WO2021084025A1 - Acier résistant à la corrosion et à durcissement par précipitation, procédé de production d'un composant d'acier, et composant d'acier - Google Patents

Acier résistant à la corrosion et à durcissement par précipitation, procédé de production d'un composant d'acier, et composant d'acier Download PDF

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WO2021084025A1
WO2021084025A1 PCT/EP2020/080438 EP2020080438W WO2021084025A1 WO 2021084025 A1 WO2021084025 A1 WO 2021084025A1 EP 2020080438 W EP2020080438 W EP 2020080438W WO 2021084025 A1 WO2021084025 A1 WO 2021084025A1
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steel
mass
content
component
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PCT/EP2020/080438
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German (de)
English (en)
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Horst HILL
André VAN BENNEKOM
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Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg
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Priority to EP20796826.4A priority Critical patent/EP3850114A1/fr
Publication of WO2021084025A1 publication Critical patent/WO2021084025A1/fr

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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C22C38/18—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
    • C22C38/48—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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • Corrosion-resistant and precipitation hardening steel method of manufacturing a steel component and steel component
  • the invention relates to a steel which, in particular, has corrosion-resistant properties and enables precipitation hardening to achieve high hardnesses.
  • the invention also relates to a method for producing a steel component, the method comprising melting a steel melt from the steel according to the invention.
  • the invention also relates to a component which is produced from a steel made according to the invention and to advantageous uses of the steel.
  • Steel materials are often characterized either by high corrosion resistance or by high hardness or wear resistance. According to the respective field of application, steel materials are selected based on this division, depending on which of the properties is in the foreground in the application.
  • Typical examples of these steels are standardized under the material numbers 1.4542 and 1.4545 in the steel-iron list.
  • the structure of corresponding steels can be converted into a predominantly martensitic structure via heat treatment and, if necessary, via quenching. Due to the low carbon content of these steels, high hardness is not initially achieved, but the steels can be hardened by a subsequent precipitation heat treatment with the formation of intermetallic phases. As a result, the corrosion resistance of these materials after the precipitation heat treatment is comparable to the corrosion resistance of conventional stainless austenitic materials, although a higher hardness and strength can be achieved overall.
  • WO 2017/198530 A1 discloses a steel material which is said to be particularly suitable for pumps and the like, which consists of, in% by mass, C: ⁇ 0.050%, Si: ⁇ 0.70 %, Mn: ⁇ 1.00%, P: ⁇ 0.030%, S: ⁇ 0.010%, Cr: 14-15.50%, Mo: 0.30-0.60%, Ni; 4.50-5.50%, V: ⁇ 0.20%, W: ⁇ 0.20%, Cu: 2.50-4.00%, Co: ⁇ 0.30%, Ti: ⁇ 0.05 %, AI: ⁇ 0.05%, Nb: ⁇ 0.05%, Ta: ⁇ 0.05%, N: ⁇ 0.05%.
  • the alloy of the steel material is designed here in such a way that Nb stabilization and the formation of hard phases are avoided, which from the point of view of the prior art would reduce the toughness. Furthermore, from WO 00/53821 A1 a precipitation-hardenable, martensitic, stainless steel alloy is known, which consists of, in% by mass,
  • the alloy should offer superior machining properties and at the same time meet the requirements for strength, ductility and hardness specified in AMS 5659 for critical applications.
  • the steel alloy includes a steel made of, in% by mass, 0.022% C, 0.23% Si, 0.44% Mn, 15.29% Cr, 4.73% Ni, 3.79% Cu, 0.25% Mo, 0.45% Nb, 0.028% P, 0.003% S, the remainder Fe and unavoidable impurities.
  • EP 3385403 A1 discloses a high-strength seamless stainless steel pipe which, even with great wall thicknesses, is said to have high strength, excellent low-temperature toughness and excellent corrosion resistance.
  • the stainless steel pipe consists of, in mass%, C: 0.05% or less, Si: 1.0% or less, Mn: 0.1 to 0.5%, P: 0.05% or less, S : less than 0.005%, Cr: more than 15.0% to 19.0% or less, Mo: more than 2.0% to 3.0% or less, Cu: 0.3 to 3.5%, Ni : 3.0% or more and less than 5.0%, W: 0.1 to 3.0%, Nb: 0.07 to 0.5%, V: 0.01 to 0.5%, AI: 0.001 to 0.1%,
  • N 0.010 to 0.100%
  • O 0.01% or less
  • Fe and unavoidable impurities as the balance.
