EP3168312B1 - Edelbaustahl mit bainitischem gefüge, daraus hergestelltes schmiedeteil und verfahren zur herstellung eines schmiedeteils - Google Patents

Edelbaustahl mit bainitischem gefüge, daraus hergestelltes schmiedeteil und verfahren zur herstellung eines schmiedeteils Download PDF

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Publication number
EP3168312B1
EP3168312B1 EP15194741.3A EP15194741A EP3168312B1 EP 3168312 B1 EP3168312 B1 EP 3168312B1 EP 15194741 A EP15194741 A EP 15194741A EP 3168312 B1 EP3168312 B1 EP 3168312B1
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Prior art keywords
content
forging
engineering steel
steel
steel according
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EP15194741.3A
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German (de)
English (en)
French (fr)
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EP3168312A1 (de
Inventor
Ulrich Reichel
Till SCHNEIDERS
Frank van Soest
Hans-Günter KRULL
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Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
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Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
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Priority to PL15194741T priority Critical patent/PL3168312T3/pl
Application filed by Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG filed Critical Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
Priority to PT15194741T priority patent/PT3168312T/pt
Priority to EP15194741.3A priority patent/EP3168312B1/de
Priority to ES15194741T priority patent/ES2733805T3/es
Priority to DK15194741.3T priority patent/DK3168312T3/da
Priority to CA3005378A priority patent/CA3005378C/en
Priority to RU2018121935A priority patent/RU2703085C1/ru
Priority to JP2018521262A priority patent/JP6616501B2/ja
Priority to KR1020187014749A priority patent/KR102178736B1/ko
Priority to US15/773,745 priority patent/US20180327873A1/en
Priority to CN201680069274.3A priority patent/CN108474049B/zh
Priority to PCT/EP2016/077761 priority patent/WO2017085072A1/de
Publication of EP3168312A1 publication Critical patent/EP3168312A1/de
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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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a structural steel with high strength and a structure which consists of at least 80 vol .-% of bainite.
  • the invention relates to a forged part, which is made of such a structural engineering steel.
  • the invention relates to a method for producing a forged component from a noble structural steel according to the invention.
  • the article states that promising materials with a bainitic structure have been found to combine good strength and toughness properties without the need for additional heat treatment resulting in tensile strengths greater than 1200 MPa, a yield strength of more than 850 MPa and an elongation at break of more than 10% at a impact energy of 27 J at room temperature.
  • the article contains a steel having (in wt%) 0.18% C, 1.53% Si, 1.47% Mn 0.007% S, 1.30% Cr , 0.07% Mo, 0.0020% B, 0.027% Nb, 0.026% Ti, 0.0080% N, balance iron and unavoidable impurities and a steel with 0.22% C, 1.47% Si, 1, 50% Mn, 0.006% S, 1.31% Cr, 0.09% Mo, 0.0025% B, 0.035% Nb, 0.026% Ti, 0.0108% N, balance iron and unavoidable impurities presented.
  • the forging is subjected to a heat treatment comprising cooling at a cooling rate Vr of more than 0.5 ° C / sec from a temperature at which the steel is austenitic to a temperature Tm of between Ms +100 ° C and Ms -20 ° C is.
  • the forging is then held for at least two minutes at a temperature which is between the temperature Tm and a temperature Tf, for which Tf> Tm -100 ° C.
  • a steel component having a substantially bainitic structure comprising at least 15% lower bainite and preferably at least 20% bainite formed between Tm and Tf.
  • the steel may also contain 0.005 - 0.03% Ti, 0.005 - 0.06% Nb, 0.0005 - 0.01% B, ⁇ 0.3% V, ⁇ 0.35% Cu, 0.005 - 0, 06% Al, 0.005-0.1% S, ⁇ 0.006% Ca, ⁇ 0.03% Te, ⁇ 0.05% Se, ⁇ 0.05% Bi, ⁇ 0.1% Pb, with the remainder of the Steel consists of iron and unavoidable impurities.
  • the contents of V and N, of S, Al, Nb, Ti and Mn, Cr, Ni, Cu, Mo are matched to each other according to special requirements.
