EP2159296B1 - Gehärteter und getemperter stahl und verfahren zur herstellung von teilen aus dem stahl - Google Patents

Gehärteter und getemperter stahl und verfahren zur herstellung von teilen aus dem stahl Download PDF

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EP2159296B1
EP2159296B1 EP07730464.0A EP07730464A EP2159296B1 EP 2159296 B1 EP2159296 B1 EP 2159296B1 EP 07730464 A EP07730464 A EP 07730464A EP 2159296 B1 EP2159296 B1 EP 2159296B1
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Prior art keywords
steel
weight
quench
obtaining
quench hardened
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French (fr)
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EP2159296A1 (de
EP2159296A4 (de
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Zurine Idoyaga Olano
Jacinto José Albarran Sanz
Maria Carmen Montero Pascual
Roberto Elvira Eguizabal
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Sidenor Investigacion y Desarrollo SA
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Sidenor Investigacion y Desarrollo SA
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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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C1/00—Refining of pig-iron; Cast iron
    • C21C1/02—Dephosphorising or desulfurising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/064—Dephosphorising; Desulfurising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium

Definitions

  • the present invention relates to a quench hardened and tempered steel and to a method for obtaining parts of said steel, having an application in the field of the steel industry, allowing its use for metal structures in the construction sector, said parts being especially suitable in the shipbuilding industry, for example for manufacturing chains for vessels and anchor line accessories.
  • the invention allows obtaining a quench hardened and tempered steel, from a chemical composition and by means of a metallurgical process, having high mechanical strength and at the same time high toughness at low temperature, in addition to having optimal weldability.
  • quench hardened and tempered steels are used for constructing metal structures and for manufacturing mechanical parts and elements of responsibility, i.e., they are subjected to loads during their work situation, and for which the slightest possibility of failure of said parts during their useful life is not admissible.
  • the essential mechanical characteristics which this type of part has to have are high mechanical strength, high toughness and an optimal ratio between the elastic limit and the mechanical strength. Furthermore, high fatigue strength and elongation are also required.
  • the high tensile strength values of quench hardened and tempered steels vary between 700 N/mm 2 and 1700 N/mm 2 , and are achieved with carbon contents by weight ranging between 0.25% and 0.60%. Furthermore, to improve other properties, the addition of variable amounts of alloying elements, such as for example Mn, Cr, Ni, Mo and V, is known.
  • the increase of the carbon content in a steel causes on one hand an increase in the tensile strength and in the cold brittleness of said steel, whereas on the other hand it causes a reduction of its toughness and ductility.
  • the toughness is the capacity of a material to absorb energy without causing fissures, being determined as an impact strength, i.e., the resistance offered by a material to the propagation of a crack, or the energy absorption capacity of the material without causing fissures.
  • quench hardened and tempered steels include the shipbuilding industry, specifically in the manufacture of chains and other accessory elements and devices for anchor lines, as well as the gas liquefaction and transport industries.
  • these properties must be maintained even at low temperatures, of an order of magnitude of 20oC below zero or even lower temperatures, considering the service conditions of these elements and parts given their field of application.
  • quench hardened and tempered steels have a good response to processes involved in the stages of manufacturing, installing and assembling these parts, such as for example hot forming and welding processes.
  • Quench hardening is a heat treatment the objective of which is to harden and increase the strength of the steels at the expense of decreasing the ductility and the resilience.
  • the resilience is the amount of energy which a material can absorb in the elastic field, i.e., before the plastic deformation when it is subjected to a load starts.
  • the resilience corresponds to the area which is under the stress-strain diagram of the tensile test of a material, between a zero deformation value and the deformation value corresponding to the creep stress, being an indicator of the brittleness of the material.
