EP3591081B1 - Verfahren zur herstellung eines einsatzgehärteten stahlbauteils - Google Patents

Verfahren zur herstellung eines einsatzgehärteten stahlbauteils Download PDF

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Publication number
EP3591081B1
EP3591081B1 EP18182024.2A EP18182024A EP3591081B1 EP 3591081 B1 EP3591081 B1 EP 3591081B1 EP 18182024 A EP18182024 A EP 18182024A EP 3591081 B1 EP3591081 B1 EP 3591081B1
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Prior art keywords
steel
steel component
weight
temperature
hardening
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EP18182024.2A
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German (de)
English (en)
French (fr)
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EP3591081A1 (de
Inventor
Frank van Soest
Hans-Günter Dr. 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 ES18182024T priority Critical patent/ES2878652T3/es
Priority to PT181820242T priority patent/PT3591081T/pt
Priority to PL18182024T priority patent/PL3591081T3/pl
Priority to EP18182024.2A priority patent/EP3591081B1/de
Publication of EP3591081A1 publication Critical patent/EP3591081A1/de
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    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • 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
    • C21D1/06—Surface 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/32—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for gear wheels, worm wheels, or the like
    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
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    • 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
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    • 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
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    • 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
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    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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    • 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
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/02—Pretreatment of the material to be coated
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/20—Carburising
    • C23C8/22—Carburising of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/28—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases more than one element being applied in one step
    • C23C8/30—Carbo-nitriding
    • C23C8/32—Carbo-nitriding of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/34—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases more than one element being applied in more than one step
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/80—After-treatment
    • 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
    • C21D2221/00—Treating localised areas of an article
    • C21D2221/10—Differential treatment of inner with respect to outer regions, e.g. core and periphery, respectively

Definitions

  • the invention relates to a method for producing a case-hardened steel component. If "%" information is given below about alloys or steel compositions, these relate to weight, unless expressly stated otherwise.
  • the steel components considered here are typically components that in practice come into metallic contact with other components in a rolling or rolling movement and are therefore exposed to high mechanical loads in the area of their contact surface.
  • Typical examples of such components are gears, shafts or axles. Comparable loads can occur in the case of tool holders, for example cutting tools and the like, come in the area of the contact surfaces between the holder and the respective tool.
  • case hardening steels are typically used today for gear manufacturing, examples of which are the steels with 16MnCr5 / 16MnCrS5 (material numbers 1.7131 /1.7139) and 18CrNiMo7-6 (material number 1.6587).
  • Tool holders such as holders for cutting bodies produced by powder metallurgy, are often made from relatively expensive tool steels, such as steels with the material numbers 1.2311, 1.2312, 1.2738, 1.2343 or 1.2343.
  • Case hardening in which the surface layer of the steel component is first subjected to a carburizing or carbonitriding treatment to increase the carbon content, is one of the common methods with which gearwheels and components that are subjected to comparable loads in use can be provided with a hardened surface layer and then the component undergoes hardening in order to achieve maximum hardness in the hardened surface layer, and nitriding or nitrocarburizing (see leaflet 477), in which the increase in hardness of the surface layer is essentially achieved by diffused nitrogen, with an additional increase in hardness by can be achieved in combination with the nitrogen diffused carbon.
  • the object of the invention was to name a method for producing a steel component which has the optimum combination of properties in those surface-hardened by a thermochemical diffusion treatment Steel components that are in rolling or rolling contact with another component during use.
  • a surface-hardened steel component is also disclosed, which has an optimal combination of hardness in its surface layer and toughness in its core area bearing the surface layer with regard to its fatigue strength.
  • the invention includes the method according to claim 1.
  • the steel to be used according to the invention opens up a robust and cost-effective production route for the production of steel components to be surface hardened by a thermochemical diffusion treatment, namely gear wheels, axles, shafts or tool holders with special application conditions.
  • a thermochemical diffusion treatment namely gear wheels, axles, shafts or tool holders with special application conditions.
  • the components produced from steel used according to the invention have a higher toughness in their core area, also called “matrix", than is the case with steels commonly used for this purpose today.
  • the invention is based on the knowledge that a modification of a steel forming a bainitic structure, which is basically from the publication EP 3 168 312 A1 a European patent application is already known for the forging production of components, is also particularly suitable as a material for the production of steel components with a thermochemically hardened surface layer. It has surprisingly been shown that the alloy concept intended for forging applications also has considerable advantages in terms of the toughness of the steel component in its core area due to the high tempering resistance of the bainitic structure of the steel proposed for use according to the invention.
