US20200009651A1 - Use of a Steel for an Additive Manufacturing Process, Method for Producing a Steel Component and Steel Component - Google Patents

Use of a Steel for an Additive Manufacturing Process, Method for Producing a Steel Component and Steel Component Download PDF

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Publication number
US20200009651A1
US20200009651A1 US16/456,117 US201916456117A US2020009651A1 US 20200009651 A1 US20200009651 A1 US 20200009651A1 US 201916456117 A US201916456117 A US 201916456117A US 2020009651 A1 US2020009651 A1 US 2020009651A1
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steel
content
component
steel powder
powder
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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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    • B22F1/0011—
    • 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
    • B22F1/0085—
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/05—Metallic powder characterised by the size or surface area of the particles
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • B22F1/142—Thermal or thermo-mechanical treatment
    • 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
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • 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
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
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    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/66—Treatment of workpieces or articles after build-up by mechanical means
    • B22F3/1055—
    • 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
    • B22F8/00—Manufacture of articles from scrap or waste metal particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y80/00—Products made by additive manufacturing
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • 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
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F2009/001—Making metallic powder or suspensions thereof from scrap particles
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/05—Light metals
    • B22F2301/052—Aluminium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
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    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/05—Light metals
    • B22F2301/058—Magnesium
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/10—Copper
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/15—Nickel or cobalt
    • B22F2301/155—Rare Earth - Co or -Ni intermetallic alloys
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • 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

  • the invention relates to the use of a steel as a steel powder for producing steel components by additive manufacturing processes, a method for producing a steel component using an additive manufacturing process and a steel component produced through the use of such a steel by using an additive manufacturing process.
  • additive manufacturing process here summarises all manufacturing processes in which a material is added to produce a component. This addition usually takes place in layers. “Additive manufacturing processes”, which are often referred to in the technical language as “generative processes” or generally as “3D printing”, thus stand in contrast to the classic subtractive manufacturing processes, such as the machining processes (for example, milling, drilling, and turning), in which material is removed in order to give shape to the component to be produced. Likewise, additive processes generally differ from conventional solid forming processes, such as forging and the like, in which the respective steel part is formed while retaining the mass of a starting or intermediate product.
  • the components produced by such additive processes are regularly subjected to an after-treatment in order to minimise the residual porosity which is usually still present in the production process.
  • the options available for this purpose are adequately described in the prior art and summarised, for example, in DE 100 39 143 C1.
  • the subject matter of this patent specification is a method for producing precision components by laser sintering of a powder material which comprises a mixture of at least two powder elements.
  • the powder material is formed by the main component, this being iron powder, and other powder alloying elements which are in elemental, pre-alloyed or partially pre-alloyed form.
  • the laser sintering process is controlled in such a way that a powder alloy is formed from the constituents of the powder in the course of the laser sintering process.
  • the powder alloy elements are carbon, silicon, copper, tin, nickel, molybdenum, manganese, chromium, cobalt, tungsten, vanadium, titanium, phosphorus, boron.
  • the content ranges indicated for these components are: C: 0.01-2 wt %, Si: up to 1 wt %, Cu: up to 10 wt %, Sn up to 2 wt %, Ni: up to 10 wt %, Mo: up to 6 wt. %, Mn: up to 2 wt. % or 10-13 wt. %, Cr: up to 5 wt. % or 12-18 wt.
  • Co up to 2 wt %
  • W up to 5 wt %
  • V up to 1 wt %
  • Ti up to 0.5 wt %
  • P up to 1 wt %
  • B up to 1 wt %.
  • a component is also to be specified which consists of steel and can be produced cost-effectively using an additive process.
  • the invention is based on the recognition that a modification of a steel, which is generally already known from EP 3 168 312 A1 for the production of components using forging technology, is also especially suitable as a material for the production of steel components by using an additive manufacturing process.
  • the soft martensitic steels commonly used today for additive manufacturing require high proportions of expensive alloy elements such as Co, Ni and Mo and a subsequent heat treatment to set the degree of hardness.
