EP3186405B1 - Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier - Google Patents

Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier Download PDF

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EP3186405B1
EP3186405B1 EP15756892.4A EP15756892A EP3186405B1 EP 3186405 B1 EP3186405 B1 EP 3186405B1 EP 15756892 A EP15756892 A EP 15756892A EP 3186405 B1 EP3186405 B1 EP 3186405B1
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Prior art keywords
steel
content
steel according
hardness
particles
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German (de)
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EP3186405A1 (fr
Inventor
Horst HILL
André VAN BENNEKOM
Oliver RIPKENS
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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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    • 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
    • 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
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
    • 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
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
    • 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
    • C22C38/50—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

Definitions

  • the invention relates to a steel for uses requiring high wear resistance, high hardness, good corrosion resistance and / or low thermal conductivity.
  • Steels with the above-mentioned property profile are particularly suitable for the production of cutting tools, perforated plates, sieves, molds and similar components for machines that are needed in the plastics processing industry.
  • a typical field of application here are machines for the regeneration or recycling of plastic products, which are melted down into a melt for their return to the processing cycle.
  • the melt is forced through a perforated plate, from which it emerges in a large number of single strands.
  • the single strands solidify and are then comminuted by means of suitable, near the perforated plate rotating blades to individual granules.
  • Both the cutters used to comminute the plastics and the perforated plates used to form the plastic strands to be comminuted by the knives must have good corrosion resistance due to the corrosive environment to which they are subjected in use and are subject to high abrasive wear.
  • the heat conductivity of the steel from which the perforated plate is made in each case should be low, so that the plastic melt coming into contact with the respective perforated plate does not extract too much heat and premature solidification of the melt occurs, especially for the application "perforated plate". which would lead to a blockage of the holes of the plate.
  • a known steel intended for this purpose is known under the material number 1.2379 (AISI designation: D2). It contains besides iron and unavoidable Impurities (in wt%) 1.55% C, 12.00% Cr, 0.80 Mo and 0.90% V.
  • Another steel also widely used in the field of plastic recycling, is standardized under material number 1.3343 (AISI designation: M2). It contains in addition to iron and unavoidable impurities (in% by weight) 0.85-0.9% C, 0.25% Mn, 4.1% Cr, 5.0% Mo, 1.9% V and 6, 4% W.
  • the highest demands on wear are to be met by the martensitic steel standardized under the material number 1.4110 (AISI designation: 440A), which in addition to iron and unavoidable impurities (in% by weight) 0.6 - 0.75% C, max. 1% Mn, max. 1% Si, max. 0.04% P, max. 0.03% S, 16 - 18% Cr and max. 0.75% Mo contains.
  • This steel achieves a hardness of at least 60 HRC after a suitable heat treatment.
  • a steel known under the trade designation "Ferro-Titanit Nikro 128" which has been specially created for the manufacture of components used in the processing of abrasive plastics, contains besides iron and unavoidable impurities (in% by weight) 13 , 5% Cr, 9% Co, 4% Ni and 5% Mo.
  • the proportion of titanium carbide in the structure of the composite steel is 30 wt .-%, which corresponds to a volume fraction of about 40 vol .-% TiC.
  • the well-known powder metallurgy produced steel achieved after over two to four hours under vacuum annealing at 850 ° C and a subsequent quenching, in which it is exposed to a nitrogen atmosphere with a pressure of 1 - 4.5 bar, an annealing hardness of about 53 HRC, which is followed by a curing treatment in which the steel is aged over six to eight hours at 480 ° C. , can be increased to a maximum hardness of about 62 HRC.