  • the contents of Nb, Ta, C, N and Cu should be 5.1 ⁇ Nb + 0.5 ⁇ Ta - 10 - 2.2 / C + 1.2 N + Cu ⁇ 1.0.
  • the steel pipe has a microstructure composed of 45% or more of an annealed martensite phase, 20 to 40% of a ferrite phase and more than 10% and 25% or less of a retained austenite phase in terms of volume ratio is formed.
  • the structure of the cast stainless steel having Cu precipitates with an average particle size of 0.1-0.4 ⁇ m, which are dispersed in a tempered martensite-based matrix .
  • a refiner disk for treating paper pulp fibers is known, which is made of a stainless steel alloy, which consists of, in mass%, 0.2-0.4% C, 0.5-1.5% Mn, 0.5 - 1.5% Si, ⁇ 0.05% S, 0.05% P, 14 - 18% Cr, 2 - 5% Ni, 2 - 5% Cu, ⁇ 1%
  • Niobium forms carbides at high temperatures during the melting process. When cooling down, these carbides are evenly distributed in the structure.
  • a stainless steel powder is known from EP 3 117934 A1, which is processed into a component or semi-finished product by pressing.
  • the particles of the stainless steel powder consist of a steel which, in mass%, consists of C: ⁇ 0.05%, Si: ⁇ 1.0%, Mn: ⁇ 1.8%, Ni: 3.0 to 8.5%, Cr: 12.0 to 20.0%, Mo: 0.1 to 2.5%, Mo: 0.1 to 2.5%, Cu: 1.0 to 5.0% and / or Ti + Al: 1.0 to 5.0%, Nb + Ta ⁇ 5 C or Nb ⁇ 5 C, N ⁇ 350 ppm; Remainder Fe and Impurities.
  • a sintered compact made from the steel powder should have a martensite content of 90% or more.
  • a steel for oil drilling applications is known from EP 2 832 881 A1, which has excellent high-temperature corrosion resistance and is said to stably achieve a strength of not less than 758 MPa.
  • the steel consists of, in mass%, C: ⁇ 0.05%, Si: ⁇ 1.0%, Mn: 0.01 - 1.0%, P: ⁇
  • JP 2015 147975 A also discloses a variant of a precipitation hardening stainless steel. This contains, in% by mass, 0.02
  • a high-strength martensitic stainless steel consists, in mass%, of 0.06% or less C, 12 to 16% Cr,
  • the steel has Al contents of less than 0.03 mass% in each case and has an area ratio of the delta ferrite Phase of at most 10% as well as fine copper precipitates that are dispersed in a matrix.
  • Mn ⁇ (N - 0, 0045) ⁇ 0.001
  • the structure of the tube mainly consists of a martensitic phase and 10 to 40% by volume of the structure of ferritic phase and up to 10% of the structure of retained austenite.
  • CN 107 385 144 A describes a process for producing a high-grade steel which belongs to the class of steels known under the designation 17-4PH. Typical representatives of this type are the steels that have been given the material numbers 1.4548 and 1.4542 in the StahlEisen list.
  • the structure of the steel contains a martensitic phase and a ferritic phase with a volume ratio of 10 to 40%, while the distribution ratio of the ferritic phase is higher than 85%.
  • EP 1 992709 A1 discloses a metal powder for use in an additive manufacturing process for producing three-dimensional objects, the powder being solidified by means of a laser or electron beam or another heat source.
  • the particles of the powder contain, in% by mass, ⁇ 0.07% C, 14.00 - 15.50% Cr, 3.5 - 5.0%
  • the steel that meets this requirement consists of 0.02 (max. 0.04)% C, 0.01 (max. 0.02)% P, 0.4 (max. 0.6%) Si, 4.2 ⁇ 0.2% Ni, 3.6 ⁇ 0.2% Cu, 0.1 (max. 0.2)% Mn, 0.01% S, 14.3 ⁇ 0.2% Cr, 0 - 0.2% Mo, 0.3 ⁇ 0.02% Nb, 0.04 (max.0.08%) N, remainder Fe.