  • the steel known per se from the publication of the aforementioned European patent application, as in FIG EP 3 168 312 A1 explained in detail, has a wide bainite window in the time-temperature diagram ("ZTU diagram"), i.e. reliably forms a bainitic structure dominated by bainite to at least 80% by volume over a large range of cooling speeds.
  • ZTU diagram time-temperature diagram
  • the known alloy specification ensures these properties of the steel even if the steel is not cooled from the forging heat, as originally intended, but is subjected to a thermochemical diffusion treatment. This also applies if the respective steel component is subjected to hardening after the diffusion treatment, as is usual with case hardening.
  • EP 2 357 262 A1 discloses a crankshaft and a manufacturing method therefor.
  • JP 2006 169637 A discloses a method of making a high strength, carburized component.
  • EP 1 070 760 A2 discloses a high-pressure-resistant component and its manufacturing method.
  • Steel components produced from steel used according to the invention are distinguished by a particularly homogeneous structure with a low variance in hardness. This optimally even distribution of the structural properties is also included
  • the homogeneous structural condition that occurs when the steel is used according to the invention also results in low internal stresses in the component.
  • the steel components produced from steel used according to the invention tend to warp and cracks or other stress-related damage at most in the course of the thermochemical hardening of the surface layer.
  • a steel component which is a gear wheel, a shaft, an axle or a tool holder, with a thermochemically hardened surface layer
  • a thermochemically hardened surface layer which consists of (in% by weight) 0.1-0, 30% C, up to 0.80% Si, 0.20 - 2.00% Mn, up to 4.00% Cr, 0.5 - 1.80% Mo, 0.004 - 0.020% N, up to 0, 40% S, 0.004 - 0.020% Al, up to 0.0025% B, up to 0.20% Nb, up to 0.02% Ti, up to 0.40% V, up to 0.5% Ni, 0.3% Cu, up to 1.5% Co and the remainder of iron and unavoidable impurities, with the Al content% Al, the Nb content% Nb, the Ti content% Ti, the V content % V and the N content% N of the steel meet the following conditions: % Al / 27 + % Nb / 45 + % Ti / 48 + % V / 25th > % N / 3.5
  • the steel to be used according to the invention is alloyed and can be processed in such a way that the steel component that is made from it has a structure consisting of at least 80% by volume of bainite in its core area.
  • the impurities of the steel to be used according to the invention which are unavoidable as a result of the production process, include all elements that are present in amounts which are ineffective in terms of alloying technology and due to the properties of interest here
  • the route chosen in each case to produce the steel powder or the selected starting material (scrap) get into the steel.
  • the unavoidable impurities also include P contents of up to 0.0035% by weight.
  • a steel component produced from steel to be used according to the invention is thus characterized in that it has a structure consisting of at least 80% by volume of bainite.
  • the rest of the structure of a maximum of 20% by volume of the total structure is taken up by residual austenite, ferrite, pearlite and / or martensite.
  • the contents of non-bainitic structural constituents of a steel component made of steel to be used according to the invention are so greatly minimized that it has a completely bainitic structure in the technical sense.
  • the alloy concept on which the steel to be used according to the invention is based avoids expensive alloy components, such as are usually required today for the case-hardening and tool steels used for the production of steel components in question, in order to set the required hardness.
  • Carbon Carbon
  • By adding 0.01% by weight in each case an increase in strength of approx. 70 MPa can be achieved.
  • This effect starts in particular from a content of at least 0.09% by weight of C, in particular at least 0.12% by weight of C,.
  • the steel By limiting the C content to a maximum of 0.30% by weight, in particular a maximum of 0.25% by weight, the steel has good elongation and toughness properties despite its maximized strength.
  • the comparably low C content in a steel to be used according to the invention also contributes to the acceleration of the bainite transformation, so that the formation of undesirable structural components is avoided.
  • An optimized effect of the presence of C in the steel to be used according to the invention can be achieved by setting the C content to 0.12-0.25% by weight.
  • Si Silicon
  • the Si content of a steel to be used according to the invention is therefore limited to 0.80% by weight, in order to allow the bainite transformation to take place as early as possible. At the same time, Si contents up to this upper limit contribute to increasing the strength through solid solution strengthening.
