EP0725156B1 - Stahl mit hoher Dehnbarkeit, Verfahren zur Herstellung und Verwendung - Google Patents

Stahl mit hoher Dehnbarkeit, Verfahren zur Herstellung und Verwendung Download PDF

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Publication number
EP0725156B1
EP0725156B1 EP96400061A EP96400061A EP0725156B1 EP 0725156 B1 EP0725156 B1 EP 0725156B1 EP 96400061 A EP96400061 A EP 96400061A EP 96400061 A EP96400061 A EP 96400061A EP 0725156 B1 EP0725156 B1 EP 0725156B1
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Prior art keywords
steel
component
temperature
minutes
room temperature
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Expired - Lifetime
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EP96400061A
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English (en)
French (fr)
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EP0725156A1 (de
Inventor
Jean Beguinot
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Industeel France SAS
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Industeel France SAS
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    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten

Definitions

  • the present invention relates to a weldable steel having a high tensile strength and good ductility.
  • Staged quenching heat treatment comprising a cooling at a cooling rate greater than or equal to 50 ° C / s up to a holding temperature, then an isothermal holding at this temperature, and finally, cooling down to the temperature ambient, is well suited for thin sheets or small parts of mechanical, but it is completely unsuitable for thick sheets, especially when they are large. Cool a sheet metal to a cooling speed greater than 50 ° C / s is all the more difficult that the sheet is thick, and, by the mere fact of the laws that govern transfers heat, it even becomes impossible when the thickness of the sheet exceeds 15 mm.
  • Inter-critical treatments are also unsuitable for manufacture of sheets with very high yield strength. Indeed, these treatments consist in bringing the steel to an intermediate temperature between the austenitization start temperature and the temperature complete austenitization, so that such treatment followed by quenching leads to mixed structures made up of a mixture of structures hardened and very softened ferrite. The presence of very softened ferrite significantly reduces the level of breaking strength it is possible to get.
  • the object of the present invention is to remedy these disadvantages by proposing a weldable steel which makes it possible to manufacture industrially welded sheets greater than 8 mm thick, having a tensile strength greater than 1200 MPa, and having a very good ductility, i.e. a uniform elongation rate greater than 5%.
  • the chemical analysis is adjusted so that: 0.005% ⁇ Ti ⁇ 0.1% 0.01% ⁇ Al ⁇ 0.5% 0.003 ⁇ N ⁇ 0.02% and, when the steel is in the solid state, the number of precipitates of titanium nitrides of size greater than 0.1 ⁇ m counted over an area of 1 mm 2 of a micrographic section, is preferably less than 4 times the total content of titanium precipitated in the form of nitrides, expressed in thousandths of% by weight.
  • the steel contains from 0.5% to 3% of chromium, less than 2% manganese, and the molydene content plus half the tungsten content is between 0.1% and 2%.
  • the sum of the silicon contents and aluminum is between 1.5% and 2.5%, and it is preferable that the carbon content is between 0.2% and 0.3%.
  • the room can be allowed to cool in air.
  • the invention finally relates to a steel part, and in particular a sheet of thickness greater than 8 mm, obtained by the process according to the invention, the tensile strength of which is greater than 1200 MPa and the ductility measured by uniform elongation is greater than 5%.
  • the structure of the part comprises from 5% to 30% and preferably from 10% to 20% residual austenite.
  • steel contains titanium, its structure preferably comprises more than 30% bainite.
  • This part is particularly suitable for manufacturing equipment for mines or quarries which must resist abrasion or manufacture of metal construction parts or parts boilermaking.
  • the steel according to the invention is a structural steel weakly or moderately alloyed which makes it possible to obtain, by a treatment suitable thermal, a mixed structure consisting of bainite and / or martensite, and from 5% to 30%, and preferably from 10% to 20%, of strongly austenite loaded with carbon.
  • the inventors found that such a structure had the advantage of combining a very high tensile strength and a very good ductility, even for low carbon contents, which allows good weldability, but only if the steel contains sufficient alloying elements increasing the hardenability.
  • the increase in ductility results from the instability of the austenite which transforms into martensite when the steel undergoes plastic deformation.
  • austenite content of the structure must be greater than 5% and preferably greater than 10%; however this content must remain below 30% and preferably 20% to avoid reducing the elastic limit too much.
  • the steel must contain more than 0.15% carbon, and preferably more than 0.2%.
  • the content carbon should remain less than or equal to 0.303%, and preferably, less than 0.3%.
  • the optimal content of carbon is between 0.2% and 0.24%.
  • steel To promote carbon enrichment of austenite during heat treatment, steel must contain at least one element taken from silicon and aluminum.
  • the sum of the silicon contents and aluminum should be greater than 1%, and preferably, greater than 1.5%. However, in order to avoid development difficulties, this sum must remain below 3%, and preferably below 2.5%. So the aluminum and silicon contents are each between 0% and 3%.
