EP3186405B1 - Steel with high wear resistance, hardness and corrosion resistance and low thermal conductivity, and use of such a steel - Google Patents

Steel with high wear resistance, hardness and corrosion resistance and low thermal conductivity, and use of such a steel Download PDF

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Publication number
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)
French (fr)
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EP3186405A1 (en
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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
    • 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
    • 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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Description

Die Erfindung betrifft einen Stahl für Verwendungen, die eine hohe Verschleißbeständigkeit, eine hohe Härte, eine gute Korrosionsbeständigkeit und/oder eine niedrige Wärmeleitfähigkeit erfordern.The invention relates to a steel for uses requiring high wear resistance, high hardness, good corrosion resistance and / or low thermal conductivity.

Wenn nachfolgend Gehaltsangaben von Stahllegierungen angegeben sind, so sind diese jeweils auf das Gewicht bezogen, soweit nicht ausdrücklich etwas anderes angegeben ist.If salary details of steel alloys are given below, these are each based on the weight, unless expressly stated otherwise.

Stähle mit dem voranstehend genannten Eigenschaftsprofil eignen sich insbesondere für die Herstellung von Schneidwerkzeugen, Lochplatten, Sieben, Formen und vergleichbaren Komponenten für Maschinen, die in der Kunststoff verarbeitenden Industrie benötigt werden.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.

Ein typisches Einsatzgebiet sind hier Maschinen für die Neuerzeugung oder das Recycling von Kunststoffprodukten, die für ihre Rückführung in den Verarbeitungskreislauf zu einer Schmelze eingeschmolzen werden. Um aus der Schmelze ein Granulat zu bilden, wird die Schmelze durch eine Lochplatte gedrückt, aus der sie in einer Vielzahl von Einzelsträngen austritt. Die Einzelstränge erstarren und werden dann mittels geeigneter, nahe der Lochplatte rotierender Messer zu einzelnen Granulatkörnern zerkleinert.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. To form a granulate from the melt, 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.

Um den Erstarrungsvorgang zu beschleunigen, kann das Auspressen der Kunststoffschmelze durch die Lochplatte und das Zerkleinern unter Wasser durchgeführt werden. Dieses Verfahren ist in der Kunststoffindustrie als "Unterwassergranulieren" bekannt.To accelerate the solidification process, the extrusion of the plastic melt through the perforated plate and the crushing can be carried out under water. This process is known in the plastics industry as "underwater granulation".

Sowohl die für das Zerkleinern der Kunststoffe eingesetzten Messer als auch die zum Formen der von den Messern zu zerkleinernden Kunststoffsträngen eingesetzten Lochplatten müssen aufgrund der korrosiven Umgebung, der sie im Einsatz ausgesetzt sind, eine gute Korrosionsbeständigkeit besitzen und sind dabei hohem abrasiven Verschleiß ausgesetzt. Gerade für die Anwendung "Lochplatte" soll gleichzeitig die Wärmeleitfähigkeit des Stahls, aus dem die Lochplatte jeweils hergestellt ist, niedrig sein, damit der mit der jeweiligen Lochplatte in Kontakt kommenden Kunststoffschmelze nicht zu viel Wärme entzogen und es zu einer vorschnellen Erstarrung der Schmelze kommt, die zu einer Verstopfung der Löcher der Platte führen würde. Diese Anforderung ergibt sich insbesondere dann, wenn es sich bei der Lochplatte um eine so genannte "Micro-Lochplatte" mit Lochdurchmessern von weniger als 1 mm handelt.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. At the same time, 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. This requirement arises in particular when the perforated plate is a so-called "micro-perforated plate" with hole diameters of less than 1 mm.

Ein für diese Zwecke vorgesehener bekannter Stahl ist unter der Werkstoffnummer 1.2379 (AISI-Bezeichnung: D2) bekannt. Er enthält neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) 1,55 % C, 12,00 % Cr, 0,80 Mo und 0,90 % V.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.

Ein anderer ebenfalls im Bereich des Kunststoff-Recyclings weit verbreiteter Stahl ist unter der Werkstoffnummer 1.3343 (AISI-Bezeichnung: M2) genormt. Er enthält neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) 0,85 - 0,9 % C, 0,25 % Mn, 4,1 % Cr, 5,0 % Mo, 1,9 % V und 6,4 % W.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.

Höchsten Verschleißanforderungen soll der unter der Werkstoffnummer 1.4110 (AISI-Bezeichnung: 440A) genormte martensitische Stahl standhalten, der neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) 0,6 - 0,75 % C, max. 1 % Mn, max. 1 % Si, max. 0,04 % P, max. 0,03 % S, 16 - 18 % Cr sowie max. 0,75 % Mo enthält. Dieser Stahl erreicht nach einer geeigneten Wärmebehandlung eine Härte von mindestens 60 HRC.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.