  • the Si content is therefore preferably at least 0.2% by weight, in particular more than 0.45% by weight, such as at least 0.46% by weight .-%, adjusted.
  • Manganese is present in contents of 0.20-2.00% by weight in the steel to be used according to the invention, in order to adjust the tensile strength and yield point by means of solid solution formation.
  • a minimum content of 0.20% by weight Mn is required so that there is an increase in strength. If this effect is to be achieved particularly reliably, an Mn content of at least 0.4% by weight can be provided. Too high an Mn content would, however, lead to a delay in the bainite transformation and thus to a predominantly martensitic transformation. Therefore, the Mn content is limited to at most 2.00% by weight, particularly at most 1.5% by weight. Negative influences of the presence of Mn can be avoid particularly safely by limiting the Mn content of the steel to be used according to the invention to a maximum of 1.2% by weight.
  • chromium of up to 4.00% by weight contribute to the hardenability and corrosion resistance of the steel to be used according to the invention due to the formation of special carbides and chromium nitrides during one of the nitriding treatment carried out according to the invention.
  • Cr chromium
  • at least 0.5% by weight or at least 0.8% by weight of Cr can be provided.
  • An optimal effect of the presence of Cr results with a Cr content of at least 1.00% by weight.
  • Cr contents above 4.00% by weight would promote undesirable martensite formation in the structure of the steel to be used according to the invention.
  • the Cr content can be limited to up to 3% by weight or up to 2.5% by weight.
  • Molybdenum (“Mo”) is present in the steel to be used according to the invention in contents of 0.5-1.8% by weight in order to delay the transformation of the structure into ferrite or pearlite and to enlarge the window for the bainite transformation. This effect occurs in particular when at least 0.6% by weight is present in the steel. With contents of more than 1.8% by weight, based on the use of the steel to be used according to the invention, which is the focus here, there is no longer any economically justifiable further increase in the positive effect of Mo. By limiting the Mo content to 1.8% by weight, the formation of a carbide phase rich in molybdenum, which would negatively affect the toughness properties, is reliably excluded. Optimal effects of Mo in the steel to be used in the present invention can be expected when the Mo content is at least 0.7% by weight. Mo contents of at most 1.5% by weight or at most 1.0% by weight have proven to be particularly effective.
  • N in the contents of 0.004-0.020% by weight provided according to the invention enables the formation of nitrides and carbonitrides to increase strength and increase fine-grain resistance without embrittlement occurring.
  • Al and N form aluminum nitride, which contributes to fine-grain stability.
  • the content of sulfur ("S") in the steel to be used according to the invention can be up to 0.4% by weight, in particular at most 0.1% by weight, in order to support the machinability of the steel.
  • S sulfur
  • an S content of at least 0.001% by weight can be provided. If the S content is above 0.4% by weight, there is a risk of red brittleness.
  • Optimal effects of the presence of S in the steel to be used according to the invention can be achieved with contents of 0.003-0.1% by weight.
  • B in contents of up to 0.0025% by weight, in particular at least 0.0001% by weight or at least 0.0005% by weight, in the steel to be used according to the invention delays the formation of ferrite or pearlite and secures it thus the formation of the desired bainitic structure in the steel to be used according to the invention.
  • B contents above 0.0025% by weight would entail the risk of embrittlement.
  • the optionally present micro-alloy elements Nb, Ti and V form carbonitrides and can thus make a significant contribution to optimizing the fine-grain stability and strength of the steel to be used according to the invention.
  • the alloying fine adjustment with regard to the mechanical properties and the structure of a steel used according to the invention is carried out according to the alloy concept used according to the invention via a combined microalloy made up of the elements Boron (“B”) in optional contents of up to 0.0025% by weight, in particular in contents of 0.0001-0.0025% by weight B or 0.0005-0.0025% by weight B, Nitrogen (“N”) in contents of 0.004-0.020% by weight, in particular at least 0.006% by weight N or up to 0.0150% by weight N, aluminum (“AI”) in contents of 0.004-0.020% by weight .-% and niobium (“Nb”) in optional contents of up to 0.020% by weight, in particular up to 0.015% by weight and in particular at least 0.003% by weight or at least 0.005% by weight of Nb, titanium (“ Ti ”) in optional contents of up to 0.02% by weight or up to 0.015% by weight, in particular at least 0.001% by weight or at least 0.005% by weight Ti, and vanadium (“ V ”)
  • the micro-alloy elements and of aluminum In order to safely use the advantages of the presence of the micro-alloy elements and of aluminum, it can be expedient to reduce the Al content to at least 0.005% by weight, the Ti content to at least 0.001% by weight, and the V content to at least 0 , 02% by weight or the Nb content to at least 0.003% by weight.
