US20180327873A1 - Engineering Steel with a Bainitic Structure, Forged Parts Produced Therefrom and Method for Producing a Forged Part - Google Patents

Engineering Steel with a Bainitic Structure, Forged Parts Produced Therefrom and Method for Producing a Forged Part Download PDF

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US20180327873A1
US20180327873A1 US15/773,745 US201615773745A US2018327873A1 US 20180327873 A1 US20180327873 A1 US 20180327873A1 US 201615773745 A US201615773745 A US 201615773745A US 2018327873 A1 US2018327873 A1 US 2018327873A1
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content
engineering steel
steel according
forging
steel
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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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Assigned to DEUTSCHE EDELSTAHLWERKE SPECIALTY STEEL GMBH & CO. KG reassignment DEUTSCHE EDELSTAHLWERKE SPECIALTY STEEL GMBH & CO. KG ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: SCHNEIDERS, Till, KRULL, Hans-Günter, REICHEL, ULRICH, van Soest, Frank
Publication of US20180327873A1 publication Critical patent/US20180327873A1/en
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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
    • 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
    • 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

Definitions

  • the invention relates to an engineering steel with high strength and a structure comprising at least 80 vol.-% bainite.
  • the invention also relates to a forged part, produced from such an engineering steel.
  • the invention relates to a method for producing a forged part from an engineering steel according to the invention.
  • the article also states that in this regard promise has been shown by materials with a bainitic structure, in which good strength and ductility properties are combined without the need for additional heat treatment, characterised by a tensile strength of more than 1,200 MPa, a yield strength of more than 850 MPa and an elongation at rupture of more than 10% with a notch impact energy of 27 J at room temperature.
  • the article presents a steel with (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, retained 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, retained iron and unavoidable impurities.
  • the forged part then undergoes heat treatment, comprising cooling at a rate of cooling Vr of more than 0.5° C./s from a temperature at which the steel is austenitic, to a temperature Tm of between Ms+100° C. and Ms ⁇ 20° C.
  • the forged part is then maintained for at least two minutes at a temperature between the temperature Tm and a temperature Tf, for which Tf>Tm ⁇ 100° C. applies.
  • the intention is to obtain a steel component with a substantially bainitic structure, comprising at least 15% lower bainite and preferably at least 20% bainite formed between Tm and Tf.
  • the problem for the invention was to provide a steel having a high strength, without the need to perform complex heat treatment processes, with a low tendency to warping and which as such is particularly for the production by forging techniques of forged parts with major changes in cross section over their length.
  • the intention is similarly to indicate a forged part which has an optimum combination of properties without complex heat treatment processes.
  • the intention is to propose a method for producing a forged part allowing, with simple means, the creation of forged parts with an optimised combination of properties.
  • the invention has solved the abovementioned problem with the engineering steel indicated in claim 1 .
  • the solution according to the invention to the abovementioned problem consists of producing such a steel component from a steel according to the invention.
  • the invention has solved the abovementioned problem in that in the production of a forged part the process steps mentioned in claim 13 are carried out.
  • An engineering steel according to the invention has a yield strength of at least 750 MPa and a tensile strength of at least 950 MPa and an at least 80 vol.-% bainitic structure, wherein the remaining 20 vol.-% of the structure can be retained austenite, ferrite, perlite or martensite.
  • the steel according to the invention is characterised by a high elongation at rupture A of at least 10%, in particular of at least 12%, wherein it has been shown in practice that steels according to the invention routinely achieve an elongation at rupture A of at least 15%.
  • the engineering steel therefore comprises (in wt.-%) 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 retained iron and unavoidable impurities, wherein the Al content % Al, the Nb content % Nb, the Ti content % Ti, the V content % V and the N content % N of the engineering steel in each case meet the following condition:
  • the unavoidable impurities resulting from production include all elements which with regard to their properties of interest here are present in quantities that have no effect on the alloying process and due to the steel-making route or the respective starting material selected (scrap) find their way into the steel.
  • the unavoidable impurities also include, in particular, contents of P of up to 0.0035 wt.-%.
  • a steel according to the invention and the forged parts produced from this can be characterised by a particularly uniform distribution of properties even if, due to variable component dimensions, during cooling from the forging heat, considered across the forged part volume, localised highly different cooling conditions prevail.
  • This insensitivity to the cooling conditions is achieved in that the engineering steel according to the invention has a homogenous, as far as possible exclusively bainitic structure with low variation in hardness. This homogenous microstructure at the same time has low internal stresses, which has a positive influence on the warping behaviour.
  • steel according to the invention is particularly suited to the production of forged components, in which sections with highly differing volumes and diameters come up against one another.
  • forged parts for the manufacture of which using forging techniques the steel according to the invention is particularly suited, are crankshafts, piston rods and similar, intended in particular, for combustion engines.
  • parts in the area of the chassis and the wheel suspension with highly different cross sections can be reliably produced from the steel according to the invention without major post-processing through grinding while maintaining the predetermined strength characteristics.
  • Engineering steel according to the invention is thus characterised in that it has a predominantly, that is to say up to at least 80 vol.-%, bainitic structure, wherein the content of non-bainitic structural components in steels according to the invention is typically minimised to such an extent that the steel according to the invention has a completely bainitic structure in the technical sense.
  • Limiting the content of C to a maximum of 0.25 wt.-% means on the one hand that an engineering steel according to the invention despite its maximised strength has good elongation and ductility properties.
  • the low C content also contributes to accelerating the bainite transformation so that the development of undesired structural components is avoided.
  • a certain quantity of carbon in the engineering steel according to the invention can also contribute to the strength.
  • contents of at least 0.09 wt.-% C in the steel can be envisaged.
  • An optimised effect of the presence of C in the steel according to the invention can thus be achieved in that the C content is adjusted to 0.09-0.25 wt.-%.
  • the Si content of a steel according to the invention is limited to 1.5 wt.-%, in particular 1 wt.-% or 0.75 wt.-%, to allow the bainite transformation to take place as early as possible. To be particularly sure of achieving this effect, the Si content can also be limited to a maximum of 0.45 wt.-%.