  • DE 10 2016 202 885 A1 discloses a steel powder with high S content for an additive manufacturing process, the particles of which consist of, in mass%, C: ⁇ 0.10%, Si: 2.0 - 9.0%, Mn: 0.05 - 6.0% , Cu: 0.5 - 4.0%, Ni: 1.0 - 24.0%, Cr: 6.0 - 28.0%, Mo: 0.2 - 4.0%,
  • Nb 0.03 - 2.0% and the remainder of Fe and unavoidable impurities.
  • the invention proposes a composition according to claim 1.
  • the invention therefore proposes a steel that consists of, in% by mass,
  • Cu 2.0 - 4.0%, optional Co: ⁇ 6.0%, Nb: 1.0 - 5.0%, optional W: 0.45 - 5.0%, where the sum of the Nb and W contents is at least 1.0% and at most 5%, optionally Mo: 0.25-6.0%, optionally AI: 0.25-6.0%, optionally Ti: 0.25 - 6.0%, the sum of the Al and Ti contents in the case of their presence being 0.25 - 6.0%,
  • the remainder consists of iron and impurities that are unavoidable due to production.
  • the alloy specification that the invention has provided for the steel according to the invention is coordinated in such a way that the possibility of effective precipitation hardening is opened up.
  • the steel according to the invention is composed in such a way that in cases in which particularly high hardnesses and strengths are required of those components made from the steel according to the invention, these hardnesses and strengths can be set by a heat treatment to which the steel component is subjected after its manufacture.
  • the steel according to the invention is here in the technical sense in particular free of C and / or free of N, in the sense that C and / or N are only present in the steel as unavoidable impurities and are not added to the alloy.
  • the coordination of the alloy components for precipitation hardening and in particular with the specific Cr content also provides good corrosion resistance even in the heat-treated state, especially since setting of the Cr content is essentially avoided.
  • a method according to the invention for producing a steel component consequently comprises the following work steps: a) Providing a steel material consisting of, in mass%,
  • Nb 1.0 - 5.0%
  • W 0.45 - 5.0%
  • Mo 0.25 - 6.0%
  • AI 0.25-6.0%
  • Ti 0.25-6.0%
  • the sum of the contents of AI and Ti in the case of their presence being 0.25-6.0% amounts to
  • carbon is not added in a targeted manner in the steel according to the invention, but can be present as an impurity in contents of up to 0.02% by mass.
  • carbon is inevitably introduced into the metallurgical process as an impurity via other alloying elements Content limited according to the invention to a maximum of 0.02 mass% in order to prevent the formation of Cr-containing carbides as precipitates and an associated reduction in corrosion resistance.
  • silicon "Si" can be used for deoxidation during the melting of starting materials and can be provided for this purpose in the levels customary in the prior art.
  • the presence of silicon can lower the melting temperature and reduce the viscosity of the melt. This results in a simplified production of components from the steel.
  • a targeted addition for this purpose to a content of at least 0.3 mass% Si can therefore be advantageous.
  • ferrite is stabilized in the structure, which is why the Si content is limited to a maximum of 1.0% by mass, in particular less than 1.0% by mass or at most 0.8% by mass.
  • Manganese "Mn” is provided in the steel according to the invention with a maximum content of 2.0% by mass, in particular less than 2.0% by mass.
  • Mn binds sulfur by forming MnS.
  • the dissolved fraction of Mn helps stabilize austenite, which means that the fraction of ⁇ -ferrite in the structure can be reduced.
  • an Mn content of at least 0.1% by mass, in particular at least 0.3% by mass or at least 0.5% by mass can be provided.
  • the Mn content is limited to a maximum of 2.0 mass% in order to prevent undesired stabilization of retained austenite. Negative influences of the presence of Mn can be further reduced by limiting the Mn content to less than 2.0 mass%, in particular at most 1.0 mass% or at most 0.8 mass%.
  • Chromium "Cr” is required in the steel according to the invention in order to provide corrosion resistance for components made from the steel.
  • a Cr content of at least 14.0% by mass is provided in order to achieve the high corrosion resistance required for the respective application. So that this effect is reliably achieved, the Cr content can be increased to at least 14.5% by mass, in particular to at least 15.0% by mass.
  • excessively high Cr contents also stabilize the ferritic structure and thus increase the proportion of remaining ⁇ -ferrite in the steel matrix, so that Cr contents above 18.0% by mass should be avoided.