  • the composite steel should be particularly suitable for the production of drop forged parts, especially chassis parts, with high strength and high toughness without final compensation.
  • the object of the invention to provide a steel which has a high strength, without the need to complete complex heat treatment processes, the has a low tendency to delay and is suitable as such in particular for the forging production of forgings with over its length large cross-sectional changes.
  • a forged part should be specified, which has an optimal combination of properties without complex heat treatment process.
  • the invention has achieved the object mentioned above by the structural steel specified in claim 1.
  • the solution according to the invention of the abovementioned object consists in that such a steel component is produced from a steel according to the invention.
  • the invention has finally achieved the abovementioned object in that during the production of a forging component, the working steps mentioned in claim 12 are run through.
  • a noble structural steel according to the invention has a yield strength of at least 750 MPa and a tensile strength of at least 950 MPa and at least 80% by volume bainitic structure, the remaining 20% by volume of the microstructure being retained austenite, ferrite, perlite or martensite.
  • the steel according to the invention is characterized by a high elongation at break A of at least 10%, in particular at least 12%, whereby it is shown in practice that steels according to the invention regularly achieve an elongation at break A of at least 15%.
  • the engineering structural steel consists of (in% by weight) up to 0.25% C, up to 1.5% Si, in particular up to 1% Si or up to 0.45% Si, 0.20-2, 00% Mn, up to 4.00% Cr, 0.7-3.0% Mo, 0.004-0.020% N, up to 0.40% S, 0.001-0.035% Al, 0.0005-0.0025% B, up to 0.015% Nb, up to 0.01% Ti, up to 0.50% V, up to 1.5% Ni, up to 2.0% Cu and balance iron and unavoidable impurities, the Al Content% Al, the Nb content% Nb, the Ti content% Ti, the V content% V and the N content% N of the noble structural steel each satisfy the following condition: % ⁇ al / 27 + % ⁇ Nb / 45 + % ⁇ Ti / 48 + % ⁇ V / 25 > % ⁇ N / 3.75
  • the unavoidable impurities due to production include all elements which are present in terms of alloying inefficiencies with regard to the properties of interest here and which enter the steel on the basis of the respectively selected melting route or the respective selected starting material (scrap).
  • the unavoidable impurities also include levels of P of up to 0.0035% by weight.
  • a steel according to the invention and the forging components produced therefrom are distinguished by a particularly uniform distribution of properties, even if locally greatly differing cooling conditions prevail as a result of changing component dimensions when cooling from forging heat through the forged part volume.
  • This insensitivity to the cooling conditions is achieved by the inventive structural steel a homogeneous, largely exclusively bainitic Structure with low variance of hardness possesses. At the same time, this homogeneous microstructure contains low residual stresses, which has a positive effect on the distortion behavior.
  • steel according to the invention is particularly suitable for the production of forged components in which sections of very different volumes and diameters abut one another.
  • forgings for whose forging technology production of the steel according to the invention is particularly suitable, are crankshafts, connecting rods and the like, which are intended in particular for internal combustion engines.
  • steel parts according to the invention in the area of the undercarriage and the suspension can be manufactured reliably with very different cross-sections without much subsequent reworking by grinding while maintaining the predetermined strength properties.
  • a particularly wide window can be used for bainitizing a noble structural steel according to the invention if the engineering steel according to the invention is continuously cooled from forging heat.
  • the alloy of the structural steel according to the invention is chosen so that in the course of cooling do not affect its properties affecting amounts of martensite or ferrite or perlite in the structure.
  • the structural steel according to the invention is thus characterized by having a predominantly, ie at least 80% by volume, bainic structure, wherein the content of non-bainitic structural constituents in steels according to the invention is typically minimized to such an extent that the steel according to the invention is completely complete in the technical sense possesses bainitic structure.
  • the noble steel steel according to the invention largely independent of the cooling rate in bainite an almost constant hardness.
  • the constant hardness is a consequence of the almost complete transformation of the former austenite into bainite, preferably into a bainitic transformation stage.
  • a noble structural steel according to the invention has good elongation and toughness properties despite its maximized strength.