  • the solutions known from practical experience which are based on steel with an austenitic structure are severely limited in terms of the maximum strength that can be achieved.
  • the invention proposes, in contrast, a material composition for use as a powder for the production of a steel component by additive manufacturing, in which, by a plurality of repetitions of the steps “applying a layer of steel powder to a previously produced steel layer”, “melting the applied steel powder layer”, “cooling the steel layer produced by melting”, the steel component is successively built from a corresponding number of steel layers.
  • This material composition opens a large window for the cooling rate to set a bainitic structure which is less solid than martensite.
  • FIG. 1 shows the TTT diagram of the steel S1 used as steel powder for additive manufacturing.
  • FIG. 2 shows the TTT diagram of the steel S2 used as steel powder for additive manufacturing.
  • a steel in the form of steel powder having a mean grain diameter of 5-150 ⁇ m is used for the production of steel components in an additive process, the steel comprising (in wt %): 0.08-0.35% C, up to 0.80% Si, 0.20-2.00% Mn, up to 4.00% Cr, 0.3-3.0% Mo, 0.004-0.020% N, 0.004-0.050% Al, up to 0.0025% B, at least one element from the group “Nb, Ti, V, S”, with the proviso that the Nb content is 0.003-0.20 wt %, the Ti content is 0.001-0.02 wt %, the V content is 0.02-0.40 wt % and/or the S content is 0.001-0.4 wt %, up to 1.5% Ni, up to 0.3% Cu, up to 2.0% Co, and the remainder being iron and unavoidable impurities, the Al content % Al, the Nb content % Nb, the Ti content % Ti, the V content
  • the unavoidable impurities due to production include all elements which are present in quantities which are ineffective in terms of alloying in respect of the properties of interest here and which enter the steel because of the selected route for producing the steel powder or the selected starting material (scrap).
  • the unavoidable impurities also include P contents of up to 0.0035 wt %.
  • the steel alloy used according to the invention as a powder for additive manufacturing is composed in such a way that there are yield strength-enhancing precipitates of carbides, such as special carbides, carbonitrides or nitrides, as a result of the intrinsic heat treatment required by the additive manufacturing due to heat conduction, said heat treatment resulting from the melting in layers of successively applied and melted powder layers.
  • carbides such as special carbides, carbonitrides or nitrides
  • the steel to be used according to the invention forms a homogeneous bainitic structure which, despite the omission of a separate heat treatment, ensures uniform properties over the volume of the additive-manufactured component.
  • the homogeneous structural state made possible by the steel alloy to be used according to the invention ensures low residual stresses and thus a low risk of cracking.
  • the steel alloy selected according to the invention for use as steel powder for an additive manufacturing process is also particularly suitable insofar as it minimises the critical cooling rate for the formation of the bainitic structure.
  • the “bainitic nose B” obtained in the time-temperature diagram (see FIGS. 1 and 2 ) for the steel to be used according to the invention is shifted towards short cooling times, as are typical for additive manufacturing.
  • alloying the steel to be used according to the invention ensures that, in the course of cooling, no amounts of martensite or ferrite or perlite influencing its properties are formed in the structure.
  • a steel component produced from steel to be used according to the invention is therefore characterised in that it contains at least 80 vol % bainite, wherein the content of non-bainitic structural constituents in steel components produced according to the invention typically is minimised to such an extent that after completion of the additive manufacturing a completely bainitic structure, in the technical sense, is present in the steel component.
  • the steel used according to the invention as steel powder for additive manufacturing may contain up to 0.35 wt % carbon (“C”) to contribute to increasing the strength of the material by carbide formation.
  • C carbon
  • the steel used according to the invention may contain up to 0.35 wt % carbon (“C”) to contribute to increasing the strength of the material by carbide formation.
  • C carbon
  • a respective increase in strength of approximately 70 MPa can be effected.