  • the quench hardening heat treatment consists of heating a steel to a temperature above its transformation point (Ac), also called upper critical temperature or transformation temperature, which depends on the chemical composition of the steel and can be for example between 800oC and 950oC, all of this for the purpose of achieving an austenitic crystal structure ( ⁇ ).
  • a rapid cooling is then performed at a rate greater than the critical one for the purpose of achieving a martensitic crystal structure, or in any case if the cooling is not rapid enough achieving a bainitic crystal structure, which provide the steels with high strengths.
  • the quench hardening is a transformation of austenite ( ⁇ ) into martensite and/or bainite with high strength.
  • the cooling rate depends on the dimensions of the part or element of steel to be quench hardened, water, oil, air or refrigerated means, such as for example a refrigerated chamber, usually being used to perform said cooling.
  • the factors affecting the quench hardening are the chemical composition of the steel, considering both the percentage of carbon and of alloying elements, the temperature and the heating time and the cooling rate.
  • the quench hardening treatment it is highly usual to perform a tempering heat treatment on the steel for the purpose of attenuating the effects and mechanical properties resulting from the quench hardening, allowing maintaining to a great extent the required strength and hardness values while at the same time the toughness and elasticity of the steel are increased.
  • Steels with an optimal combination of mechanical strength, elongation and elastic limit are thus obtained, steels being obtained with an elastic limit value of up to 75% the breaking load value.
  • the elastic limit is greater than the elastic limit of steels in which normalizing and annealing heat treatments have been performed.
  • Tempering is a heat treatment consisting of heating to a temperature lower than the starting temperature of the austenitic transformation, which usually occurs between 450oC and 600oC.
  • the carbon contained in the martensite in forced solution, precipitates as carbides and a transformation of the retained austenite ( ⁇ ) occurs, whereas the martensite is transformed into extremely small cementite (Fe 3 C) particles dispersed in a ferrite ( ⁇ ) matrix, whereby the stresses created in the abrupt cooling performed in the quench hardening treatment are eliminated.
  • martempering is a particular case of the previously described quench hardening and tempering treatment, in which the quench hardening is stopped before the martensitic transformation takes place, for the purpose of homogenizing the temperature of a part of steel, prior to continuing the cooling so that martensite is formed, then proceeding as in the case of a tempering treatment.
  • Korean patent number KR 100320959-B describes a method for obtaining a steel with high toughness at very low temperatures with high Mn content, which by weight is between 16% and 22%.
  • Japanese patent number JP 2000256783 describes a steel with high and toughness, with resistance to corrosion under stress, as well as to the method for manufacturing it, in which the elastic limit of said steel exceeds 960 N/mm 2 (140 ksi), with contents by weight of C between 0.20% and 0.35%, of Cr between 0.20% and 0.70%, of Mo between 0.10% and 0.50%, and of V between 0.10% and 0.30%.
  • European patent application EP0225425A2 describes a low alloy steel used as a material for steam turbines or the like, and more specifically to nickel-chrome-molybdenum steel.
  • patent application US2002/0124716A1 discloses a method for producing tubes for heavy guns in the caliber range of 105 mm and the greater, made from heat-treatable steel.
  • the present invention relates to a quench hardened and tempered steel and to a method for obtaining parts of said steel, in which as a result of various investigations an optimal combination of two opposing mechanical properties, high tensile strength, with strength values of at least 1200 N/mm 2 , and high toughness at low temperature, with KV resilience values at -20°C of at least 60 J.
  • the invention allows obtaining a quench hardened and tempered steel, from a novel chemical composition and a certain metallurgical process, having high mechanical strength and at the same time high toughness at low temperature, in addition to having optimal weldability, which is important, for example, in the specific case of manufacturing chains for the shipbuilding industry.
  • the heat treatment performed in the steel significantly affects the mechanical characteristics of the steel finally obtained, i.e., the initial chemical composition is subjected to a certain quench hardening and tempering method, which must necessarily be performed in specific time and temperature conditions.
  • the inventors have verified a synergic effect between a novel combination of chemical elements and a method for obtaining said steel, which contemplates a specific heat treatment, achieving a quench hardened and tempered steel with high strength and toughness, in addition to a good suitability for welding and shaping processes.