  • Mo is present in the engineering steel according to the invention in contents of 0.6-3.0 wt.-%, to delay the transformation of the structure into ferrite or perlite. This effect occurs in particular if at least 0.7 wt.-%, in particular more than 0.70 wt.-% Mo, is present in the steel. For contents of more than 3.0 wt.-% no further economically viable increase in the positive effect of Mo occurs in the steel according to the invention. Apart from this, above 3.0 wt.-% Mo there is a danger of formation of a molybdenum-rich carbide phase, which can negatively influence ductility properties. Optimum effects of Mo in the steel according to the invention can be expected if the Mo content is at least 0.7 wt.-%. Here, Mo contents of a maximum of 2.0 wt.% have proven particularly effective.
  • Manganese is present in contents of 0.20-2.00 wt.-% in the steel according to the invention, in order to adjust the tensile strength and yield strength.
  • a minimum content of 0.20 wt.-% Mn is necessary to achieve an increase in strength. If it is intended to achieve this effect with particular reliability, then an Mn content of at least 0.35 wt.-% may be provided for.
  • Excessively high Mn contents lead to delays in bainite transformation and thus to a predominantly martensitic transformation.
  • the Mn content is therefore limited to a maximum of 2.00 wt.-%, in particular 1.5 wt.-%. Negative influences from the presence of Mn can be particularly reliably avoided by limiting the Mn content in the steel according to the invention to a maximum of 1.1 wt.-%.
  • the sulphur content of a steel according to the invention can be up to 0.4 wt.-%, in particular max. 0.1 wt.-% or max. 0.05 wt.-%, to support the machinability of the steel.
  • Fine adjustment of the alloying techniques with regard to the mechanical properties and the microstructure of an engineering steel according to the invention takes place according to the alloying concept according to the invention through combined micro-alloying of the elements of boron in contents of 0.0005-0.0025 wt.-%, nitrogen in contents of 0.004-0.020 wt.-%, in particular at least 0.006 wt.-% N or up to 0.0150 wt.-% N, aluminium in contents of 0.001-0.035 wt.-% and Niob in contents of up to 0.015 wt.-%, titanium in contents of up to 0.01 wt.-% and vanadium in contents of up to 0.10 wt.-%.
  • the contents of microelements provided according to the invention and balanced with one another and the N content contribute to an increase in the fine grain stability and strength.
  • the binding according to the invention of N also allows the boron to be effective as a dissolved element in the matrix and suppresses the formation of ferrite and/or perlite.
  • the Al content may be expedient to set the Al content to at least 0.004 wt.-%, the Ti content to at least 0.001 wt.-%, the V content to at least 0.02 wt.-% or the Nb content to at least 0.003 wt.-%.
  • the microalloying elements V, Ti and Nb, on the one hand, and Al, on the other, can in each case be present in combination with one or more elements from the group “Al, V, Ti, Nb” or alone in quantities above the stated 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 durability and the corrosion-resistance of the steel according to the invention.
  • at least 0.5 wt.-% or at least 0.8 wt.-% Cr can be provided.
  • Ni up to 1.5 wt.-% can likewise contribute to the hardenability of the steel.
  • the alloying elements reaching the steel according to the invention via the starting material or intentionally added alloying elements also include Cu, the content of which, in order to avoid negative influences in the steel according to the invention is limited to a maximum of 2.0 wt.-%.
  • a positive effect of the optional presence of copper in the alloying of an engineering steel according to the invention consists of the formation of the finest retained austenite films and the associated significant raising of the level of ductility. This effect can be achieved in that at least 0.3 wt.-% Cu, in particular more than 0.3 wt.-% Cu, is present in the engineering steel according to the invention.
  • an optimised positive effect of the copper content can be achieved.
  • a steel according to the invention is heated to heat temperatures typical for hot working of at least 100° C. above the respective Ac3 temperature, in particular a heat temperature of more than 900° C. for the hot working, then hot worked and finally cooled in a regulated or unregulated fashion under stationary or moving air to a temperature of less than 200° C., in particular to room temperature, then over an extremely broad range of cooling speeds following transformation a uniform bainitic structure results.
  • the Ac3 temperature of the steel can be determined in a known manner on the basis of its respective composition.
  • the upper limit to the range of the heating temperature is typically 1,300° C., in particular 1,250° C. or 1,200° C.
  • the t8/5 time can be used here, thus the time taken by the respective hot-worked part to cool from 800° C. to 500° C.
  • this t8/5 time is intended to be 10-1,000 s.
  • the cooling time selected in each specific case should be selected based on the respective heating temperature.
  • the influence of the heating temperature can be understood from the time-temperature diagram attached as FIG. 2 , in which for the heating temperatures 900° C. (unbroken line), 1,100° C. (dashed line) and 1,300° C. (dotted line) the respective position of the respective bainite range is shown across the cooling time. Accordingly, at low heating temperatures of 900° C. shorter t8/5 times should be selected, to achieve the desired bainitic structure, whereas at higher heating temperatures the cooling can be slower. A high certainty that during cooling of steel according to the invention the bainite range will be reached independently of the respective heating temperature exists for steels according to the invention at heating temperatures in the range of 900-1,300° C. and accordingly if the t8/5 time is 100-800 s.
  • the alloying concept according to the invention therefore allows high hot-working temperatures of more than 1,150° C., as a result of which the forming forces during the hot-working can be reduced without an undesired grain growth occurring.
  • the method according to the invention for producing forged parts with a yield strength of at least 750 MPa and a tensile strength of at least 950 MPa and an at least 80 vol.-% bainitic structure, which can contain in total up to 20 vol.-% of retained austenite, ferrite, perlite or martensite, comprises the following process steps:
  • the respective semi-finished product representing the starting point of the forging is heated to a forging temperature of more than 1,150° C.
  • a further adjustment of the mechanical properties, in particular the strength and ductility of the components hot-worked, in particular forged, from steel according to the invention, can take place by means of tempering treatment, during which the respective part is maintained for a duration of 0.5-2 h in the temperature range 180-375° C.
  • the semi-finished products are heated for forging deformation to a heat temperature Tw, then in a conventional manner hot worked using drop forging to produce forged parts and then cooled to room temperature in the air. With some of the forged parts obtained, a tempering treatment is then performed.
  • Table 2 shows the heating temperatures Tw applied in the examples, the t8/5 time necessary in each case for passing through the critical temperature range of 800-500° C., the temperature and duration of the tempering treatment, where this was actually carried out, and the proportion of bainite in the structure, the tensile strength Rm, the yield strength Re, the extension A and the notch impact energy W of the forged part obtained after forging.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
  • Forging (AREA)
  • Heat Treatment Of Articles (AREA)
US15/773,745 2015-11-16 2016-11-15 Engineering Steel with a Bainitic Structure, Forged Parts Produced Therefrom and Method for Producing a Forged Part Abandoned US20180327873A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP15194741.3 2015-11-16
EP15194741.3A EP3168312B1 (fr) 2015-11-16 2015-11-16 Acier inoxydable de construction comprenant un joint bainitique, pièce forgée ainsi fabriquée et procédé de fabrication d'une pièce forgée
PCT/EP2016/077761 WO2017085072A1 (fr) 2015-11-16 2016-11-15 Acier de construction fin présentant une structure bainitique, pièce forgée fabriquée à partir de celui-ci et procédé pour la fabrication d'une pièce forgé