  • the object of the invention to provide a steel that can be produced on an industrial scale using conventional methods and has a profile optimized in terms of its properties. Likewise, practical uses of such a steel should be mentioned.
  • the invention provides a steel for applications requiring high wear resistance, high hardness, good corrosion resistance and / or low thermal conductivity.
  • the steel according to the invention achieves a hardness of at least 56 HRC in the cured state and contains in its structure a total of at least 30% by weight of hard phases present which, in addition to the TiC particles of carbide, Oxide or nitride particles exist.
  • the content of TiC particles is at least 20% by weight.
  • the hard phases are embedded in a matrix which comprises (in% by weight) 9.0 - 15.0% Cr, 5.0 - 9.0% Mo, 3.0 - 7.0% Ni, 6.0 - 11.0% Co, 0.3 - 1.5% Cu, 0.1 - 2.0% Ti, 0.1 - 2.0% Al,
  • a steel according to the invention is particularly suitable for the production of components for the regeneration and recycling of plastic products.
  • perforated plates in particular microgranulation perforated plates
  • knives for shredding plastic parts can be produced from steel according to the invention. Such knives become as above already explained, also required in the production of granules of molten plastic strands, as they are produced by means of perforated plates of the type described above in Granulier wisdomen.
  • a steel according to the invention contains at least 20% by weight of TiC embedded in a matrix which contributes to the hardenability of the steel by precipitation formation and which at the same time is chosen such that a low thermal conductivity of less than 35W / mK is guaranteed regardless of the respective heat treatment state.
  • the passive current density of the steel according to the invention is less than 5 ⁇ A / cm 2 , measured in oxygen-free 0.5 molar sulfuric acid with a potential change rate of 600 mV / h against a calomel reference electrode at 20 ° C.
  • Steel according to the invention therefore exhibits corrosion resistance with high hardness and optimized wear resistance, which is comparable to the corrosion resistance of conventional austenitic stainless steels.
  • the according to means of ultrasonic measurement as a function of sound propagation velocity determined modulus of elasticity of the invention steels is at a temperature of 20 ° C at more than 270 GPa, in particular more than 300 GPa, so that the steel according to the invention or components made therefrom also highest demands on their strength certainly fulfill.
  • the thermal expansion coefficient of steel according to the invention is in the temperature range from 20.degree. C. to 600.degree. C. at 7 ⁇ 10 -6 / K to 12 ⁇ 10 -6 / K, which is significant for applications for which the steels according to the invention are intended.
  • the steel according to the invention contains at least 20% by weight, corresponding to about 30% by volume of TiC, or at least 28% by weight of TiC, in particular at least 30% by weight of TiC.
  • the TiC content should not exceed an upper limit of 45% by weight. In this way it is possible to ensure that steel according to the invention can be reliably manufactured and further processed. Too high a hard phase content leads to increased hardness and wear resistance.
  • a steel according to the invention also contributes that According to the invention further hard phases are present in addition to the TiC particles in the steel matrix, so that the volume fraction of the hard phases in the structure of the steel is at least 30 wt .-% in total.
  • This can be done by separate addition of carbide, nitride or oxide particles in the production of the steel.
  • the elements (Ni, Al, Ti) forming the weight fractions of the precipitates can also be adjusted within the specifications according to the invention in such a way that a sufficient amount of hardness-increasing precipitates in the matrix reliably results in the work steps completed during the production of the steel forms.
  • the contents of Mo and Co are markedly increased in the steel according to the invention and the contents of Ni and Ti are markedly reduced.
  • the specifications for the Cu, Al, TiC and NbC contents of an alloy according to the invention have been varied compared to the known steel.
  • the precipitates that form in the steel matrix of the steel according to the invention are intermetallic precipitates, in whose formation above all the elements Ni, Al and Ti are involved. These elements form Ni 3 Al and Ni 3 Ti or mixed forms.