  • the low C content also contributes to the acceleration of the bainite transformation in a steel according to the invention, so that the formation of undesired structural constituents is avoided.
  • a certain amount of carbon in the engineering steel according to the invention can also contribute to the strength.
  • a content of at least 0.09 wt .-% C is provided in the steel.
  • An optimized effect of the presence of C in the steel according to the invention is thus achieved by setting the C content to 0.09-0.25% by weight.
  • the Si content of a steel according to the invention is limited to 1.5% by weight, in particular 1% by weight or 0.75% by weight, in order to allow the bainite transformation to proceed as early as possible. In order to achieve this effect particularly reliably, the Si content can also be limited to at most 0.45 wt .-%.
  • Mo is present in the noble structural steel according to the invention in contents of 0.6-3.0% by weight, in order to delay the transformation of the microstructure into ferrite or perlite. This effect occurs in particular when at least 0.7 wt .-%, in particular more than 0.70 wt .-% Mo, are present in the steel. At contents of more than 3.0% by weight, no economically viable further increase occurs in the steel according to the invention the positive effect of Mo more. In addition, above 3.0 wt% Mo, there is a risk of forming a molybdenum-rich carbide phase which may adversely affect the toughness properties. Optimum effects of Mo in the steel of the present invention can be expected when the Mo content is at least 0.7 wt%. Mo contents of not more than 2.0% by weight have proved to be particularly effective.
  • Manganese is present at levels of 0.20-2.00% by weight in the steel of the present invention to adjust the tensile strength and yield strength.
  • a minimum content of 0.20% by weight of Mn is required in order to increase the strength. If this effect is to be achieved particularly reliably, then an Mn content of at least 0.35 wt .-% can be provided. Too high Mn contents lead to the delay of the bainite transformation and thus to a predominantly martensitic transformation. Therefore, the Mn content is limited to at most 2.00 wt%, especially 1.5 wt%. Negative influences of the presence of Mn can be avoided particularly reliably by limiting the Mn content in the steel according to the invention to a maximum of 1.1% by weight.
  • the sulfur content of a steel according to the invention can be up to 0.4 wt .-%, in particular max. 0.1% by weight or max. 0.05 wt .-% to assist the machinability of the steel.
  • the fine-tuning with regard to the mechanical properties and the microstructure of a structural steel according to the invention is carried out according to the inventive alloy concept via a combined microalloying of the elements boron in contents of 0.0005-0.0025 wt.%, Nitrogen in contents of 0.004-0.020 % By weight, in particular at least 0.006% by weight of N or up to 0.0150% by weight of N, aluminum in contents of 0.001-0.035% by weight and niobium in contents of up to 0.015% by weight, titanium at levels of up to 0.01% by weight and vanadium at levels of up to 0.10% by weight.
  • the contents% Al,% Nb,% Ti,% V and% N of Al, Nb, Ti, V and N are on the condition % ⁇ al / 27 + % ⁇ Nb / 45 + % ⁇ Ti / 48 + % ⁇ V / 25 > % ⁇ N / 3.75 linked together so that the nitrogen contained in the structural steel over the respective existing contents of Al and the addition of necessary additionally added levels of Nb, Ti and V is fully bonded and boron can thus delay conversion.
  • the setting of N according to the invention makes it possible for boron to become effective as a dissolved element in the matrix and to suppress the formation of ferrite and / or perlite.
  • the micro-alloying elements V, Ti, Nb on the one hand and Al on the other hand may be present in each case in combination with one or more elements of the group "Al, V, Ti, Nb" or alone in amounts above said minimum contents.
  • contents of Cr of up to 4.00 wt .-%, in particular up to 3 wt .-% or up to 2.5 wt .-%, contribute to the hardenability and corrosion resistance of the steel according to the invention.
  • at least 0.5% by weight or at least 0.8% by weight of Cr may be provided for this purpose.
  • levels of Ni of up to 1.5 wt .-% may also contribute to the hardenability of the steel.