  • the Cr content can be 14.50-18.0 mass%, in particular 15.00-17.50 mass -%.
  • Nickel “Ni” is present in the steel according to the invention, among other things, in order to ensure the hardenability of the steel which is necessary for the strength required in each case. Furthermore, Ni can increase the corrosion resistance and bring about an increase in toughness.
  • the improvement in hardenability through the contribution of Ni is due both to the stabilization of the austenite during solution annealing, which enables diffusion-free lattice folding during quenching, and to the formation of intermetallic phases during precipitation hardening such as, for example, intermetallic phases of the Ni 3 Ti and type Ni 3 AI. Nickel effectively stabilizes the austenitic phase and thus reduces the proportion of ⁇ -ferrite in the structure of a component made from steel.
  • a minimum Ni content of 3.0% by mass is therefore provided, with Ni contents of at least 3.5% by mass, in particular more than 3.5% by mass, having proven to be particularly favorable.
  • the positive influences of Ni can be used advantageously up to a content of 6.0 mass% Ni, with contents of up to 5.5 mass%, in particular less than 5.5 mass% or up to 5.0 % By mass, prove to be particularly advantageous in practice. If the Ni content is less than 5.0% by mass, the ferrite content in the structure can be further reduced without significantly reducing the hardenability of the steel.
  • Copper “Cu” is present in the steel according to the invention in a content of at least 2.0% by mass as a mandatory element in order to support precipitation hardening. Copper can accelerate precipitation hardening, especially since copper can serve as a nucleus for the precipitation of intermetallic phases. Furthermore, copper phases such as ⁇ -Cu can be precipitated, which themselves contribute to the increase in hardness. By providing a minimum Cu content of 2.5 mass%, the effect of Cu on precipitation hardening can be enhanced. At the same time, however, too high a Cu content would stabilize the austenitic phase and could cause retained austenite to remain. To avoid this, the Cu content is limited to a maximum of 4.0% by mass. Adverse effects of the presence of Cu can thereby be avoided with particular certainty that the Cu content is at most 3.5% by mass.
  • Co is provided as an optional additional element in order, on the one hand, to obtain austenite stabilization and an associated reduction in the ⁇ -ferrite content.
  • Co can also contribute indirectly to the precipitation hardening in that the solubility of other alloying elements and in particular of Mo can be reduced, which promotes the formation of intermetallic phases.
  • at least 1.5% by mass of Co are provided in the steel according to the invention, this minimum content being combined in particular with the addition of Mo as an alloy. If the Co content exceeds 6% by mass, no further economically sensible increase in the positive effects of Co is achieved. In particular, the Co content is limited to less than 5.0 mass% for this purpose.
  • Nb, W, Mo, Al, Ti "provided, Nb of these elements being present as a mandatory component.
  • the elements of the group” Nb, W, Mo, Al, Ti “contribute to precipitation hardening.
  • only Nb of the elements from the group "Nb, W, Mo, Al, Ti” is provided, ie only Nb is added, while the other elements of the group are present as unavoidable impurities.
  • Mo in particular can be provided as an additional element, Mo in particular also being able to be added in combination with Co.
  • two or more elements of the group “Nb, W, Mo, Al, Ti” can be present in combination in the alloy of a steel according to the invention.
  • Molybdenum “Mo” can optionally be present in the steel according to the invention in contents of up to 6.0% by mass in order to contribute to precipitation hardening through the precipitation of Mo-containing intermetallic phases such as Fe 2 Mo.
  • the Mo content can also promote the formation of other intermetallic phases.
  • a minimum content of 0.25% by mass can be provided in order to promote the precipitation of intermetallic phases.
  • the positive influences on the properties of the steel according to the invention can be used particularly reliably by reducing the Mo content to at least 1.0% by mass.
  • a minimum Mo content of more than 2.0% by mass can bring about a further improvement in precipitation hardening become.
  • increasing Mo contents can stabilize the ferrite in the structure, so that the upper limit of the Mo content of 6.0 mass% must be observed.
  • Optimal use of Mo can be achieved with Mo contents of at most 5.0 mass%, in particular at most 4.0 mass% or at most 3.5 mass%, with Mo contents of up to 3.0 Mass% have proven to be particularly effective.
  • Niobium "Nb” is added to the steel according to the invention in order to stabilize the steel structure by binding unavoidable carbon impurities.