  • These intermetallic phases are present in the structure with grain sizes of the order of 10 nm and are not counted to the total hard phase content. Due to their small size they make compared to the coarse hard phase particles, as they are embedded according to the invention in the matrix of the steel according to the invention, no major contribution to the resistance to abrasive wear. However, the intermetallic precipitations cause an increase in the hardness and strength of the metal matrix and thus also contribute to the improvement of the service properties.
  • Chromium is present in the steel of the invention at levels of 9.0-15.0% by weight to ensure the required corrosion resistance. Optimally, the Cr content is 12.5-14.5 wt .-%.
  • Molybdenum is contained in the steel according to the invention in amounts of 5.0-9.0 wt .-%, on the one hand to ensure sufficient corrosion resistance, in particular with regard to pitting corrosion and on the other hand to support the formation of intermetallic phases, by the hardness of the steel matrix, in which the hard phases are embedded, is increased.
  • the Mo content of the steel according to the invention is 6.5-7.5% by weight.
  • Cobalt is contained in the steel according to the invention in contents of 6.0 - 11.0 wt .-%, in order to To increase martensite start temperature and on the other hand to reduce the solubility of Mo in the metal matrix.
  • the Mo contained in the steel matrix according to the invention can participate more intensively in the formation of intermetallic phases.
  • the Co content of the steel according to the invention is 8.0-10.0% by weight.
  • Copper is contained in the steel of the present invention at levels of 0.3-1.5 weight% to accelerate precipitation hardening.
  • the Cu content of the steel according to the invention is 0.5-1.0% by weight.
  • Nickel is present in the steel of the invention at levels of 3.0 to 7.0 weight percent. Nickel is needed in the steel matrix in sufficient quantity to stabilize the austenitic phase in solution annealing, which is typically done at about 850 ° C. This is especially important when the material according to the invention is quenched starting from the solution annealing temperature. Due to the presence of nickel, the austenite is stabilized to such an extent that martensite is safely formed during quenching. If too little nickel is present in the steel matrix provided according to the invention, this effect is not achieved with the necessary certainty. If, on the other hand, too much nickel is present in the steel matrix, no martensite forms, since the austenitic phase is then stable even at room temperature.
  • the second object of nickel in the steel according to the invention is precipitation hardening by formation of intermetallic phases with elements such as Al and Ti. Therefore, in the steel matrix of the invention Steel, the contents of Ni, Al and Ti coordinated so that on the one hand, the martensite is given and on the other the precipitation hardening is made possible. Optimally, the Ni content of the steel according to the invention is 4.5-5.5% by weight.
  • Titanium is present in the steel of the present invention at levels of 0.1-2.0 weight percent to permit precipitation hardening in combination with Ni as discussed above.
  • the Ti content of the steel according to the invention is 0.8 to 1.2% by weight.
  • aluminum is contained in the steel of the present invention at levels of 0.1-2.0% by weight to effect precipitation hardening in combination with Ni.
  • the Al content of the steel according to the invention is 1.0 to 1.4% by weight.
  • the steel according to the invention can be hardened with extremely low distortion, since titanium carbide has a low thermal expansion and no transformation.
  • the wear resistance of the steel according to the invention is increased.
  • the NbC particles have a lower thermal conductivity than TiC, which has a favorable effect on the service properties of the steel according to the invention.
  • TiC and NbC are isomorphic carbides and therefore miscible with each other. This leads to the formation of mixed carbides in diffusion reactions.
  • a change in the Valence electron concentration and thus the formation of vacancies in the interstitial carbon is reduced and the suitability for use improved. This effect is achieved by the presence of at least 2.0% by weight of NbC in the steel according to the invention. An optimal influence is obtained when the NbC content is 2.0-3.0% by weight.
  • the steel according to the invention By producing the steel according to the invention by powder metallurgy in a conventional manner, it is possible to ensure that its structure is free from segregations and fiber progressions.