  • the micro-alloy elements V, Ti, Nb on the one hand and Al on the other hand can be present in each case in combination with one or more elements from the group "Al, V, Ti, Nb" or alone in amounts above the minimum contents mentioned.
  • the contents% Al,% Nb,% Ti,% V and% N of Al, Nb, Ti, V and N are above the condition in the steel to be used according to the invention % Al / 27 + % Nb / 45 + % Ti / 48 + % V / 25th > % N / 3.5 linked together in such a way that the nitrogen contained in the steel to be used according to the invention is completely bound via the respective existing contents of Al as well as the optionally additionally added contents of Nb, Ti and V and boron can thus have a conversion-retarding effect.
  • the binding of N according to the invention also enables the optionally present boron to act as a dissolved element in the matrix of the steel and suppress the formation of ferrite and / or pearlite.
  • Ni up to 0.5% by weight improve the toughness of the steel to be used according to the invention. If this effect is to be used, it occurs from a Ni content of at least 0.1% by weight, in particular at least 0.15% by weight.
  • the alloying elements that enter the steel to be used according to the invention via the starting material or are added in a targeted manner also include Cu, the content of which is limited to a maximum of 0.3% by weight in order to avoid negative influences in the steel to be used according to the invention.
  • Co Cobalt
  • contents of up to 1.5% by weight causes the bainite formation to be shifted to shorter times.
  • the positive influence of Co can be used in particular with Co contents of at least 0.25% by weight, in particular at least 0.5% by weight, with Co contents of up to 1.0% by weight have proven to be particularly effective.
  • a steel alloy particularly suitable for the purposes according to the invention accordingly consists of (in% by weight) 0.12 - 0.25% C, 0.20 - 0.80% Si, 0.40 - 1.20% Mn, 1.0-3.0% Cr, 0.5-1.8% Mo, 0.004-0.020% N, up to 0.40% S, 0.004-0.020% Al, 0.0005-0.0025% B, up to 0.10% Nb, up to 0.015% Ti, up to 0.20% V, up to 0.5% Ni, and / or up to 1.5% Co, the remainder being iron and unavoidable impurities, for which the explanations given above in this regard also apply here.
  • the steel to be used for the production of steel components is suitable for all of the thermochemical diffusion processes "carburizing", “carbonitriding”, “nitriding” or “nitrocarburizing” described in the above mentioned leaflets 452 and 477.
  • carburizing or carbonitriding is carried out as a thermochemical diffusion treatment.
  • carburizing carburizing, carbonitriding
  • hardening takes place during conventional case hardening in accordance with the hardening methods "direct hardening (type A)", “single hardening (type B)", “isothermal hardening”, which are also described in detail in leaflet 452 Converting (Type C) "or” Double Hardening (Type D) ".
  • direct hardening type A
  • the steel component is quenched directly from the heat of the preceding carburizing or carbonitriding treatment.
  • the steel component With single hardening (type B), after the previous carburizing or carbonitriding treatment, the steel component is first cooled to room temperature and then heated again to an austenitizing temperature above the Ac1 and below the Ac3 temperature of the steel and then quenched.
  • type C hardening after isothermal conversion
  • the steel component is initially cooled from the heat of the preceding carburizing or carbonitriding treatment to a temperature range in which certain carbide precipitates are formed, and then, starting from this temperature range, it is again heated through to an austenitizing temperature above the Ac1 and below the Ac3 temperature of the steel, in order then to be quenched.
  • double hardening (type D) after the steel component has been cooled to room temperature from the heat of the previous carburizing or carbonitriding treatment, as with single hardening type A, it goes through a hardening process twice, which is only performed once with single hardening type A.
  • the cooling to be carried out must in any case be set so that, on the one hand, the carburizing or carbonitriding hardness-increasing precipitates on the carburized edge layer and, in the non-carburized core area of the component, a structure consisting of at least 80% by volume of bainite according to the stipulation explained above.
  • the temperature range of 800-500 ° C. must be passed through in a time t8 / 5 of at least 6 s, in particular at least 10 s, and at most 600 s, during the cooling process.