  • the formation of niobium carbides prevents the precipitation of chromium carbides, which would be very detrimental to the corrosion resistance of components made from steel.
  • the Nb content can be based on the content of carbon impurities. For example, an Nb content corresponding to five times the C content can be provided in order to ensure that C is reliably set.
  • the invention also found that Nb also participates very effectively in precipitation hardening, so that a significantly higher Nb content can be set to improve the hardness that can be achieved; in one embodiment, Nb has contents of at least 1.0 mass- % intended to improve precipitation hardening.
  • Nb contents of more than 5.0% by mass there is no further increase in the positive effects of the presence of Nb. Rather, higher Nb contents can also promote the formation of ⁇ -ferrite.
  • the Nb content can be limited to a maximum of 3.0% by mass.
  • tungsten “W” can have a similar function to Nb and, from contents of 0.45% by mass, in particular at least 1.0% by mass, can lead to a significant improvement in precipitation hardening.
  • the W content is limited to a maximum of 5.0% by mass and in particular a maximum of 3.0% by mass, since higher contents would not lead to any further increase in hardness and at the same time the ⁇ -ferrite content could increase.
  • the contents of the elements Nb and W are interchangeable.
  • the effects of the elements Nb and W in the steel according to the invention can therefore be used particularly effectively if Nb and W are present at the same time in effective percentages by mass.
  • the sum of the contents of Nb and the optionally present W is accordingly 1.0-5.0% by mass, being 1.45-5.0% by mass in the case of the presence of W.
  • the total content of Nb and W can in particular be limited to a maximum of 3.0% by mass in order to use the effect of Nb and the optionally added W particularly effectively.
  • Aluminum “AI” can be used in the steel according to the invention in contents of
  • Al content is limited to a maximum of 6.0 mass%.
  • the Al content is limited to a maximum of 3.0% by mass, in particular a maximum of 2.0% by mass, adverse effects of the presence of Al in the steel according to the invention can be prevented particularly reliably.
  • Titanium "Ti” has a similar effect in the steel according to the invention . like aluminum and can be used to support precipitation hardening through the formation of intermetallic phases.
  • a minimum content of 0.25% by mass Ti, in particular 1.0% by mass Ti can be provided.
  • the Ti content is limited to a maximum of 6.0 mass%. Disadvantageous effects of the presence of Ti in the steel according to the invention can be avoided particularly reliably by reducing the Ti content to a maximum of 3.0% by mass, in particular a maximum of 2.0% by mass.
  • Al or Ti can each be present alone in the steel according to the invention. Due to their similar effect, however, Ti and Al are interchangeable with one another or complement one another, so that a combination of Al and Ti contents can also be provided. It has proven possible in principle for Al and Ti to be present in contents of 0.45-6.0 mass%. However, it proves to be particularly economical if the sum of the contents of Al and Ti is 0.45-6.0 mass%, in which case both elements are each in effective contents of, for example, at least 0.05 mass%, in particular at least 0.1 mass% or at least 0.2 mass%, and where the sum of the contents of Nb and W is 0.45 - 5.0 mass%, in particular 0.45 - 3.0 mass% or 1.0-3.0 mass%.
  • Sulfur "S” and phosphorus “P” are undesirable components in the steel according to the invention, but can get into the steel as unavoidable impurities due to the manufacturing process. Their contents must in any case be limited so that they have no influence on the properties of the steel according to the invention .
  • the invention provides for the S content and the P content to be limited to a maximum of 0.035% by mass in each case.
  • composition of a steel according to the invention which is not covered by the alloy elements explained above, is occupied by iron and the impurities unavoidable due to the production process, which also include the contents of S and P, in each case the contents of the impurities are in such a low range to keep that they have no influence with regard to the desired properties of the steel according to the invention and the components made from it.
  • the preparation of one component of the invention from the steel of this invention is made by a molding process, wherein this includes according to the understanding of the present invention casting process, methods of powder metallurgy, additive manufacturing processes, such as 3D-printing techniques, or any other method in which a molten or powdered steel material in a solid shape depicting the respective component is brought into being.
