP 80107296 A EP80107296 A EP 80107296A EP 80107296 A EP80107296 A EP 80107296A EP 0030309 B1 EP0030309 B1 EP 0030309B1
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EP
European Patent Office
Prior art keywords
steel
temperature
hot
intermediate temperature
lies
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
EP80107296A
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German (de)
English (en)
Other versions
EP0030309A3 (en
EP0030309A2 (fr
Inventor
Klaus Dipl.-Ing. Freier
Constantin M. Dr.-Ing. Vlad
Klaus Dipl.-Ing. Hulka
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.)
Stahlwerke Pein Salzgitter AG
Preussag Stahl AG
Original Assignee
Stahlwerke Pein Salzgitter AG
Preussag Stahl 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
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=25782269&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP0030309(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Priority claimed from DE19792949124 external-priority patent/DE2949124C2/de
Priority claimed from DE19803030060 external-priority patent/DE3030060A1/de
Application filed by Stahlwerke Pein Salzgitter AG, Preussag Stahl AG filed Critical Stahlwerke Pein Salzgitter AG
Publication of EP0030309A2 publication Critical patent/EP0030309A2/fr
Publication of EP0030309A3 publication Critical patent/EP0030309A3/de
Application granted granted Critical
Publication of EP0030309B1 publication Critical patent/EP0030309B1/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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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 hot strip or heavy plate from a denitrified steel.
  • the invention further relates to hot strip or heavy plate made from denitrated steel.
  • thermo-mechanical treatment of steels means a controlled reshaping of the steel in a temperature range around the transformation point Ar 3 with a controlled precipitation and / or transformation of the structure at the same time.
  • thermo-mechanically treated steels When mechanically and technologically testing these steels, especially in the presence of notches in a wide temperature range above the complete brittle fracture (Charpy impact test), tears are often observed perpendicular to the fracture surface (referred to as »separation «, »splitting « or »splitting «).
  • »separation«, »splitting « or »splitting « This tendency to split the fracture surfaces of thermo-mechanically treated steels is important, for example, for the operation of long-distance pipelines because it reduces the ability of these steels to stop the propagation of tough fractures.
  • Proposals have already been made for the production of high-strength steels for long-distance pipelines, in which fracture splitting no longer occurs in the impact strength test, but all of which are associated with high alloy costs and high production costs.
  • the invention has for its object to achieve an increased impact strength, even at low temperatures (ie CVN transition temperature TÜ5 0 of at least -30 ° C) by controlling the occurrence of the separations in a hot-rolled hot strip or heavy plate.
  • the hot strip or sheet made of denitrified steel consisting of carbon 0.04 to 0.16%, manganese 1.25 to 1.90%, silicon 0.02 to 0 , 55%, phosphorus 0.004 to 0.020%, sulfur 0.002 to 0.015%, aluminum 0.02 to 0.08%, niobium 0.02 to 0.08%, balance iron and any impurities during hot rolling the last finishing stand with a temperature of Leaves 750 ° C to 820 ° C and is cooled to an intermediate temperature at a cooling rate of 2 to 10 ° C / s if the intermediate temperature is between 450 ° C and 570 ° C and then the hot strip or sheet in the reel or in the stack Air slowly cools to room temperature, creating a ferritic-pearlitic structure.
  • the method according to the invention can therefore significantly improve the usability of the steel, for example for large pipe fem lines, without the need for excessive alloy additives.
  • vanadium 0.02 to 0.10% has a particularly favorable effect on the increase in the strength properties of a steel according to the invention, since the vanadium precipitation takes place mainly in the ferrite grain and not at grain boundaries.
  • the steel has a ferritic-pearlitic structure and the ratio of C v max to C V 100 is between 1.0 and 1.3.
  • C v 100 denotes the high notch impact value (highest values) at which the samples are just showing a 100% deformation fracture.