  • This effect succeeds from a C content of 0.08 wt %, in particular from a content of at least 0.09 wt % C.
  • Limiting the C content to at most 0.35 wt % ensures that a steel to be used according to the invention has good elongation and toughness properties despite its maximised strength.
  • the comparatively 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 undesired structural constituents is avoided.
  • An optimised 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 0.08-0.25 wt %, in particular 0.09-0.25 wt %.
  • Si Silicon
  • the Si content of a steel to be used according to the invention is therefore limited to at most 0.80 wt %, in particular to at most 0.45 wt %, in order to allow the bainite transformation to take place as early as possible.
  • Si contents up to this upper limit increase the strength due to solid solution strengthening.
  • Molybdenum (“Mo”) is present in the steel to be used according to the invention at contents of 0.3-3.0 wt % to delay the transformation of the structure into ferrite or perlite. This effect occurs in particular when at least 0.6 wt %, in particular more than 0.70 wt % Mo, are present in the steel. At contents of more than 3.0 wt %, in the steel to be used according to the invention there is no economically justifiable further increase in the positive effect of Mo. In addition, above 3.0 wt % Mo, there is a risk of forming a molybdenum-rich carbide phase which may adversely affect the toughness properties.
  • Mo content is at least 0.7 wt %.
  • Manganese (“Mn”) is present at contents of 0.20-2.00 wt % in the steel to be used according to the invention to adjust the tensile strength and yield strength by mixed crystal formation.
  • a minimum content of 0.20 wt % of Mn is required in order to increase the strength. If this effect is to be achieved particularly reliably, then a Mn content of at least 0.35 wt % can be provided. Excessively high Mn contents, however, would delay the bainite transformation and thus lead to a predominantly martensitic transformation. Therefore, the Mn content is limited to at most 2.00 wt %, in particular at most 1.5 wt %. Negative influences of the presence of Mn can be avoided particularly reliably by limiting the Mn content in the steel to be used according to the invention to a maximum of 1.1 wt %.
  • the content of sulphur (“S”) in the steel to be used according to the invention can be up to 0.4 wt %, in particular at most 0.1 wt %, in order to promote the machinability of the steel.
  • S sulphur
  • an S-content of at least 0.001 wt % may be provided.
  • Optimum effects of the presence of S in the steel to be used according to the invention can be achieved at contents of 0.003-0.1 wt %.
  • the fine adjustment of alloying techniques with regard to the mechanical properties and the structure quality of a steel to be used according to the invention is carried out in accordance with the alloying concept to be used according to the invention through a combined microalloying of the elements boron (“B”) in optional contents of up to 0.0025 wt %, in particular at least 0.0005 wt % B, nitrogen (“N”) in contents of 0.004-0.020 wt %, in particular at least 0.006 wt % N or up to 0.0150 wt % N, aluminium (“Al”) in contents of 0.004-0.050 wt % and niobium (“Nb”) in optional contents of up to 0.20 wt %, in particular at least 0.003 wt % or at least 0.005 wt % Nb, wherein the Nb content may in particular also be limited to at most 0.05 wt % Nb, titanium (“Ti”) in optional contents of up to 0.02 wt %, in particular at
  • N in the contents provided according to the invention allows formation of nitrides and carbonitrides to increase the strength and raise the fine grain resistance, without causing embrittlement.
  • Al forms aluminium nitride with N, which contributes to fine grain stability.
  • B delays the formation of ferrite or perlite and thus ensures the formation of the desired bainitic structure in the steel to be used according to the invention.
  • B contents above 0.0025 wt % would entail the risk of embrittlement.
  • the respective micro-alloying elements Nb, Ti and V, which are also optionally present, form carbonitrides and can thus make a significant contribution to optimising the fine grain stability and strength of the steel to be used according to the invention.
  • the micro-alloying elements V, Ti, Nb on the one hand and Al on the other hand may be present respectively in combination with one or more elements from the group “Al, V, Ti, Nb” or alone in amounts above said minimum contents.