  • Manganese which greatly increases the hardenability, is also necessary in contents higher than 0.1% to obtain a good hot ductility, but its content must remain below 4.5%, and preferably less than 2%, so as not to stabilize the austenite too much. Of preferably, the manganese content must be between 1.2% and 1.7%.
  • Nickel which is not essential, increases the hardenability and has a favorable effect on the weldability and on the toughness at low temperature. But this item is expensive. In addition, too strong contents, it stabilizes the austenite too much. Also its content must remain below 9%. Preferably, the nickel content must be between 1.5% and 2.5%.
  • Chromium, molybdenum and tungsten are also not essential, but these elements increase the hardenability and above all can form very hardening carbides.
  • chromium content must be greater than 0.5%, and, from preferably also less than 3%, and more preferably less than 1.5%.
  • Tungsten in Any Content Has Effects equivalent to that of molybdenum in half content. Also for these two elements we consider the sum of the molybdenum content and the half the tungsten content. Beyond 3% the effect is no longer significant for the steels concerned, and this value is a maximum. Well that these two elements are not essential, it is desirable that the sum of the molybdenum content and half the content of tungsten is greater than 0.1%. Preferably, the sum of the content molybdenum and half the tungsten content should be less at 2%, and preferably less than 0.5%.
  • steel contains less than 0.02% nitrogen, however it may be desirable to increase the content of this element up to 0.3% to provide additional hardening without harming weldability.
  • the structure of the steel contains more than 30% of bainite, its toughness can be increased by adding between 0.005% and 0.1% of titanium.
  • the steel must then contain between 0.01% and 0.5% aluminum and between 0.003% and 0.02% nitrogen, in addition, the titanium must be added to the steel in a very gradual way to limit the precipitation of large titanium nitrides in liquid steel.
  • a steel is thus obtained which, in the solid state, is such that the number of precipitates of titanium nitrides of size greater than 0.1 ⁇ m counted over an area of 1 mm 2 of a micrographic section, is less than 4 times the total content of precipitated titanium in the form of titanium nitrides, expressed in thousandths of% by weight.
  • titanium is in this form in steel, it considerably refines the structure and the bainitic sub-structure. This has the effect of lowering the resilience transition temperature by at least 30 ° C and significantly increasing the resilience at room temperature, when the steel structure comprises at least 30% bainite.
  • the rest of the chemical composition of steel is made up by iron and by impurities resulting from the production.
  • the steel contains 0.2% 0.24% carbon, 1.5% to 2.5% silicon plus aluminum, 1.2% 1.7% manganese, 1.5% 2.5% nickel, 0.5% 1.5% chromium, from 0.1% to 0.5% molybdenum, possibly from 0.0005% to 0.005% boron, possibly from 0.005% to 0.1% of titanium introduced as shown above.
  • This heat treatment makes it possible to obtain a structure consisting of martensite and / or lower bainite which are not very softened and from 5% to 30% of residual austenite highly enriched in carbon.
  • the slow passage in the vicinity of M s allows the carbon enrichment of the austenite. It must therefore be long enough, but not too long so as not to soften the structure too much.
  • Heat treatment can be done either in the warm of shaped by hot plastic deformation, either after this surgery.
  • the semi-finished product When the heat treatment is done in the hot forming by hot plastic deformation, the semi-finished product must be reheated before plastic deformation to a temperature higher than Ac 3 and lower than 1300 ° C to avoid an excessive magnification of the austenitic grain and the plastic deformation (rolling for example) must preferably end above Ab 3 to prevent the ferrito-pearlitic transformation from starting.
  • the cooling to a temperature close to M s carried out at a cooling rate greater than 0.3 ° C / s, can be carried out, for example, by controlled watering with water.
  • the slow passage in the vicinity of M s can then be obtained by air cooling which can also serve as cooling to room temperature.
  • cooling to room temperature which follows the slow passage in the vicinity of M s , can advantageously be achieved by cooling with water in order to limit as much as possible the self-income of the structure obtained.
  • cooling to the vicinity of M s , the slow passage in the vicinity of M s and cooling to the ambient can be carried out directly by air cooling. This is particularly the case, when the product is a sheet of thickness at least equal to 30 mm. It is also possible to treat, by air cooling, sheets of thickness less than 30 mm, by stacking several sheets so as to form a packet of thickness greater than 30 mm.
  • the product When the heat treatment is carried out after shaping by hot plastic deformation and return to ambient temperature of the product, the product must be austenitized by reheating above Ac 3 in order to obtain a complete austenitization, then it can be cooled either in the same way as when the heat treatment is carried out in the hot forming, or by any suitable means to carry out the recommended thermal cycle.
  • the titanium of steel C was introduced in accordance with the invention.
  • the steels according to the invention have elongations uniforms at least 2.5 times higher than those of steels according to the art prior.
  • These parts are in particular sheets of thickness greater than 8 mm.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (13)