  • C v max is the temperature-dependent value that has the highest impact value of the entire test.
  • the steel produced according to the invention has a complete absence of fracture splits in the CVN impact test (CVN-Charpy-V-Notch) while at the same time ensuring CVN transition temperatures of at least -30 ° C.
  • the steel of the composition mentioned has a reduced number of separations. Nevertheless, it still has a significantly higher notched impact strength.
  • the notched impact strength in J / cm 2 decreases with increasing number of "separations" in the fracture surfaces of the CVN samples.
  • the reason for this decrease in impact strength lies in the fact that the separations that run perpendicular to the main fracture surface and parallel to the sample surface mainly occur before they pass through the main crack, as can be seen in Figure 1, so that when the samples are bent during the Notch impact test requires less energy to initiate the necking start.
  • Such a material is obtained by maintaining an intermediate temperature of 500 to 570 ° C.
  • the intermediate temperature is 550 ° to 620 ° C
  • the temperature on the last finishing stand from 750 ° C to 850 ° C can be.
  • FIGS. 2 and 3 clearly show the advantages of reducing the number of "separations" in the impact test.
  • the notched impact strength increases on average from 150 J / cm 2 to 230 J / cm 2 for those with molybdenum, chromium or nickel alloys alloyed steels of grade X 70 (Fig. 3) and from 160 J / cm 2 to 280 J / cm 2 for niobvanadin-containing steels of grade X 70 (Fig. 2), which increases the impact strength by 53 or 75%. corresponds.
  • the temperature at which the hot strip or sheet leaves the last finishing stand during hot rolling need not be quite as narrow for a low-separation steel according to the invention as for the production of a separation-free steel.
  • a temperature range of 7 50 ° to 850 ° C is possible.
  • additions of 0.002 to 0.08 zirconium and / or 0.004 to 0.051 cerium can also be used when carrying out the new process with an intermediate temperature of 550 ° to 620 ° C.
  • composition of the steels is shown in Table 6, in which the proportions of the constituents contained in the steel are given in percent. The numbers of the melts are only used to identify the steel.
  • the steels were manufactured according to the parameters given in Table 7. In it are the initial thickness, the thickness of the rolled steel sheet, the blast furnace temperature, the final roll temperature and the temperature after cooling (reel temperature). In all cases with the exception of sheet A, the steel was wound up. The last column shows the cooling rate from the final roll temperature to the reel temperature in ° C / s. The steel then slowly cools down in the reel.
  • the mechanical-technological properties of the investigated and inventive steels are summarized in Table 8.
  • the letters “L” and “Q” characterize the position of the specimen in relation to the rolling direction, namely "L” a longitudinal specimen and “Q” a cross specimen on which the impact test was carried out.
  • the other three columns contain the usual information about the yield strength and tensile strength.
  • the ak value indicates the energy consumption of the steel at various points on the a k curve depending on the temperature.
  • C v 100 characterizes the lowest temperature at which there is still a complete deformation fracture.
  • C v max characterizes the area of maximum energy absorption, while TÜ 50 specifies the temperature at which the Charpy V impact test specimens according to DIN 50115 show 50% deformation fracture in the fracture surfaces in the transition area between brittle fracture and deformation fracture.
  • the next two columns indicate the transition temperature for the points C v 100 and TÜ 50 . It turns out that the TÜ 50 is always considerably below -30 ° C, so that high toughness is guaranteed even at low temperatures.
  • the steels are characterized by a high energy consumption.
  • the quotient C v max to C v l 00 is close to 1, namely between 1 and 1.3. All of these steels are free of tears perpendicular to the fracture surface (separations).
  • Tables 1 to 5 relate to low-separation steels according to the invention with a higher notched impact strength
  • Tables 6 to 8 characterize separation-free steels which naturally have a very high notched impact strength.