Ein unter der Handelsbezeichnung "Ferro-Titanit Nikro 128" bekannter Stahl, der speziell für die Herstellung von Komponenten, die bei der Verarbeitung von abrasiven Kunststoffen eingesetzt werden, geschaffen worden ist, enthält neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) 13,5 % Cr, 9 % Co, 4 % Ni und 5 % Mo. Der Anteil an Titancarbid im Gefüge des so zusammengesetzten Stahls beträgt 30 Gew.-%, was einem Volumenanteil von ca. 40 Vol.-% TiC entspricht.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.

Der bekannte pulvermetallurgisch hergestellte Stahl erreicht nach einer über zwei bis vier Stunden unter Vakuum durchgeführten Glühung bei 850 °C und einer anschließenden Abschreckung, bei der er einer Stickstoffatmosphäre mit einem Druck von 1 - 4,5 bar ausgesetzt wird, eine Glühhärte von ca. 53 HRC, die durch eine anschließende Aushärtbehandlung, bei der der Stahl über sechs bis acht Stunden bei 480 °C ausgelagert wird, auf eine Maximalhärte von ca. 62 HRC gesteigert werden kann. Aus diesem Stahl werden typischerweise Lochplatten, Granuliermesser, Spritzdüsen sowie Schnecken, Ringe und sonstige Presswerkzeuge für die Verarbeitung von abrasiv wirkenden Kunststoffen sowie Komponenten für Pumpen, Abfüllköpfe und Ringmesser hergestellt, die für Konserven-Abfüllmaschinen benötigt werden (s. Datenblatt "Ferro-Titanit Nikro 128", enthalten in der Broschüre "Ferro-Titanit - Die Härte aus Krefeld", 06/2001, veröffentlicht von der Deutsche Edelstahlwerke GmbH).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. From this steel are typically produced perforated plates, granulators, spray nozzles and screws, rings and other pressing tools for the processing of abrasive plastics and components for pumps, filling heads and ring knives, which are required for canning filling machines (see data sheet "Ferro-Titanit Nikro 128 ", contained in the brochure" Ferro-Titanit - Die hardness from Krefeld ", 06/2001, published by Deutsche Edelstahlwerke GmbH).

Von Horst Hill ist in seiner Dissertation " Neuartige Metallmatrixverbundwerkstoffe (MMC) zur Standzeiterhöhung verschleißbeanspruchter Werkzeuge in der polymerverarbeitenden Industrie", Bochum Univ. Diss. 2011, veröffentlicht beim Selbstverlag des Lehrstuhls Werkstofftechnik, Ruhr-Universität Bochum, ISBN 978-3-943063-08-0 , schließlich ein Stahl vorgeschlagen worden, der aus (in Gew.-%) 13,5 % Cr, 1,0 % Mo, 9,0 % Ni, 5,5 % Co, 1,0 % Cu, 2,0 % Ti und 1,25 % Al, Rest Eisen und unvermeidbare Verunreinigungen besteht. Der TiC-Anteil im Gefüge dieses Stahls liegt ebenfalls bei 30 Gew.-%. Zusätzlich sind im Gefüge jedoch 5 Gew.-% NbC als Hartphase vorhanden.By Horst Hill is in his dissertation " Novel metal matrix composites (MMC) for increasing the service life of tools subject to wear in the polymer processing industry ", Bochum Univ. Diss. 2011, published by the Department of Materials Science, Ruhr-University Bochum, ISBN 978-3-943063-08-0 Finally, a steel has been proposed which consists of (in wt%) 13.5% Cr, 1.0% Mo, 9.0% Ni, 5.5% Co, 1.0% Cu, 2.0% Ti and 1.25% Al, residual iron and unavoidable impurities. The TiC content in the microstructure of this steel is also 30% by weight. In addition, however, 5 wt .-% NbC are present in the microstructure as the hard phase.

Der derart zusammengesetzte Stahl ließ bei seiner Erzeugung im Labormaßstab auf vielversprechendes Potenzial hoffen. Allerdings erwies sich seine betriebssichere großtechnische Erzeugung als problematisch.The composite steel thus gave rise to promising potential in its laboratory scale production. However, his reliable large-scale production proved problematic.