  • the nitrogen contained in the steel to be used according to the invention is bound completely via the respectively present contents of Al as well as any additionally added contents of Nb, Ti and V, and boron can thus delay transformation.
  • the binding of N according to the invention makes it possible for the optionally present boron to act as a dissolved element in the matrix of the steel and to suppress the formation of ferrite and/or perlite.
  • Cr chromium
  • at least 0.5 wt % or at least 0.8 wt % of Cr may be provided for this purpose.
  • Cr contents above 4.00 wt % would promote undesirable martensite formation in the structure of the steel to be used according to the invention.
  • Ni contents of up to 1.5 wt % which are also optionally present improve the toughness of the steel to be used according to the invention. If this effect is to be utilised, it occurs from a Ni content of at least 0.1 wt %, in particular at least 0.15 wt %.
  • the alloying elements occurring or deliberately added via the starting material into the steel to be used according to the invention include Cu, whose content is limited to max. 0.3 wt %, in particular less than 0.3 wt %, to avoid negative influences in the steel to be used according to the invention.
  • cobalt optionally present in the steel to be used according to the invention causes a shift in bainite formation to shorter times.
  • the positive influence of Co can be utilised in particular at Co contents of at least 0.1 wt %, in particular at least 0.5 wt %.
  • a method according to the invention for producing a steel component comprises the following steps:
  • the manufacture of the steel powder consisting of steel to be used according to the invention can be carried out in a conventional manner, for example by gas atomisation or by any other suitable method.
  • a steel melt melted according to the invention can be atomised into the steel powder, for example by gas or water atomisation or a combination of these two atomisation methods.
  • the powder particles obtained in this manner can be sieved in order to select those having a suitable grain size for further processing according to the invention.
  • grains having an average diameter of 5-150 ⁇ m have proven to be suitable for the purposes of the invention.
  • a component produced according to the invention is characterised in that it has a structure comprising at least 80 vol % bainite, in particular a completely bainitic structure in the technical sense.
  • the steel powder to be used according to the invention is suitable for any additive manufacturing process of the type known from the prior art and explained at the outset, in which the adjoining particles collected by the heat supplied are fused by local heat input, and thus the steel powder portion treated in this way is solidified during the subsequent cooling in the respective section to be formed of the component to be produced.
  • the known laser melting and laser sintering processes which permit a precisely limited, intensive heating of the steel powder particles and a correspondingly accurate formation of the component to be produced, are suitable for the production of a component according to the invention.
  • the strength and ductility of a steel component produced according to the invention can be set via a conventional heat treatment.
  • This heat treatment may comprise a fine adjustment of the bainitic structure of the steel component produced according to the invention, in which the steel component is heated to an austenitising temperature above the Ac3 temperature and then cooled from the austenitising temperature in air or in oil, the cooling being carried out at a cooling rate of at least 0.5 K/s and less than 300 K/s, in particular 3.0-300 K/s, which is sufficient for setting the bainitic structure, which should be as complete as possible.
  • the steel to be used according to the invention has a B content of 0.0005-0.0025 wt %. The presence of such B contents is particularly effective here in preventing the formation of undesirable ferrite or perlite in the structure of the steel component in the course of the cooling.
  • a tempering treatment may be carried out, in which the steel component is held at a temperature of 450-600° C. over a period of 0.5-6 hours, wherein the specifically provided duration of the tempering treatment can be chosen depending on the size and volume of the steel component, in order to again support, in a targeted manner, the previously mentioned strength increase due to special carbide formation, said strength increase already being obtained in the course of the additive manufacturing.
  • Steel components produced according to the invention after completion of the additive manufacturing (step d), i.e. before step e), already have a tensile strength of at least 900 MPa, in particular at least 1145 MPa, a yield strength of at least 560 MPa, in particular at least 675 MPa, and an elongation at break A5.65 of at least 8%.