  • NiCrMoV alloyed steel comprising the following chemical composition in percentage by weight:
  • alloying elements are used in alloyed steels to improve the tensile strength, the tempering resistance, the toughness or other characteristics, but not with the indicated concentrations by weight, with the proposed combination of elements, nor for obtaining the previously described properties which allow their use in the mentioned applications.
  • Manganese increases the quench hardenability and reduces the transformation temperature, which allows obtaining a fine grain crystal structure, allowing at the same time increasing the strength and improving the toughness.
  • chromium allows a marked shift of the curves of the TTT, Temperature-Time-Transformation, diagrams towards the right, whereby it allows increasing to a great extent the quench hardenability in a less expensive manner than other elements, as in the case of steels of the state of the art.
  • Nickel is a moderate agent favoring the quench hardenability and which allows reducing the tendency to cracking during the quench hardening.
  • the indicated nickel contents allow obtaining a fine grain, achieving higher impact strength, mainly at low temperatures.
  • Molybdenum has a strong effect favoring the quench hardenability, being in turn a strong former of carbides, which provide a considerable secondary hardening effect during the tempering.
  • vanadium is a microalloying element which causes an intense hardening by precipitation and which, when it remains in solid solution, highly increases the quench hardenability, furthermore showing a strong secondary hardening effect during the tempering at high temperature, of an order of magnitude greater than 575°C.
  • the steel proposed by the invention can additionally comprise at least one of the following elements or a combination thereof, with a percentage by weight:
  • the steel of the invention comprises any or several of the following elements, with a percentage by weight:
  • the presence of phosphorus and sulfur is generally detrimental for the applications requiring toughness at low temperature, since they reduce the elongation and the strength of the steel, an attempt being made to eliminate these elements in the manufacturing processes.
  • the general recommendation for ordinary steels of the state of the art is that the S content, as well as the P content does not exceed 0.060%, and 0.030% in the case of quality steels.
  • a preferred composition of the steel proposed by the invention comprises, in percentage by weight:
  • the steel can additionally comprise at least one of the following elements, or a combination thereof, by weight:
  • This entire method for manufacturing steel allows achieving low levels of sulfur levels, below 0.010% by weight, and phosphorus, below 0.015% by weight, in addition to a low inclusion level.
  • TTT Temporal-Time-Transformation
  • the invention contemplates performing a method by which said part of steel can be obtained.
  • the method for obtaining parts of said steel comprises a quench hardening process which is performed with an austenization at a temperature greater than 800°C, followed by a subsequent cooling, for example in water.
  • the method then comprises a tempering process which is carried out at a temperature greater than 550°C for about 2 hours, thus achieving the adjustment of the hardness and toughness of the material, in addition to preventing decreases of resilience, which are associated with the brittleness phenomenon of tempering.
  • the method for obtaining parts of steel comprises the following steps:
  • Table 1 shows the chemical compositions in percentage by weight: Table 1 C Mn Si P S Cr Ni Mo V Cu Al A .17 .51 .29 .008 .006 1.00 3.30 .25 .014 .30 .032 B .27 .24 .12 .006 .004 1.80 1.70 .59 .130 .14 .005 C .20 .81 .34 .009 .007 1.53 2.72 .38 .004 .23 .031 D .26 1.45 .18 .015 .003 1.28 1.06 .69 .130 .24 .012 E .27 .42 .25 .011 .005 2.03 2.04 .36 .010 .22 .007 F .24 .64 .24 .009 .005
  • steels A, B, C, D and E do not reach a strength of 1200 N/mm 2 , maintaining a KV resilience at -20°C of 60 J.
  • Steels A and C have low carbon and vanadium contents, such that with the toughness demanded at low temperature, only strength values of about 1100 N/mm 2 are achieved.
  • steels B, D and E despite having a greater carbon content, do not achieve the desired levels of strength, since the combination of alloying elements is not the suitable one for reaching the demanded mechanical characteristics.
  • Figure 3 shows the KV resilience values at -20°C obtained with a strength of 1200 N/mm 2 for the different steels A-F.
  • steel F having a chemical composition within the limits object of the invention, i.e., it is the steel proposed by the invention, it has been verified that after being subjected to a quench hardening and tempering treatment it reaches the required mechanical characteristics and furthermore has no welding problem.