Vor diesem Hintergrund bestand die Aufgabe der Erfindung darin, einen Stahl zu schaffen, der sich im industriellen Maßstab unter Anwendung konventioneller Verfahren erzeugen lässt und ein hinsichtlich seiner Eigenschaften optimiertes Profil aufweist. Ebenso sollten praxisgerechte Verwendungen eines solchen Stahls genannt werden.Against this background, 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.

In Bezug auf den Stahl ist diese Aufgabe dadurch gelöst worden, dass ein solcher Stahl erfindungsgemäß die in Anspruch 1 angegebenen Merkmale besitzt.With respect to the steel, this object has been achieved in that such a steel according to the invention has the features specified in claim 1.

Vorteilhafte Ausgestaltungen der Erfindung sind in den abhängigen Ansprüchen angegeben und werden nachfolgend wie der allgemeine Erfindungsgedanke im Einzelnen erläutert.Advantageous embodiments of the invention are specified in the dependent claims and are explained below as the general inventive concept in detail.

Mit der Erfindung steht ein Stahl für Anwendungen, die eine hohe Verschleißbeständigkeit, eine hohe Härte, eine gute Korrosionsbeständigkeit und/oder eine niedrige Wärmeleitfähigkeit erfordern, zur Verfügung.The invention provides a steel for applications requiring high wear resistance, high hardness, good corrosion resistance and / or low thermal conductivity.

Der erfindungsgemäße Stahl erzielt im gehärteten Zustand eine Härte von mindestens 56 HRC und enthält in seinem Gefüge in Summe mindestens 30 Gew.-% Hartphasen vorhanden, die neben den TiC-Partikeln aus Karbid-, Oxid- oder Nitrid-Partikeln bestehen. Dabei beträgt im erfindungsgemäßen Stahl der Gehalt an TiC-Partikeln mindestens 20 Gew.-%.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. In the steel according to the invention, the content of TiC particles is at least 20% by weight.

Erfindungsgemäß sind die Hartphasen in eine Matrix eingebettet, welche (in Gew.-%) aus 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, According to the invention, 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,

Rest Eisen und unvermeidbaren Verunreinigungen besteht.Residual iron and unavoidable impurities persist.

Die Komponenten eines erfindungsgemäßen Stahls sind so eingestellt, dass er höchsten Anforderungen genügt, wie sie an Stähle gestellt werden, die im Bereich der kunststoffverarbeitenden Industrie eingesetzt werden. Dementsprechend eignet sich ein erfindungsgemäßer Stahl insbesondere für die Herstellung von Komponenten zum Neuerzeugen und zum Recycling von Kunststoffprodukten. So lassen sich aus erfindungsgemäßem Stahl beispielweise für das Granulieren von aus abrasiven Kunststoffen gebildeten Schmelzen benötigte Lochplatten, insbesondere Mikrogranulierlochplatten, herstellen, die selbst dann noch optimale Gebrauchseigenschaften aufweisen, wenn ihre Lochöffnungen mikrofein ausgebildet sind, um entsprechend feingekörnte Granulate zu erzeugen. Genauso lassen sich aus erfindungsgemäßem Stahl Messer zum Zerkleinern von Kunststoffteilen herstellen. Solche Messer werden, wie oben bereits erläutert, ebenfalls bei der Herstellung von Granulaten aus erschmolzenen Kunststoffsträngen benötigt, wie sie mit Hilfe von Lochplatten der voranstehend erläuterten Art in Granuliereinrichtungen erzeugt werden.The components of a steel according to the invention are adjusted to meet the highest demands placed on steels used in the plastics processing industry. Accordingly, a steel according to the invention is particularly suitable for the production of components for the regeneration and recycling of plastic products. Thus, for example, perforated plates, in particular microgranulation perforated plates, can be produced from steel according to the invention for granulating melts formed from abrasive plastics, which even have optimum performance properties if their perforation openings are microfine in order to produce correspondingly finely granulated granules. In the same way, 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 Granuliereinrichtungen.

Um das hierzu benötigte Eigenschaftsprofil bereitzustellen, enthält ein erfindungsgemäßer Stahl mindestens 20 Gew.-% TiC, die eingebettet sind in eine Matrix, die durch Ausscheidungsbildung zur Härtbarkeit des Stahls beiträgt und die gleichzeitig so gewählt ist, dass eine niedrige Wärmeleitfähigkeit von weniger als 35 W/mK unabhängig vom jeweiligen Wärmebehandlungszustand gewährleistet ist.In order to provide the property profile required for this purpose, 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.