  • a positive effect of the optional presence of copper in the alloy of a structural steel according to the invention consists in the formation of finest Austenitfilmen and the associated significant increase in the toughness level. This effect can be achieved by providing at least 0.3% by weight of Cu, in particular more than 0.3% by weight of Cu, in the structural steel according to the invention. By limiting the Cu content to at most 0.9 wt%, an optimized positive effect of the copper content can be obtained.
  • steel according to the invention is heated to thermal temperatures of at least 100.degree. C. above the respective Ac.sub.3 temperature, in particular more than 900.degree. C., then heat-deformed and finally regulated or uncontrolled to quiescent or agitated air to a temperature cooled to less than 200 ° C, especially at room temperature, so it turns out at an extremely wide range the cooling rate after the transformation a uniform bainitic structure.
  • the Ac3 temperature of the steel may be determined in a manner known per se based on its composition.
  • the upper limit of the range of the heat temperature is typically 1300 ° C, especially 1250 ° C or 1200 ° C.
  • the t8 / 5 time can be used here, ie the time within which each thermoformed part cools from 800 ° C to 500 ° C. This t8 / 5 time should be at 10 - 1000 s in the cooling of manufactured from inventive steel components.
  • the specific cooling time selected should be selected as a function of the respective heat temperature.
  • the influence of the heat temperature can be calculated using the Fig. 2 enclosed ZTU diagram is reproduced, in which for the heat temperatures 900 ° C (solid line), 1100 ° C (dashed line) and 1300 ° C (dotted line) the respective position of the respective bainite over the cooling time is shown.
  • the heat temperatures 900 ° C (solid line), 1100 ° C (dashed line) and 1300 ° C (dotted line) the respective position of the respective bainite over the cooling time is shown.
  • the alloying concept according to the invention thus permits high thermoforming temperatures of more than 1150 ° C., as a result of which the forming forces during hot forming can be reduced without undesired grain growth occurring.
  • a further adjustment of the mechanical properties, in particular the strength and toughness, of the hot-formed according to the invention steel, in particular forged components can by means of a tempering treatment be carried out in which the respective part over a duration of 0.5 - 2 h in the temperature range of 180 - 375 ° C is maintained.
  • tensile strengths of at least 950 MPa, a yield strength of at least 750 MPa, and an elongation at break A of at least 15% can be reliably determined in the steel according to the invention, with it being found in practice that even higher elongation values A of at least 17% are regularly achieved become.
  • This combination of properties in forged steel according to the invention occur in particular when they have been produced in the manner according to the invention.
  • the semi-finished products are heated to a thermal temperature Tw for forging deformation, then thermoformed in a conventional manner by swaging to forgings and then cooled in air to room temperature. For some of the obtained forgings a tempering treatment was then carried out.