  • a steel assembled and provided according to the invention (step a) of the method according to the invention can be cast in step b) of the method according to the invention, for example, as molten steel to form a steel component or as steel powder or wire using powder metallurgy or additive manufacturing processes to form the respective steel component be shaped
  • a steel powder composed according to the invention can be produced in a conventional manner, for example by gas atomization or any other method suitable methods are carried out, a steel melt composed according to the invention being atomized into a steel powder, for example by gas or water atomization or a combination of these two atomization methods. If necessary, those powder particles obtained in this way are selected for further processing according to the invention by sieving which have a suitable grain size.
  • the steel component can then be produced by powder metallurgy, for example, by sintering and / or hot isostatic pressing (HIP) of the steel powder.
  • powder metallurgy for example, by sintering and / or hot isostatic pressing (HIP) of the steel powder.
  • HIP hot isostatic pressing
  • additive manufacturing is understood to mean manufacturing processes in which a material is added to produce a component. This is usually done in layers.
  • “Additive manufacturing processes”, which are often referred to as “generative processes” or also generally as “3D printing”, are in contrast to the classic subtractive manufacturing processes such as machining processes (e.g. milling, drilling and turning) , in which material is removed in order to give the component to be manufactured its shape.
  • the additive manufacturing principle makes it possible to manufacture geometrically complex structures that cannot be implemented or can only be implemented at great expense using conventional manufacturing processes, such as the machining processes, primary forming processes or forming processes already mentioned (see VDI status report "Additive Manufacturing Processes", September 2014, published by verierir Ingenieure eV, Department of Production Technology and Manufacturing Processes, www.vdi.de/statusadditiv).
  • additive processes can be carried out using laser radiation and selective laser melting and / or laser sintering.
  • the steel powder can also be selectively joined under the action of electrons in electron beam melting or sintering.
  • additive manufacturing methods include 3D printing, where a binding agent is applied to the powder via a print head, as well as laser deposition welding.
  • the steel component can also be shaped using suitable forming processes (e.g. rolling and forging) and / or material-removing processes such as machining processes (e.g. milling, drilling and turning). Shaping is carried out, in particular, at least partially before the heat treatment.
  • suitable forming processes e.g. rolling and forging
  • material-removing processes such as machining processes (e.g. milling, drilling and turning). Shaping is carried out, in particular, at least partially before the heat treatment.
  • the steel component can undergo a solution heat treatment (step c) of the method), in which the component is brought to a solution heat treatment temperature of 900-1200 ° C, in particular 1000-1100 ° C or 1020-1080 ° C, for example.
  • the component can be kept at these temperatures for a solution annealing period of 1-5 hours, the steel material typically being heated to the respective solution annealing temperature at heating rates of 1-20 K / min.
  • the steel component is quenched with known quenching agents, such as water, oil, polymers, emulsion or inert gas, with cooling rates of 1 - 200 K / min, in particular of at least 5 K / min or at least 20 K / min Can apply.
  • Cooling rates of 30-200 K / min have proven to be particularly advantageous for quenching.
  • the structure of the steel in the component can be adjusted with a transition to the austenitic phase and a diffusion-free lattice flap during quenching.
  • the further heat treatment of the steel component (step d) of the method) forms strength-increasing precipitates in the structure of the steel component, so that a hardening heat treatment is carried out and the hardness of the steel component is increased. This is possible in particular, as explained above, by coordinating the alloy components of the steel according to the invention.
  • the heat treatment (step d) of the method) is carried out in particular as artificial aging, in which, for example, the steel component over a period of 0.5-80 hours, in particular 2-10 hours, at a temperature of 400-700 ° C, in particular 450 - 550 ° C. Heating rates and / or cooling rates of 1-20 K / min, in particular 5-15 K / min, can be used, for example, in connection with the aging process.
  • the heat treatment (step d) of the method according to the invention can increase the hardness ⁇ HRC by at least 5 HRC, in particular at least 10 HRC or at least 13 HRC, with increases of at least 16 HRC even being achieved in practice. That is, the heat treatment carried out according to the invention makes it possible to obtain a component whose hardness after the heat treatment is higher by the amount ⁇ HRC than before the heat treatment.
  • ⁇ HRC is the difference between the hardness of the steel component after the heat treatment and the hardness of the steel component before the heat treatment, each specified in "HRC" (HRC hardness determined in accordance with the currently applicable DIN EN ISO 6508).
  • the heat treatment typically includes a solution heat treatment with subsequent aging.
  • the heat treatment is carried out at elevated temperatures until the specified increase in hardness is achieved.