  • thermochemical diffusion treatment is to be carried out as nitriding or nitrocarburizing for the purpose of forming the hardened surface layer, which is not covered by the present invention, then the procedure described in detail in leaflet 477 can be selected.
  • the steel component After being heated to an austenitizing temperature above the Ac3 temperature of the steel from which the steel component is made, the steel component is continuously cooled so that the temperature range of 800 - 500 ° C in a time t8 / 5 of at least 6 s, in particular at least 10 s, and a maximum of 1000 s, in particular a maximum of 200 s, is run through in order to form in the component a structure consisting of at least 80% by volume of bainite in accordance with the stipulation explained above.
  • the nitriding or nitrocarburizing step in which the steel component is placed in a nitrogen or nitrogen and carbon-containing atmosphere at a temperature below the Ac1 temperature of the steel from which the steel component is made, in accordance with the instructions and stipulations contained in leaflet 477 exists, the lying temperature is maintained and then cooled.
  • the duration for which the steel component is held under the carbonaceous medium during the carburizing step is set in a manner known per se, depending on the size of the component and taking into account the carbonaceous medium used and the temperature at which the carburization is carried out, as follows chosen so that a carburized surface layer with a thickness lying within the specifications according to the invention is achieved.
  • the shortest duration can be indicated, for example, for smaller components, such as gear parts, in particular gears, shafts and axles, of automobile transmissions and the like, whereas the longest duration can be appropriate for large components, such as gear parts, in particular gears, shafts and axles, of large gears that are intended for slewing bearings such as those used in wind turbines or ship propulsion systems.
  • the temperature at which the steel component is kept during the carburizing step (step b.1) is typically up to 950 ° C.
  • the carburizing process can be accelerated and the duration required for the required carburizing can be shortened accordingly.
  • step b1) the steel component is hardened in a hardening step b2) heated to an austenitizing temperature which is at least 20 ° C above the Ac1 temperature and below the Ac3 temperature of the steel from which the steel component is made, and based on the austenitizing temperature with a cooling rate of 0.5 - 50 K / s , in particular at least 1.5 K / s or more than 1.5 K / s, cooled to room temperature.
  • the steel component made of steel according to the invention can optionally be subjected to a stress-relieving anneal between steps b1) and b2), in which it is heated for a period of 15 - 120 min Range of 150 - 680 ° C is maintained.
  • the steel component can optionally be subjected to a tempering treatment in a manner known per se, in which it is kept at a temperature of 150-275 ° C for a period of 30-180 minutes and then cooled to room temperature in an uncontrolled manner becomes.
  • a tempering treatment in a manner known per se, in which it is kept at a temperature of 150-275 ° C for a period of 30-180 minutes and then cooled to room temperature in an uncontrolled manner becomes.
  • Such tempering can further reduce the risk of cracking.
  • a case-hardened steel component according to the invention can be produced that is made from the steel to be used according to the invention, which consists of (in% by weight) 0.12-0.25% C, 0.20-0.80% Si, 0.40-1.20% Mn, 1.0-3.0% Cr, 0.5-1.8% Mo, 0.004-0.020% N, up to 0.40% S, 0.004-0.020% AI, 0.0001 - 0.0025% B, up to 0.10% Nb, up to 0.01% Ti, up to 0.20% V, up to 0.5% Ni, up to 1.0% Co and as the remainder iron and unavoidable impurities, is made and a surface layer with a hardness of 500 - 800 HV and according to the invention in its core area consists of at least 80% by volume of bainite, which consists of highly tempered bainite, which comes from the structure that the steel component after insertion (step b.1) and before hardening (step b.2 ), and newly formed bainite
  • This structural composition results from hardening of the components according to the invention in the two-phase area.
  • the existing bainitic structural components that have arisen from the "old", i.e. prior to hardening (step b.2) can be separated from the "new" bainitic structural components that have arisen in the course of the hardening by a slight brown coloration of the new bainite from the old,
  • highly tempered bainite which has a grayish color and an indicated grainy structure.
  • the structure of a component that has gone through the above-explained case hardening process modified in accordance with the invention is characterized in that it has a Charpy-V notch impact energy of more than 40 J, in particular more than 40 J, determined in accordance with DIN EN 10045, in the core area of the steel component 60 J.
  • Cr, V, Nb or Ti contents of the steel used in accordance with the invention arise from the formation of nitrides for a high surface hardness.