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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)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (11)

1. Procédé pour fabriquer du feuillard à chaud ou de la tôle forte au moyen d'un traitement mécanique et thermique par lequel on obtient un formage important de l'acier dans une zone de température du point de conversion Ar3, à partir d'un acier dénitruré constitué par 0,04 à 0,16% de carbone, 1,25 à 1,90% de manganèse, 0,02 à 0,55% de silicium, 0,004 à 0,020% de phosphore, 0,002 à 0,015 de soufre, 0,02 à 0,08% d'aluminium, 0,02 à 0,08 de niobium, le reste étant du fer des impuretés éventuelles, dans lequel dans le cadre du laminage à chaud, le feuillard à chaud ou la tôle quitte la dernière cage finisseuse à une température de 750°C à 820°C, est refroidi à une température intermédiaire avec une vitesse de refroidissement de 2 à 10°C/s, caractérisé en ce que la température intermédiaire est située entre 450°C et 570°C et en ce que le feuillard à chaud ou la tôle refroidit ensuite lentement à la température ambiante à l'air sur le dévidoir ou l'empilage, de sorte qu'une structure ferritique-perlitique est engendrée.
2. Procédé selon la revendication 1, caractérisé en ce qu'à l'acier on ajoute par alliage du vanadium en addition à raison de 0,02 à 0,10%
3. Procédé selon une des revendications 1 ou 2, caractérisé en ce que la température intermédiaire se situe entre 450°C et 500°C.
4. Procédé selon une des revendications 1 ou 2, caractérisé en ce que la température intermédiaire se situe entre 500°C et 570°C.
5. Procédé pour fabriquer du feuillard à chaud ou de la tôle forte au moyen d'un traitement mécanique et thermique par lequel on obtient un formage important de l'acier dans une zone de température du point de conversion Ar3, à partir d'un acier dénitruré constitué par 0,04 à 0,16% de carbone, 1,25 à 1,90% de manganèse, 0,02 à 0,55% de silicium, 0,004 à 0,020 de phosphore, 0,002 à 0,015% de soufre, 0,02 à 0,08% d'aluminium, 0,02 à 0,08% de niobium, ainsi que 0,15 à 0,35% d'additifs de molybdène, 0,10 à 0,30% de chrome, et/ou 0,30 à 0,90% de nickel seul ou en combinaison, le reste étant du fer et des impuretés éventuelles dans lequel dans le cadre du laminage à chaud, le feuillard à chaud ou la tôle forte quitte la dernière cage finisseuse à une température de 750°C à 850°C, est refroidi à une température intermédiaire avec une vitesse de refroidissement de 2 à 10°C/s, caractérisé en ce que la température intermédiaire est sitúee entre 450°C et 620°C et en ce que le feuillard à chaud ou la tôle refroidit ensuite lentement à la température ambiante à l'air sur le dévidoir ou l'empilage, de sorte qu'une structure férritique-perlitique est engendrée.
6. Procédé selon la revendication 5, caractérisé en ce qu'on ajoute par alliage à l'acier, du vanadium en addition à raison de 0,02 à 0,10%
7. Procédé selon une des revendications 5 ou 6, caractérisé en ce que la température intermédiaire se situe entre 450°C et 550°C et en ce que, dans le cadre du laminage à chaud, le feuillard à chaud ou la tôle forte quitte la dernière cage finisseuse à une température de 750°C à 820°C.
8. Procédé selon une des revendications 5 ou 6, caractérisé en ce que la température intermédiaire se situe entre 550°C et 620°C.
9. Procédé selon la revendication 8, caractérisé par une addition de 0,002 à 0,08% de zirconium.
10. Procédé selon la revendication 8 ou 9, caractérisé par une addition de 0,004 à 0,051 %de cérium.
11. Feuillard à chaud ou tôle forte, fabriqué selon un procédé selon une des revendications 1 à 10.
EP80107296A 1979-12-06 1980-11-22 Feuillard à chaud ou tôle forte en acier dénitruré et procédé pour sa fabrication Expired EP0030309B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
DE2949124 1979-12-06
DE19792949124 DE2949124C2 (de) 1979-12-06 1979-12-06 Warmband oder Grobblech aus denitriertem Stahl und Verfahren zu seiner Herstellung
DE19803030060 DE3030060A1 (de) 1980-08-08 1980-08-08 Warmband oder grobblech aus einem denitrierten stahl und verfahren zu seiner herstellung
DE3030060 1980-08-08

Publications (3)

Publication Number Publication Date
EP0030309A2 EP0030309A2 (fr) 1981-06-17
EP0030309A3 EP0030309A3 (en) 1982-05-12
EP0030309B1 true EP0030309B1 (fr) 1985-02-13

Family

ID=25782269

Family Applications (1)

Application Number Title Priority Date Filing Date
EP80107296A Expired EP0030309B1 (fr) 1979-12-06 1980-11-22 Feuillard à chaud ou tôle forte en acier dénitruré et procédé pour sa fabrication

Country Status (4)