  • the carbide, nitride and oxide particles used according to the invention as hard phases are already supplied as "finished" particles during powder metallurgical production.
  • both the sintering, as well as the HIP (hot isostatic pressing) route can be used.
  • supersolidus liquid phase sintering based on gas-atomized steel powder is also suitable for the production of steels according to the invention.
  • a description of the commonly used in the powder metallurgical production of steels of the type in question here applied steps can be found for example in Foller, M .; Meyer, H .; Lammer, A .: Wear and Corrosion of Ferro-Titanite and Competing Materials.
  • Tool steels in the next century Proceedings of the 5th International Conference on Tooling, September 29th - October 1st, University of Leoben, Austria, 1999, p.
  • the steel according to the invention can be subjected to a conventional heat treatment to set its mechanical properties, in which it is heated for 2-4 hours, then quenched under a nitrogen atmosphere pressurized from 1 to 4.5 bar and finally at 480 for 6 to 8 hours ° C is outsourced.
  • Steel according to the invention regularly has a hardness of more than 62 HRC after such a heat treatment.
  • the steel according to the invention has a hardness of more than 50 HRC.
  • composition of the steel V corresponded to the composition of the known under the name "Ferro-Titanit Nikro 128", for example, in the above-mentioned publication documented steel.
  • the completed in the powder metallurgical production of both steels E, V operations corresponded to the steps that are commonly used in the powder metallurgy production of steel "ferro-titanite Nikro 128 "are explained in the above-mentioned literature.
  • samples PE1, PV1 of steels E and V were subjected to heat treatment, which also corresponded to the standard heat treatment of Ferro-Titanit Nikro 128 steel.
  • the samples PE1 and PV1 were first held for a period of two to four hours in vacuo at a temperature of 850 ° C and then quenched under a pressure of 1 - 4.5 bar pressurized nitrogen atmosphere. This is followed by a curing treatment in which the samples PE1, PV1 have been stored at a temperature of 480 ° C. for six to eight hours each.
  • Fig. 1 shows a section of a scanning electron micrograph of a section of a sample PE1 of the thus standard heat-treated steel according to the invention E.
  • the metal matrix is visible through the bright areas, whereas the surrounded by the matrix TiC inclusions are shown dark.
  • the TiC content of the samples according to the invention PE1, PE2 was, as indicated in Table 1, each more than 30 wt .-%.
  • the density of the samples PE1, PE2 produced from the steel E according to the invention was 6.55 g / cm 3 , thus achieving the theoretical density. How out Fig. 1 shows that the structure has no residual porosity.
  • FIG Fig. 3 The result of a current density potential measurement carried out on samples PE1 produced from steel E according to the invention and samples PV1 produced from comparison steel V is shown in FIG Fig. 3 shown.
  • the current density potential curve determined for the samples PE1 is shown as a solid line and the current density potential curve determined for the samples PV1 is shown as a dashed line.
  • the current density potential curves were measured in oxygen-free 0.5 molar sulfuric acid with a potential change rate of 600 mV / h against a calomel reference electrode at 20 ° C.
  • the passive current densities determined for the samples according to the invention PE1 were in each case below 5 ⁇ A / cm 2 .
  • the E modulus has been determined by means of ultrasound as a function of the sound propagation speed to 318 GPa.
  • the modulus of elasticity of the conventional samples PV1 was 294 GPa.
  • Table 3 gives an overview of the thermal expansion of steel E. It was measured by means of a Bähr dilatometer in temperature steps of 100 ° C up to a maximum temperature of 600 ° C. It can be seen that the thermal expansion coefficient ⁇ th 6 / K is in this temperature range 7-12 10-.
  • Fig. 4 an example of the result of a dilatometer measurement on a sample PE1 produced from the steel according to the invention, which confirms this result.
  • Table 1 stolen Cr Not a word Ni Co Cu Ti al TiC NbC e 13.5 7.0 5.0 9.0 0.8 1.0 1.2 33 2.5 V 13.5 5.0 4.0 9.0 0.8 1.0 1.0 30 - Data in wt .-%, balance iron and unavoidable impurities sample average hardness HRC PE1 65 PV1 62 PE2 54 PV2 53 Temperature [° C] ⁇ th 100 8.4 200 8.7 300 9.0 400 9.2 500 9.4 600 9.7