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

Claims (6)

  1. Abschreckgehärteter und vergüteter Stahl mit hoher Zugfestigkeit und hoher Kerbschlagfestigkeit, umfassend die folgenden Elemente mit einem Gewichtsprozentsatz:
    0,22% ≤ C ≤ 0,30%
    0,40% ≤ Mn ≤ 1,0%
    1,00% ≤ Cr ≤ 2,50%
    1,80% ≤ Ni ≤ 4,0%
    0,30% ≤ Mo ≤ 0,90%
    0,001% ≤ V ≤ 0,50%
    0,050% ≤ Si ≤ 0,50%
    P ≤ 0,015%
    S ≤ 0,010%
    0,005% ≤ Al ≤ 0,050%,
    dadurch gekennzeichnet, dass er zusätzlich mindestens eines der folgenden Elemente mit einem Gewichtsprozentsatz umfasst:
    Cu ≤ 0,350%
    0,005% ≤ Ti ≤ 0,050%
    0,004% ≤ N ≤ 0,020%
    Ca ≤ 0,005%
    Bi ≤ 0,15%
    Pb ≤ 0,20%
    Te ≤ 0,02%
    Se ≤ 0,04% und als Rest Eisen und Verunreinigungen.
  2. Abschreckgehärteter und vergüteter Stahl nach Anspruch 1, dadurch gekennzeichnet, dass er die folgenden Elemente mit einem Gewichtsprozentsatz umfasst:
    0,23% ≤ C ≤ 0,28%
    0,50% ≤ Mn ≤ 0,90%
    1,20% ≤ Cr ≤ 2,0%
    2,0% ≤ Ni ≤ 3,50%
    0,30% ≤ Mo ≤ 0,70%
    0,001% ≤ V ≤ 0,20%.
  3. Abschreckgehärteter und vergüteter Stahl nach einem der Ansprüche 1 und 2, dadurch gekennzeichnet, dass er mindestens eines der folgenden Elemente mit einem Gewichtsprozentsatz umfasst:
    0,10% ≤ Si ≤ 0,35%
    P ≤ 0,015%
    S ≤ 0,010%
    Cu ≤ 0,350%
    0,005% ≤ Al ≤ 0,035%
    0,005% ≤ Ti ≤ 0,050%
    0,004% ≤ N ≤ 0,020%.
  4. Abschreckgehärteter und vergüteter Stahl nach einem der vorangegangenen Ansprüche, dadurch gekennzeichnet, dass er eine mechanische Zugfestigkeit größer als oder gleich ungefähr 1200 N/mm2 und eine KV-Verformungsarbeit bei -20°C größer oder gleich ungefähr 60 J aufweist.
  5. Verfahren zum Erhalten von Teilen eines abschreckgehärteten und vergüteten Stahls nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass es umfasst, den Stahl zu erhalten mittels der folgenden Schritte:
    - Kontrollieren der Ausgangsmaterialien des Ofens, d.h. von Schrott und insbesondere Koks und Kalk,
    - Ausführen einer Oxidationsperiode in einem Elektroofen für die Entphosphorung des Stahls vor der Schaumschlacke,
    - Abschlacken der Schaumschlacke bis zu einem Vorhandensein von Phosphor von weniger als 0,007% Gew.-%,
    - Kippen bei Standard-Temperatur und -Teilen pro Million (ppm) von Sauerstoff, wobei sichergestellt wird, dass keine Schlacke aus dem Ofen in die Gießpfanne übertritt,
    - Desoxidieren mit Al, um hochgradig flüssige weiße Schlacke mit einer Kalk-Spat-Base zu erhalten,
    - Kontrollieren der Ausgangsmaterialien für das Frischen,
    - Ausführen von zwei Vakuums mit einer intermediären H-Probe, wobei die Vakuumzeit angesehen wird als diejenige, die unter 2 mbar liegt,
    - Beenden des zweiten Vakuums bei einer Temperatur, die erlaubt, ein Schlackeneinschluss-Dekantierverfahren danach auszuführen und die Schmelze mit Argon zu rühren, um die Schlacke aufzubrechen, und ohne ein Ausführen von Zugaben oder Erwärmen und
    - Abstechen mit einem speziellen Schutz des Stroms.
  6. Verfahren zum Erhalten von Teilen von abschreckgehärtetem und vergütetem Stahl nach Anspruch 5, dadurch gekennzeichnet, dass es nach Erhalten des Stahls die folgenden Schritte umfasst:
    - Herstellen eines Teils aus dem Stahl,
    - Ausführen einer der Abschreckhärtung dienenden Wärmebehandlung, die mit einer Austenitisierung bei einer Temperatur über 800°C ausgeführt wird, in dem Teil, gefolgt von einem nachfolgenden Abkühlen, und
    - Ausführen einer Vergütungsbehandlung, die bei einer Temperatur über 550°C für ungefähr 2 Stunden ausgeführt wird, in dem Teil.
EP07730464.0A 2007-04-13 2007-04-13 Gehärteter und getemperter stahl und verfahren zur herstellung von teilen aus dem stahl Active EP2159296B1 (de)