  • the thermal temperatures Tw used in the examples, the t8 / 5 time required for the passage of the critical temperature range of 800 - 500 ° C, respectively, are the temperature and duration of the t8 / 5 time Tempering treatment, if one has been carried out, as well as the bainite content in the structure, the tensile strength Rm, the yield strength Re, the elongation A and the impact energy W of the forging obtained after forging indicated.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Forging (AREA)
EP15194741.3A 2015-11-16 2015-11-16 Edelbaustahl mit bainitischem gefüge, daraus hergestelltes schmiedeteil und verfahren zur herstellung eines schmiedeteils Active EP3168312B1 (de)

Priority Applications (12)

Application Number Priority Date Filing Date Title
PT15194741T PT3168312T (pt) 2015-11-16 2015-11-16 Aço estrutural de alta qualidade com estrutura bainítica, peça forjada e método para a produção de peça forjada
EP15194741.3A EP3168312B1 (de) 2015-11-16 2015-11-16 Edelbaustahl mit bainitischem gefüge, daraus hergestelltes schmiedeteil und verfahren zur herstellung eines schmiedeteils
ES15194741T ES2733805T3 (es) 2015-11-16 2015-11-16 Acero fino estructural con estructura bainitica, pieza forjada fabricada a partir del mismo y procedimiento para fabricar una pieza forjada
DK15194741.3T DK3168312T3 (da) 2015-11-16 2015-11-16 Konstruktionsædelstål med bainitisk struktur, smedeemne fremstillet deraf og fremgangsmåde til fremstilling af et smedeemne
PL15194741T PL3168312T3 (pl) 2015-11-16 2015-11-16 Stopowa stal konstrukcyjna o strukturze bainitycznej, wytworzony z niej element kuty i sposób wytwarzania elementu kutego
RU2018121935A RU2703085C1 (ru) 2015-11-16 2016-11-15 Конструкционная сталь с бейнитной структурой, получаемые из нее кованые детали и способ производства кованой детали
CA3005378A CA3005378C (en) 2015-11-16 2016-11-15 Engineering steel with a bainitic structure, forged parts produced therefrom and method for producing a forged part
JP2018521262A JP6616501B2 (ja) 2015-11-16 2016-11-15 ベイナイト組織を有する工業用鋼材，該鋼材から製造される鍛造部品，並びに，鍛造部品の製造方法
KR1020187014749A KR102178736B1 (ko) 2015-11-16 2016-11-15 베이나이트 조직의 고-등급 구조용 강, 베이나이트 조직의 고-등급 구조용 강으로 제조된 단조품 및 단조품 제조 방법
US15/773,745 US20180327873A1 (en) 2015-11-16 2016-11-15 Engineering Steel with a Bainitic Structure, Forged Parts Produced Therefrom and Method for Producing a Forged Part
CN201680069274.3A CN108474049B (zh) 2015-11-16 2016-11-15 具有贝氏体组织结构的优质结构钢，由其生产的锻造件和锻造件的生产方法
PCT/EP2016/077761 WO2017085072A1 (de) 2015-11-16 2016-11-15 Edelbaustahl mit bainitischem gefüge, daraus hergestelltes schmiedeteil und verfahren zur herstellung eines schmiedeteils

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Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
PL3591081T3 (pl) 2018-07-05 2021-10-25 Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg Sposób wytwarzania węgloutwardzonej cieplnie stalowej części konstrukcyjnej
EP3591078B1 (de) 2018-07-05 2021-12-22 Deutsche Edelstahlwerke Specialty Steel GmbH & Co. KG Verwendung eines stahls für ein additives fertigungsverfahren, verfahren zur herstellung eines stahlbauteils und stahlbauteil
CZ308108B6 (cs) * 2018-07-20 2020-01-08 Univerzita Pardubice Bainitická ocel se zvýšenou kontaktně-únavovou odolností
WO2021009543A1 (en) * 2019-07-16 2021-01-21 Arcelormittal Method for producing a steel part and steel part
CN110527912A (zh) * 2019-09-24 2019-12-03 王平 一种红土镍矿冶炼高强韧耐候耐火合金结构钢的制备