  • the bainitic core area (matrix) experiences an increase in hardness of approx. 100 - 150 MPa during nitriding or nitrocarboring due to the formation of Special carbides, in particular from the Mo content (molybdenum-rich carbide) contained in the steel.
  • the specifically set parameters "duration” and "temperature” of the nitriding or nitrocarburizing treatment are set in a manner known per se, depending on the component size, so that a hardened surface layer is achieved with a thickness within the specifications according to the invention.
  • steps B1) and B2) on the steel component which is still relatively soft after step B1), in order to reduce tool wear compared to machining in the final hardened state Reduce.
  • the steel to be used according to the invention is particularly suitable for the production of surface-hardened gear wheels, axles, shafts or tool holders for cutting tools produced by powder metallurgy.
  • a gear was formed from steel S1.
  • the gear was then subjected to a conventional manner in accordance with the procedure described in leaflet 452, initially to carburizing at 920 ° C. over a period of 300 min under a carbon-containing atmosphere composed in a manner known per se for this purpose.
  • the gear is through thermochemical diffusion created a carburized surface layer with a thickness of 520 ⁇ m.
  • the gearwheel was then cooled to room temperature, the cooling rate being 2 K / s and the critical temperature range of 800-500 ° C. being passed through in a t8 / 5 time of 10 minutes.
  • the resulting gear was then heated to an austenitizing temperature of 920 ° C. and held at this temperature for 30 minutes.
  • the gear was then quenched at a cooling rate of 2 K / s.
  • the critical temperature range of 800 - 500 ° C was passed through in a t8 / 5 time of 600 s.
  • the gear wheel case-hardened in this way had a hardness of 750 HV on the surface of its hardened edge layer and a completely bainitic structure in its core area (matrix) bearing the hardened edge layer.
  • the gear was then quenched in oil to room temperature.
  • the critical temperature range of 800 - 500 ° C was passed through in a t8 / 5 time of 17 s.
  • the gearwheel then went through a stress-relieving heat treatment, in which it was held at 650 ° C. for one hour in order to relieve the stresses that had arisen during the previously performed carburizing treatment.
  • the component was heated in a hardening step to an austenitizing temperature and held at this temperature for one hour, which was 40 ° C. below the Ac3 temperature of steel S2, the Ac3 temperature of steel S2 previously known per se Way has been determined by means of a dilatometer experiment.
  • the gearwheel was then quenched in oil again, so that here too the t8 / 5 time was 17 s.
  • the gear was subjected to a conventional tempering in which it was held at 180 ° C. for one hour.
  • the case-hardened gear wheel had a hardness of 750 HV on the surface of its hardened edge layer and a completely bainitic structure in its core area (matrix) bearing the hardened edge layer, which consisted of newly formed and old, highly tempered bainite.
  • a gear with a diameter of less than 40 mm was formed from steel S3.
  • the gearwheel was then first subjected to carburizing at 920 ° C. over a period of 30 minutes under a carbon-containing atmosphere that is usually used for this purpose.
  • a carbonized (carburized) surface layer with a thickness of 530 ⁇ m was created on the gear wheel by thermochemical diffusion.
  • the gear was then quenched in water at a cooling rate of 3 K / s to room temperature.
  • the critical temperature range of 800 - 500 ° C was passed through in a t8 / 5 time of 300 s.
  • the component was heated in a hardening step to an austenitizing temperature and held at this temperature for one hour, which was 920.degree.
  • the gearwheel was then quenched in water, the t8 / 5 time being 300 s.
  • the gear wheel case-hardened in this way had a hardness of 760 HV on the surface of its hardened edge layer and a completely bainitic structure in its core area (matrix) bearing the hardened edge layer.

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EP18182024.2A 2018-07-05 2018-07-05 Verfahren zur herstellung eines einsatzgehärteten stahlbauteils Active EP3591081B1 (de)

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ES18182024T ES2878652T3 (es) 2018-07-05 2018-07-05 Procedimiento para la fabricación de una pieza de construcción de acero endurecida por cementación
PT181820242T PT3591081T (pt) 2018-07-05 2018-07-05 Processo para a produção de um componente em aço cementado
PL18182024T PL3591081T3 (pl) 2018-07-05 2018-07-05 Sposób wytwarzania węgloutwardzonej cieplnie stalowej części konstrukcyjnej
EP18182024.2A EP3591081B1 (de) 2018-07-05 2018-07-05 Verfahren zur herstellung eines einsatzgehärteten stahlbauteils

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