  • the corresponding increases in hardness can be significantly higher than those obtained from standard materials with material number 1.4542
  • the hardness increases achieved are, in particular, due to the composition of the steel according to the invention.
  • components made from the steel according to the invention have good corrosion resistance due to the coordination of the alloy components.
  • the structure of the component produced according to the invention can be determined by setting the alloy of the steel according to the invention.
  • the structure here is predominantly martensitic.
  • the structural fraction of (residual) austenite in the steel component produced is preferably reduced to less than 20% by volume in order to obtain a martensitic structure that is as complete as possible.
  • melt S1 - S4 were melted, the composition of which is given in Table 1.
  • the composition of the melt S1 corresponds to the nominal composition of the standard material 1.4542 (17-4 PH) and serves as a comparative example.
  • Samples were produced from the melts S1-S4 by casting. All samples were first brought to a temperature of 1050 ° C. at a heating rate of 10 K / min and solution annealed at this temperature for 2 h in a vacuum. At the end of the solution heat treatment the Samples were quenched with nitrogen gas at a pressure of 3.5 bar, the cooling rates being in a range of 30 - 50 K / min.
  • the samples were brought to 480 ° C at a heating rate of 10 K / min and aged at this temperature for 5 h to form strength-increasing precipitates in the structure of the steel. After the holding time, the samples were cooled at a cooling rate of 10 K / min.
  • the samples made of the steel according to the invention corresponding to the melts S2 to S4, allow a very large increase in hardness through a heat treatment, in particular due to the composition of the alloy with the specific contents of the elements from the group "Nb, W, Mo , AI, Ti ".
  • the samples according to the invention show significant increases in hardness, in particular due to the additional content of Mo, which contributes to the formation of intermetallic phases.
  • Samples S2, S3 and S4 also show that a targeted increase in the Nb content contributes to the increase in hardness.
  • an increase in hardness of ⁇ HRC 16 HRC occurred.
  • a final hardness of at least 40 HRC is achieved for all samples according to the invention.
  • the samples made from the steel S2, S3 and S4 according to the invention also have high corrosion resistance and are therefore advantageous for use in medical technology or in aerospace.
  • the steel according to the invention is also particularly suitable for powder-metallurgical processing, in particular by means of additive manufacturing.

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

Abstract

Selon l'invention, un acier, qui est caractérisé par une dureté et une résistance élevées ainsi que par une bonne résistance à la corrosion, est constitué des éléments suivants en pourcentage en masse : C : < 0,02 %, Si : < 2,0 %, Mn : < 2,0 %, Cr : de 14,0 à 18,0 %, Ni : de 3,0 à 6,0 % ; Cu : de 2,0 à 4,0 %, éventuellement Co : < 6,0 %, Nb : de 1,0 à 5,0 %, éventuellement W : de 0,45 à 5,0 %, la somme des concentrations de Nb et W étant d'au moins 1,0 % et d'au plus 5 %, éventuellement Mo : de 0,25 à 6,0 %, éventuellement Al : de 0,25 à 6,0 %, éventuellement Ti : de 0,25 à 6,0 %, la somme des concentrations d'Al et de Ti, s'ils sont présents, étant de 0,25 à 6,0 %, P : < 0,035 %, S : < 0,035 %, le reste étant du fer et des impuretés inévitables. L'invention se rapporte en outre à un procédé de production d'un composant, ledit procédé étant basé sur un acier de ce type, à un composant produit à partir de l'acier selon l'invention et à des utilisations avantageuses de l'acier.