  1. Stahl, dadurch gekennzeichnet, dass er die folgende chemische Zusammensetzung in Gewichtsprozent hat: 0,15 % ≤ C ≤ 0,303 % 0 % ≤ Si ≤ 3 % 0 % ≤ Al ≤ 3 % 0,1 % ≤ Mn ≤ 4,5 % 0 % ≤ Ni ≤ 9 % 0 % ≤ Cr ≤ 6 % 0 % ≤ Mo + W/2 ≤ 3 % 0 % ≤ V ≤ 0,5 % 0 % ≤ Nb ≤ 0,5 % 0 % ≤ Zr ≤ 0,5 % N ≤ 0,3 %
    gegebenenfalls 0,0005 % bis 0,005 % Bor,
    gegebenenfalls 0,005 % bis 0,1 % Titan,
    gegebenenfalls mindestens eines der Elemente Ca, Se, Te, Bi und Pb
       mit Gehalten kleiner als 0,2 %,
    der Rest besteht aus Eisen und Verunreinigungen aus der Verarbeitung,
    wobei die chemische Zusammensetzung außerdem den folgenden Beziehungen genügt: 1 % ≤ Si + Al ≤ 3 % und 4,6x(% C) + 1,05x(% Mn) + 0,54x(% Ni) +0,66x(% Mo + % W/2) + 0,5x(% Cr) + K ≥ 3,8 mit
    K = 0,5, wenn der Stahl Bor enthält,
    K = 0, wenn der Stahl kein Bor enthält.
  2. Stahl nach Anspruch 1, dadurch gekennzeichnet, dass 0,005 % ≤ Ti ≤ 0,1 % 0,01 % ≤ Al ≤ 0,5 % 0,003 % ≤ N < 0,02 % und dadurch, dass im festen Zustand die Anzahl der Aushärtungen an Titannitriden mit einer Teilchengröße über 0,1 µm auf einer Fläche von 1 mm2 eines Mikroschliffes kleiner als das Vierfache des Gesamtgehalts an in Form von Nitriden ausgeschiedenem Titan ist, ausgedrückt in Tausendstel Gewichtsprozent.
  3. Stahl nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass 0,5 % ≤ Cr ≤ 3 % 0,1 % ≤ Mo + W/2 ≤ 2 % Mn ≤ 2 %
  4. Stahl nach Anspruch 1, Anspruch 2 oder Anspruch 3, dadurch gekennzeichnet, dass 1,5 % ≤ Si + Al ≤ 2,5 %
  5. Stahl nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass 0,2 % ≤ C ≤ 0,3 %
  6. Stahl nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass er die folgende chemische Zusammensetzung in Gewichtsprozent hat: 0,20 % ≤ C ≤ 0,24 % 0 % ≤ Si ≤ 2,5 % 0 % ≤ Al ≤ 2,5 % 1,2 % ≤ Mn ≤ 1,7 % 1,5 % ≤ Ni ≤ 2,5 % 0,5 % ≤ Cr ≤ 1,5 % 0,1 % ≤ Mo + W/2 ≤ 0,5 % wobei die chemische Zusammensetzung außerdem den folgenden Beziehungen genügt: 1,5 % ≤ Si + Al ≤ 2,5 % und 4,6x(% C) + 1,05x(% Mn) + 0,54x(% Ni) +0,66x(% Mo + % W/2) + 0,5x(% Cr) + K ≥ 3,8 mit
    K = 0,5, wenn der Stahl Bor enthält,
    K = 0, wenn der Stahl kein Bor enthält.
  7. Verfahren zur Herstellung eines Teils aus Stahl mit hoher Festigkeit und hoher Duktilität, dadurch gekennzeichnet, dass:
    man einen Stahl nach einem der Ansprüche 1 bis 6 erschmilzt,
    man den Stahl gießt und ihn in Form eines Halbfabrikats verfestigen lässt,
    man das Halbfabrikat durch plastische Warmverformung in seine Form bringt, um ein Teil aus Stahl zu erhalten,
    man das Teil durch Erhitzen über Ac3 °C austenitisiert, es dann bis auf die Umgebungstemperatur in der Weise abkühlt, dass die Abkühlungsgeschwindigkeit zwischen der Austenitiserungstemperatur und Ms + 150 °C größer als 0,3 °C/s ist, dass die Verweilzeit zwischen Ms + 150 °C und Ms - 50 °C zwischen 5 und 90 Minuten liegt und dass die Abkühlgeschwindigkeit bis zur Umgebungstemperatur größer als 0,02 °C/s ist.