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PCT/ES2007/000224 WO2008125700A1 (es) 2007-04-13 2007-04-13 Acero de temple y revenido y procedimiento para obtener piezas de dicho acero

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EP2159296A1 EP2159296A1 (de) 2010-03-03
EP2159296A4 EP2159296A4 (de) 2014-09-10
EP2159296B1 true EP2159296B1 (de) 2016-03-16

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EP (1) EP2159296B1 (de)
BR (1) BRPI0721566A2 (de)
ES (1) ES2576453T3 (de)
WO (1) WO2008125700A1 (de)

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US10428410B2 (en) 2010-10-29 2019-10-01 Carnegie Mellon University High toughness secondary hardening steels with nickel as a primary strength and toughening agent
WO2012058404A1 (en) * 2010-10-29 2012-05-03 Carnegie Mellon University High toughness secondary hardening steel
RU2530095C1 (ru) * 2013-07-12 2014-10-10 Российская Федерация, От Имени Которой Выступает Министерство Промышленности И Торговли Российской Федерации Высокопрочная сталь с повышенной деформируемостью после закалки
EP3168319B1 (de) * 2014-07-08 2020-12-16 Sidenor Investigación y Desarrollo, S.A. Mikrolegierter stahl zum warmformen von hochbeständigen teilen mit hoher streckgrenze
KR102113045B1 (ko) * 2016-02-19 2020-05-20 닛폰세이테츠 가부시키가이샤 강
CN108603260B (zh) * 2016-02-19 2021-08-13 日本制铁株式会社 钢
CN109093099A (zh) * 2018-09-30 2018-12-28 宁波市镇海甬鼎紧固件制造有限公司 一种耐低温高强度螺帽及其生产方法
CN111500927A (zh) * 2020-04-25 2020-08-07 浙江普兰卡钎具股份有限公司 一种钎头壳体的钢材及其制备方法
CN114941104B (zh) * 2022-05-09 2023-08-18 河南中原特钢装备制造有限公司 超高强度30CrNi2MoV锻制钻具材料的热处理工艺

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3254991A (en) * 1962-06-29 1966-06-07 Republic Steel Corp Steel alloy and method of making same
JPS54145318A (en) * 1978-05-08 1979-11-13 Toshiba Corp Low alloy steel of high toughness
JPH0617540B2 (ja) * 1984-02-13 1994-03-09 キヤタピラ− トラクタ− カンパニ− 窒化鋼製品
JPS62109949A (ja) * 1985-11-06 1987-05-21 Kobe Steel Ltd 耐応力腐食割れ性に優れたＮｉＣｒＭｏ鋼
KR100320959B1 (ko) 1996-12-30 2002-06-20 전선기 극저온충격특성이우수한고망간강및그제조방법
KR100325714B1 (ko) 1997-12-24 2002-06-29 이구택 저온인성이우수한베이나이트계강재의제조방법
JP2000256783A (ja) 1999-03-11 2000-09-19 Sumitomo Metal Ind Ltd 靭性と耐硫化物応力腐食割れ性に優れる高強度油井用鋼およびその製造方法
DE10111304C2 (de) * 2001-03-09 2003-03-20 Buderus Edelstahlwerke Ag Verfahren zur Herstellung von Rohren für schwere Geschütze
US7537727B2 (en) * 2003-01-24 2009-05-26 Ellwood National Forge Company Eglin steel—a low alloy high strength composition
WO2005121384A2 (en) * 2003-12-04 2005-12-22 Chamberlian Manufacturing Corporation High strength steel alloy
KR100536660B1 (ko) 2003-12-18 2005-12-14 삼화강봉주식회사 저온충격 특성이 우수한 냉간압조용 강선과 그 제조 방법

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