PCT/EP2020/080438 2019-10-31 2020-10-29 Acier résistant à la corrosion et à durcissement par précipitation, procédé de production d'un composant d'acier, et composant d'acier WO2021084025A1 (fr)

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EP20796826.4A EP3850114A1 (fr) 2019-10-31 2020-10-29 Acier résistant à la corrosion et à durcissement par précipitation, procédé de production d'un composant d'acier, et composant d'acier

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EP19206615.7 2019-10-31
EP19206615 2019-10-31

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113828801A (zh) * 2021-09-23 2021-12-24 中南大学 一种电弧增材与深冷轧制成形复合制造装置和方法
CN114150232A (zh) * 2021-11-25 2022-03-08 香港理工大学深圳研究院 一种共格和非共格纳米相复合强化的超高强度马氏体时效钢及其制造方法
CN114855092A (zh) * 2022-07-05 2022-08-05 北京科技大学 一种增材制造高强韧不锈钢及其制备工艺

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WO1997040204A1 (fr) 1996-04-24 1997-10-30 J&L Fiber Services, Inc. Alliage d'acier inoxydable pour disque de raffineur de pate a papier
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CN107385144A (zh) 2017-05-25 2017-11-24 中原特钢股份有限公司 沉淀硬化马氏体不锈钢17‑4ph冶炼工艺
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EP0649915A1 (fr) 1993-10-22 1995-04-26 Nkk Corporation Acier inoxydable martensitique à haute résistance, et procédé pour sa fabrication
WO1997040204A1 (fr) 1996-04-24 1997-10-30 J&L Fiber Services, Inc. Alliage d'acier inoxydable pour disque de raffineur de pate a papier
WO2000053821A1 (fr) 1999-03-08 2000-09-14 Crs Holdings, Inc. Acier inoxydable durcissable par precipitation a usinabilite amelioree, destine a etre utilise dans des conditions extremes
EP2145970A1 (fr) 2007-03-22 2010-01-20 Hitachi Metals, Ltd. Acier inoxydable moulé martensitique durci par précipitation ayant une excellente aptitude à l'usinage et son procédé de fabrication
EP1992709A1 (fr) 2007-05-14 2008-11-19 EOS GmbH Electro Optical Systems Poudre métallique à utiliser avec un procédé additif pour la production d'objets en trois dimensions et procédé utilisant une telle poudre métallique
EP2341161A1 (fr) 2008-10-30 2011-07-06 Sumitomo Metal Industries Limited Tuyau en acier inoxydable à haute limite élastique présentant une résistance élevée à la corrosion fissurante en présence d'hydrogène sulfuré et une résistance à la corrosion en présence de dioxyde de carbone à haute température
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EP2832881A1 (fr) 2012-03-26 2015-02-04 Nippon Steel & Sumitomo Metal Corporation Acier inoxydable pour puits de pétrole et tuyau en acier inoxydable pour puits de pétrole
EP2918697A1 (fr) 2012-12-21 2015-09-16 JFE Steel Corporation Tuyau sans soudure en acier inoxydable hautement résistant pour puits de pétrole, et procédé de fabrication de celui-ci
JP2015147975A (ja) 2014-02-06 2015-08-20 大同特殊鋼株式会社 析出硬化型ステンレス鋼及びセンサー用部品
EP3117934A1 (fr) 2014-03-14 2017-01-18 Sanyo Special Steel Co., Ltd. Poudre d'acier inoxydable à durcissement par précipitation et pastille frittée de celle-ci
DE102016202885A1 (de) 2015-02-27 2016-09-01 Japan Silicolloy Industry Co., Ltd. Selektives Laserinterverfahren, Wärmebehandlungsverfahren, Metallpulver, und geformtes Produkt
EP3385403A1 (fr) 2016-02-08 2018-10-10 JFE Steel Corporation Tube sans soudure en acier inoxydable à haute résistance pour puits de pétrole et procédé pour le fabriquer
WO2017198530A1 (fr) 2016-05-19 2017-11-23 Böhler Edelstahl GmbH & Co KG Procédé de fabrication d'un matériau acier et matériau acier
CN107385144A (zh) 2017-05-25 2017-11-24 中原特钢股份有限公司 沉淀硬化马氏体不锈钢17‑4ph冶炼工艺

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113828801A (zh) * 2021-09-23 2021-12-24 中南大学 一种电弧增材与深冷轧制成形复合制造装置和方法
CN113828801B (zh) * 2021-09-23 2022-04-22 中南大学 一种电弧增材与深冷轧制成形复合制造装置和方法
CN114150232A (zh) * 2021-11-25 2022-03-08 香港理工大学深圳研究院 一种共格和非共格纳米相复合强化的超高强度马氏体时效钢及其制造方法
CN114150232B (zh) * 2021-11-25 2022-11-29 香港理工大学深圳研究院 一种共格和非共格纳米相复合强化的超高强度马氏体时效钢及其制造方法
CN114855092A (zh) * 2022-07-05 2022-08-05 北京科技大学 一种增材制造高强韧不锈钢及其制备工艺

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