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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)
  • Powder Metallurgy (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Claims (12)

  1. Acier destiné à des applications qui nécessitent une haute résistance à l'abrasion, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique,
    - étant précisé que l'acier, à l'état durci, présente une dureté d'au moins 56 HRc,
    - étant précisé que la structure de l'acier contient au moins 30 % en poids de phases dures composées, outre des particules de TiC, d'autres particules de carbure, d'oxyde ou de nitrure,
    - étant précisé que la teneur en particules de TiC atteint au moins 20 % en poids et qu'entre 2 et 4,5 % du poids est composé de particules de Nbc,
    et
    - étant précisé que les phases dures sont intégrées à une matrice qui est composée de (en % du poids)
    9,0 à 15,0 % de Cr,
    5,0 à 9,0 % de Mo,
    3,0 à 7,0 % de Ni,
    6,0 à 11,0 % de Co,
    0,3 à 1,5 % de Cu,
    0,1 à 2,0 % de Ti,
    0,1 à 2,0 % d'Al,
    et de fer pour le reste ainsi que d'inévitables impuretés.
  2. Acier conforme à la revendication 1,
    caractérisé en ce que sa teneur en Cr
    se situe entre 12,5 et 14,5 % en poids.
  3. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Mo se situe entre 6,5 et 7,5 % en poids.
  4. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Ni se situe entre 4,5 et 5,5 % en poids.
  5. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Co se situe entre 8 et 10 % en poids.
  6. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Cu se situe entre 0,5 et 1,0 % en poids.
  7. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Ti se situe entre 0,8 et 1,2 % en poids.
  8. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Al se situe entre 1,0 et 1,4 % en poids.
  9. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce que sa teneur en TiC s'élève au maximum à 45 % en poids.
  10. Acier conforme à l'une des revendications précédentes,
    caractérisé en ce qu'il est fabriqué par métallurgie des poudres.
  11. Utilisation d'un acier obtenu conformément à l'une des revendications précédentes aux fins de la fabrication de composants employés pour le recyclage ou la fabrication de produits en plastique.
  12. Utilisation conforme à la revendication 11, caractérisée en ce que les composants constituent un plateau perforé ou un couteau pour la fragmentation de pièces de plastique.
EP15756892.4A 2014-08-28 2015-08-26 Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier Active EP3186405B1 (fr)

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DE102014112374.3A DE102014112374A1 (de) 2014-08-28 2014-08-28 Stahl mit hoher Verschleißbeständigkeit, Härte und Korrosionsbeständigkeit sowie niedriger Wärmeleitfähigkeit und Verwendung eines solchen Stahls
PCT/EP2015/069477 WO2016030396A1 (fr) 2014-08-28 2015-08-26 Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier

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NL1043487B1 (en) * 2019-11-28 2021-08-31 Bosch Gmbh Robert Ring component of a drive belt for a continuously variable transmission
JP7287916B2 (ja) * 2020-03-12 2023-06-06 株式会社神戸製鋼所 積層造形物の製造方法、及び積層造形物
CN111455274A (zh) * 2020-04-08 2020-07-28 鞍钢股份有限公司 一种80Ksi级别9Cr火驱热采油井管及其制造方法
CN112251749B (zh) * 2020-10-23 2023-04-07 黑龙江科技大学 一种利用等离子熔覆制备定向阵列的陶瓷相增强高熵合金耐磨涂层的方法
WO2022102805A1 (fr) * 2020-11-10 2022-05-19 한국재료연구원 Matériau composite à base de fe renforcé par des particules de tic et procédé pour la préparation de celui-ci

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KR20170041276A (ko) 2017-04-14
JP6210502B1 (ja) 2017-10-11
BR112017002127A2 (pt) 2017-11-21
CN107075624A (zh) 2017-08-18
RU2674174C2 (ru) 2018-12-05
RU2017106319A (ru) 2018-08-28
WO2016030396A1 (fr) 2016-03-03
RU2017106319A3 (fr) 2018-08-28
US20180119257A1 (en) 2018-05-03
JP2017532434A (ja) 2017-11-02
DE102014112374A1 (de) 2016-03-03
EP3186405A1 (fr) 2017-07-05

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