CN111041344A (zh) * 2019-10-23 2020-04-21 舞阳钢铁有限责任公司 高强韧性低屈强比易焊接的固定海上结构钢板及生产方法
CN111394661B (zh) * 2020-04-30 2021-07-27 西京学院 一种低合金高强韧性马贝复相钢的制备工艺
CN115094350B (zh) * 2022-07-13 2023-01-24 江油市长祥特殊钢制造有限公司 一种核电sa182f316l阀体锻件的制备方法
CN115491605B (zh) * 2022-09-27 2023-03-31 东风商用车有限公司 热锻用贝氏体钢、制造热锻零部件的工艺、装置及系统

Family Cites Families (25)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4394187A (en) * 1981-02-25 1983-07-19 Sumitomo Metal Industries, Ltd. Method of making steels which are useful in fabricating pressure vessels
JPH05287439A (ja) * 1992-04-07 1993-11-02 Nippon Steel Corp 延性の優れたＭｏ−Ｖ系超高張力電縫鋼管
JPH0741856A (ja) * 1993-07-28 1995-02-10 Nkk Corp 耐硫化物応力腐食割れ性に優れた高強度鋼管の製造法
JP3241897B2 (ja) * 1993-10-12 2001-12-25 新日本製鐵株式会社 引張強度、疲労強度および被削性に優れる熱間鍛造用非調質鋼
JP3300500B2 (ja) * 1993-10-12 2002-07-08 新日本製鐵株式会社 疲労強度、降伏強度および被削性に優れる熱間鍛造用鋼の製造方法
FR2744733B1 (fr) 1996-02-08 1998-04-24 Ascometal Sa Acier pour la fabrication de piece forgee et procede de fabrication d'une piece forgee
CN1163942A (zh) * 1996-02-08 1997-11-05 阿斯克迈塔尔公司 制造锻件用钢及锻件制造方法
FR2757877B1 (fr) * 1996-12-31 1999-02-05 Ascometal Sa Acier et procede pour la fabrication d'une piece en acier mise en forme par deformation plastique a froid
JP3854807B2 (ja) * 2001-03-08 2006-12-06 株式会社神戸製鋼所 溶接性および均一伸びに優れた高張力厚鋼板
JP3901994B2 (ja) * 2001-11-14 2007-04-04 新日本製鐵株式会社 非調質高強度・高靭性鍛造品およびその製造方法
JP3668713B2 (ja) * 2001-11-26 2005-07-06 株式会社神戸製鋼所 溶接性および均一伸びに優れた高張力厚鋼板
EP1408131A1 (de) * 2002-09-27 2004-04-14 CARL DAN. PEDDINGHAUS GMBH & CO. KG Stahlzusammensetzung und daraus hergestellte Gesenkschmiedeteile
FR2847273B1 (fr) * 2002-11-19 2005-08-19 Usinor Piece d'acier de construction soudable et procede de fabrication
JP4174041B2 (ja) * 2004-08-06 2008-10-29 新日本製鐵株式会社 １１５０ＭＰａ以上の引張強さを有する溶接用鋼の製造法
US7214278B2 (en) * 2004-12-29 2007-05-08 Mmfx Technologies Corporation High-strength four-phase steel alloys
JP5472423B2 (ja) * 2005-03-29 2014-04-16 Ｊｆｅスチール株式会社 耐切断割れ性に優れた高強度・高靱性厚鋼板
DE102005052069B4 (de) * 2005-10-28 2015-07-09 Saarstahl Ag Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen
EP2123787A1 (fr) * 2008-05-06 2009-11-25 Industeel Creusot Acier à hautes caractéristiques pour pièces massives
JP5176885B2 (ja) * 2008-11-10 2013-04-03 新日鐵住金株式会社 鋼材及びその製造方法
JP5729803B2 (ja) * 2010-05-27 2015-06-03 株式会社神戸製鋼所 高張力鋼板およびその製造方法
CN102337478B (zh) * 2010-07-15 2012-11-14 宝山钢铁股份有限公司 强韧性、强塑性优良的100公斤级调质钢板及其制造方法
WO2012161323A1 (ja) * 2011-05-26 2012-11-29 新日鐵住金株式会社 機械構造用鋼部品およびその製造方法
JP5152440B2 (ja) * 2011-05-26 2013-02-27 新日鐵住金株式会社 機械構造用鋼部品およびその製造方法
JP2013104124A (ja) * 2011-11-16 2013-05-30 Jfe Steel Corp 曲げ加工性に優れた直接焼入れ焼戻し型高張力鋼板およびその製造方法
US20140283954A1 (en) * 2013-03-22 2014-09-25 Caterpiller Inc. Bainitic microalloy steel with enhanced nitriding characteristics

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

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DK3168312T3 (da) 2019-07-01
JP6616501B2 (ja) 2019-12-04
ES2733805T3 (es) 2019-12-03
KR102178736B1 (ko) 2020-11-13
CN108474049A (zh) 2018-08-31
PL3168312T3 (pl) 2019-09-30
PT3168312T (pt) 2019-07-16
CA3005378C (en) 2020-07-14
CN108474049B (zh) 2021-01-08
JP2019501280A (ja) 2019-01-17
US20180327873A1 (en) 2018-11-15
KR20180071357A (ko) 2018-06-27
WO2017085072A1 (de) 2017-05-26
EP3168312A1 (de) 2017-05-17
RU2703085C1 (ru) 2019-10-15
CA3005378A1 (en) 2017-05-26

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