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US (1) US20180327873A1 (fr)
EP (1) EP3168312B1 (fr)
JP (1) JP6616501B2 (fr)
KR (1) KR102178736B1 (fr)
CN (1) CN108474049B (fr)
CA (1) CA3005378C (fr)
DK (1) DK3168312T3 (fr)
ES (1) ES2733805T3 (fr)
PL (1) PL3168312T3 (fr)
PT (1) PT3168312T (fr)
RU (1) RU2703085C1 (fr)
WO (1) WO2017085072A1 (fr)

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ES2908807T3 (es) 2018-07-05 2022-05-04 Deutsche Edelstahlwerke Specialty Steel Gmbh & Co Kg Uso de un acero para un procedimiento de fabricación aditivo, procedimiento para la fabricación de una pieza constructiva de acero y pieza constructiva de acero
PL3591081T3 (pl) 2018-07-05 2021-10-25 Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg Sposób wytwarzania węgloutwardzonej cieplnie stalowej części konstrukcyjnej
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JP6616501B2 (ja) 2019-12-04
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EP3168312B1 (fr) 2019-04-10
PT3168312T (pt) 2019-07-16
CN108474049B (zh) 2021-01-08
WO2017085072A1 (fr) 2017-05-26
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KR102178736B1 (ko) 2020-11-13
CN108474049A (zh) 2018-08-31

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