  • the mechanical properties of a steel component according to the invention can be improved to such an extent that its tensile strength is at least 1050 MPa, in particular at least 1230 MPa, its yield strength is at least 615 MPa, in particular at least 750 MPa, and its elongation at break A5.65 is at least 8%.
  • melts S1, S2, S3 according to the invention were melted and respectively atomised in a conventional manner in the gas flow into steel powder having a grain size of 5-150 ⁇ m.
  • the composition of melts S1-S3 is given in Table 1.
  • steel components were produced using “Selective Laser Melting” (“3D printing/SLM method”), which were test bodies for determining the optimal parameters for additive manufacturing, namely cubes with approx. 20 mm edge length, and blanks for tensile and impact tests.
  • 3D printing/SLM method Selective Laser Melting
  • the tensile strength Rm_V of the steel components obtained after the additive manufacturing is shown in Table 2.
  • the steel components thus obtained were subjected to a machining operation in order to optimally adapt them to their respectively required final shape.
  • the components each underwent a heat treatment in which they were aged for a period tA at a temperature TA.
  • the respective ageing time tA and ageing temperature TA are also listed in Table 2.
  • Table 2 indicates the tensile strength Rm_N which the components exhibited after mechanical processing and ageing.
  • Table 2 indicates the structure of the components.
US16/456,117 2018-07-05 2019-06-28 Use of a Steel for an Additive Manufacturing Process, Method for Producing a Steel Component and Steel Component Abandoned US20200009651A1 (en)

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CN111549275A (zh) * 2020-04-30 2020-08-18 中车工业研究院有限公司 一种车轴增材修复用铁基合金粉末及其制备方法和应用
CN111549341A (zh) * 2020-05-29 2020-08-18 精诚工科汽车系统有限公司 镍基激光熔覆粉末及其制备方法和用途
CN112719296A (zh) * 2020-12-29 2021-04-30 中国人民解放军陆军装甲兵学院 一种4Cr5MoSiV1合金钢力学性能调控方法
EP4180225A1 (de) * 2021-11-12 2023-05-17 SSAB Technology AB Stahlpulver zur verwendung in generativen fertigungsverfahren

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DE102020106517A1 (de) * 2020-03-10 2021-09-16 Universität Paderborn Isotropes, rissfreies Stahldesign mittels Additiver Fertigungsverfahren
CN112195412B (zh) * 2020-10-12 2021-12-24 马鞍山钢铁股份有限公司 一种大功率发动机曲轴用Nb-V微合金化高强韧性贝氏体非调质钢及其制备方法

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DE10039143C1 (de) 2000-08-07 2002-01-10 Fraunhofer Ges Forschung Verfahren zur Herstellung präziser Bauteile mittels Lasersintern und deren Nachbehandlung
PT3168312T (pt) 2015-11-16 2019-07-16 Deutsche Edelstahlwerke Specialty Steel Gmbh & Co Kg Aço estrutural de alta qualidade com estrutura bainítica, peça forjada e método para a produção de peça forjada
CN107214336B (zh) * 2017-06-16 2019-07-30 东北大学 一种利用激光选区熔化技术制备24CrNiMo贝氏体合金钢的方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111549275A (zh) * 2020-04-30 2020-08-18 中车工业研究院有限公司 一种车轴增材修复用铁基合金粉末及其制备方法和应用
CN111549341A (zh) * 2020-05-29 2020-08-18 精诚工科汽车系统有限公司 镍基激光熔覆粉末及其制备方法和用途
CN112719296A (zh) * 2020-12-29 2021-04-30 中国人民解放军陆军装甲兵学院 一种4Cr5MoSiV1合金钢力学性能调控方法
EP4180225A1 (de) * 2021-11-12 2023-05-17 SSAB Technology AB Stahlpulver zur verwendung in generativen fertigungsverfahren
WO2023083899A1 (en) * 2021-11-12 2023-05-19 Ssab Technology Ab Steel powder for use in additive manufacturing processes

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EP3591078A1 (de) 2020-01-08

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