Country Link
US (1) US4397697A (fr)
EP (1) EP0030309B1 (fr)
CA (1) CA1149711A (fr)
DE (1) DE3070180D1 (fr)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59100214A (ja) * 1982-11-29 1984-06-09 Nippon Kokan Kk <Nkk> 厚肉高張力鋼の製造方法
US4662950A (en) * 1985-11-05 1987-05-05 Bethlehem Steel Corporation Method of making a steel plate for construction applications
DE3721641C1 (de) * 1987-07-01 1989-01-12 Thyssen Stahl Ag Verfahren zur Herstellung von Warmband
DE3818879C1 (fr) * 1988-06-01 1989-11-16 Mannesmann Ag, 4000 Duesseldorf, De
HU205393B (en) * 1988-06-22 1992-04-28 Gyoergy Vizi Process for producing corner element of steel container from hot rolled steel plate
DE4033700C1 (fr) * 1990-10-19 1992-02-06 Stahlwerke Peine-Salzgitter Ag, 3150 Peine, De
US5833667A (en) * 1993-03-19 1998-11-10 Venetec International, Inc. Catheter anchoring system
JP3509603B2 (ja) * 1998-03-05 2004-03-22 Ｊｆｅスチール株式会社 靱性に優れた降伏強さが３２５ＭＰａ以上の極厚Ｈ形鋼
EP1205570A4 (fr) * 2000-03-02 2004-11-10 Matsushita Electric Ind Co Ltd Cadre de masque d'ecran cathodique couleur, plaque d'acier utile dans ce masque, procede de production de cette plaque, et ecran cathodique couleur dote de ce cadre
DE102020206298A1 (de) * 2020-05-19 2021-11-25 Thyssenkrupp Steel Europe Ag Stahlflachprodukt und Verfahren zu dessen Herstellung

Family Cites Families (20)

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Publication number Priority date Publication date Assignee Title
US3102831A (en) * 1960-08-10 1963-09-03 Molybdenum Corp Production of columbium containing steels
US3704180A (en) * 1968-08-28 1972-11-28 Inland Steel Co Method for producing tough,high strength steel article
USRE28790E (en) * 1969-07-16 1976-04-27 Jones & Laughlin Steel Corporation High-strength low-alloy steels having improved formability
ZA705046B (en) * 1969-07-30 1971-04-28 Armco Steel Corp Process for production of high strength low alloy steel
US3726723A (en) * 1970-05-11 1973-04-10 American Metal Climax Inc Hot-rolled low alloy steels
US3849209A (en) * 1972-02-01 1974-11-19 Nippon Steel Corp Manufacturing method of high tension, high toughness steel
JPS5324892B2 (fr) * 1972-10-19 1978-07-24
US3860456A (en) * 1973-05-31 1975-01-14 United States Steel Corp Hot-rolled high-strength low-alloy steel and process for producing same
US3976514A (en) * 1975-02-10 1976-08-24 Nippon Steel Corporation Method for producing a high toughness and high tensil steel
IT1028878B (it) * 1975-02-10 1979-02-10 Italsider Spa Procedimento per la fabbricazione di un acciaio ad elevata resistenza antiinvecchiante, particolarmente adatto alla costuruzione di tubi saldati ed atto a sopportare elevate deformazioni plastiche a freddo, acciaio atto ad essere impiegato in detto procedimento ed acciaio ottenuto da tale procedimento
JPS5220322A (en) * 1975-08-08 1977-02-16 Sumitomo Metal Ind Ltd Process for producing a hot rolled steel band having a strong toughnes s and a high strength
IT1052444B (it) * 1975-11-28 1981-06-20 Centro Speriment Metallurg Processo per la produzione di acciaio strutturale meccanicamente anisotropo e acciaio cosi ottenuto
JPS52101627A (en) * 1976-02-23 1977-08-25 Sumitomo Metal Ind Ltd Non-tempered shape steel in low temp. toughness
JPS52107225A (en) * 1976-03-05 1977-09-08 Sumitomo Metal Ind Ltd Production of high tensile hot rolled steel
JPS52123921A (en) * 1976-04-13 1977-10-18 Nippon Kokan Kk <Nkk> Production of steel plate with high toughness
JPS5421917A (en) * 1977-07-20 1979-02-19 Nippon Kokan Kk <Nkk> Method of manufacturing non-quenched high-tensile steel having high toughness
JPS5822522B2 (ja) * 1977-08-18 1983-05-10 住友金属工業株式会社 強靭非調質高張力鋼板の製造法
JPS5827327B2 (ja) * 1977-11-21 1983-06-08 日本鋼管株式会社 セパレ−シヨンの生じない制御圧延高張力鋼の製造法
JPS54132421A (en) * 1978-04-05 1979-10-15 Nippon Steel Corp Manufacture of high toughness bainite high tensile steel plate with superior weldability
JPS5828327B2 (ja) * 1978-04-18 1983-06-15 日本鋼管株式会社 極めて優れた延性を有する極低炭素高張力鋼の製造方法

Also Published As

Publication number Publication date
CA1149711A (fr) 1983-07-12
DE3070180D1 (en) 1985-03-28
EP0030309A3 (en) 1982-05-12
EP0030309A2 (fr) 1981-06-17
US4397697A (en) 1983-08-09

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