  8. Verfahren zur Herstellung eines Teils aus Stahl hoher Festigkeit und hoher Duktilität, dadurch gekennzeichnet, dass:
    man einen Stahl nach einem der Ansprüche 1 bis 6 erschmilzt,
    man den Stahl gießt und ihn in Form eines Halbfabrikats verfestigen lässt,
    man das Halbfabrikat durch plastische Warmverformung in seine Form bringt, um ein Teil aus Stahl zu erhalten,
    man das Stück durch Erhitzen über Ac3 °C austenitisiert, es dann bis auf die Umgebungstemperatur in der Weise abkühlt, dass die Abkühlungsgeschwindigkeit zwischen der Austenitiserungstemperatur und Ms + 150 °C größer als 0,3 °C/s ist, dass die Verweilzeit zwischen Ms + 150 °C und Ms - 50 °C zwischen 5 und 90 Minuten liegt und dass die Abkühlgeschwindigkeit bis zur Umgebungstemperatur größer als 0,02 °C/s ist.
  9. Verfahren nach Anspruch 7 oder Anspruch 8, dadurch gekennzeichnet, dass man zum Abkühlen des Teils von der Austenitisierungstemperatur auf die Umgebungstemperatur das Teil an der Luft abkühlen lässt.
  10. Teil aus Stahl nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass sein Mikrogefüge aus Bainit und/oder Martensit und 5 % bis 10 % Austenit besteht, seine Zugfestigkeit über 1200 MPa liegt und seine durch gleichförmige Dehnung gemessene Duktilität größer als 5 % ist.
  11. Teil aus Stahl nach Anspruch 10, dadurch gekennzeichnet, dass sein Gefüge mindestens 30 % Bainit enthält.
  12. Teil nach Anspruch 10 oder 11, dadurch gekennzeichnet, dass es sich um ein Blech mit einer Stärke größer als 8 mm handelt.
  13. Benutzung eines Stahls nach einem der Ansprüche 1 bis 6 für die Herstellung von Ausrüstungen hoher Verschleißfestigkeit für den Bergbau oder für Tiefbauarbeiten oder für die Herstellung von Teilen des Stahlbaus oder Kesselbaus.
EP96400061A 1995-01-31 1996-01-11 Stahl mit hoher Dehnbarkeit, Verfahren zur Herstellung und Verwendung Expired - Lifetime EP0725156B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9501079A FR2729974B1 (fr) 1995-01-31 1995-01-31 Acier a haute ductilite, procede de fabrication et utilisation
FR9501079 1995-01-31

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EP0725156A1 EP0725156A1 (de) 1996-08-07
EP0725156B1 true EP0725156B1 (de) 2001-07-18

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US (1) US5695576A (de)
EP (1) EP0725156B1 (de)
JP (1) JPH08239738A (de)
DE (1) DE69613868T2 (de)
FR (1) FR2729974B1 (de)

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CN112359284A (zh) * 2020-11-04 2021-02-12 南阳汉冶特钢有限公司 一种高强度低温韧性耐磨钢板hy550nme及其生产方法
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CN114959422A (zh) * 2022-06-06 2022-08-30 山东冀凯装备制造有限公司 一种高强度低合金贝氏体铸钢的制备方法

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US5695576A (en) 1997-12-09
FR2729974A1 (fr) 1996-08-02
DE69613868D1 (de) 2001-08-23
EP0725156A1 (de) 1996-08-07
DE69613868T2 (de) 2001-11-29
FR2729974B1 (fr) 1997-02-28
JPH08239738A (ja) 1996-09-17

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