Die Passivstromdichte des erfindungsgemäßen Stahls ist geringer als 5 µA/cm2, gemessen in sauerstofffreier 0,5 molarer Schwefelsäure mit einer Potenzialänderungsgeschwindigkeit von 600 mV/h gegen eine Kalomel-Bezugselektrode bei 20 °C. Erfindungsgemäßer Stahl weist daher bei hoher Härte und optimiertem Verschleißwiderstand eine Korrosionsbeständigkeit auf, die vergleichbar ist mit der Korrosionsbeständigkeit konventioneller austenitischer rostfreier Stähle.The passive current density of the steel according to the invention is less than 5 μA / 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.

Das gemäß mittels Ultraschallmessung in Abhängigkeit der Schallausbreitungsgeschwindigkeit bestimmte E-Modul erfindungsgemäßer Stähle liegt bei einer Temperatur von 20 °C bei mehr als 270 GPa, insbesondere mehr als 300 GPa, so dass der erfindungsgemäße Stahl bzw. daraus hergestellte Komponenten auch höchste Anforderungen an ihre Festigkeit sicher erfüllen.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.

Der gemäß mittels Dilatometer ermittelte thermische Ausdehnungskoeffizient von erfindungsgemäßem Stahl liegt in dem für Anwendungen, für die erfindungsgemäße Stähle vorgesehen sind, bedeutsamen Temperaturbereich von 20 °C bis 600 °C bei 7 x 10-6/K bis 12 x 10-6/K.The thermal expansion coefficient of steel according to the invention, as determined by means of a dilatometer, 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.

Durch die Anwesenheit einer ausreichenden Menge der extrem harten, thermodynamisch stabilen TiC-Partikel, die eine geringe Dichte bei niedriger Wärmeleitfähigkeit besitzen, wird in Kombination mit der erfindungsgemäß vorgesehenen Stahlmatrix, die ebenfalls eine hohe Härte erreicht, eine maximierte Verschleißbeständigkeit bei gleichzeitig minimierter Wärmeleitfähigkeit erhalten. Optimalerweise enthält dazu der erfindungsgemäße Stahl mindestens 20 Gew.-%, entsprechend etwa 30 Vol.-% TiC, oder mindestens 28 Gew.-% TiC, insbesondere mindestens 30 Gew.-% TiC. Jedoch sollte der TiC-Gehalt eine Obergrenze von 45 Gew.-% nicht überschreiten. Auf diese Weise lässt sich gewährleisten, dass sich erfindungsgemäßer Stahl betriebssicher herstellen und weiterverarbeiten lässt. Zu hohe Hartphasengehalte führen zwar zu erhöhter Härte und Verschleißbeständigkeit. Allerdings wird die thermische Ausdehnung reduziert, was die Verbundfertigung mit Stahlsubstraten deutlich erschwert. Zudem bedeutet ein höherer Hartphasengehalt, dass der Werkstoff spröder und rissempfindlicher wird. Gleichzeitig werden die mechanischen Bearbeitungsmöglichkeiten bei zu hohen Hartphasengehalten signifikant herabgesetzt. Ein Vorteil von erfindungsgemäßem Stahl besteht hier darin, dass auch er konventionell zerspanend bearbeitet werden kann.The presence of a sufficient amount of the extremely hard, thermodynamically stable TiC particles, which have a low density with low thermal conductivity, in combination with the inventively provided steel matrix, which also achieves a high hardness, a maximized wear resistance and simultaneously minimized thermal conductivity is obtained. Optimally, 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. However, 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. However, the thermal expansion is reduced, which makes joint production with steel substrates much more difficult. In addition, a higher hard phase content means that the material becomes more brittle and more susceptible to cracking. At the same time, the mechanical processing options are significantly reduced at high hard phase contents. An advantage of steel according to the invention here is that it too can be machined conventionally by machining.

Zur Optimierung der Härte und Verschleißbeständigkeit eines erfindungsgemäßen Stahls trägt zudem bei, dass erfindungsgemäß zusätzlich zu den TiC-Partikeln in der Stahlmatrix weitere Hartphasen vorhanden sind, so dass der Volumenanteil der Hartphasen am Gefüge des Stahls insgesamt mindestens 30 Gew.-% beträgt. Dies kann durch gesonderte Zugabe von Karbid-, Nitrid- oder Oxid-Partikeln bei der Erzeugung des Stahls erfolgen. Alternativ oder ergänzend dazu können auch die die Gewichtsanteile der Ausscheidungen bildenden Elemente (Ni, Al, Ti) innerhalb der erfindungsgemäßen Vorgaben so eingestellt werden, dass sich im Zuge der bei der Erzeugung des Stahls absolvierten Arbeitsschritte zuverlässig eine ausreichende Menge an härtesteigernden Ausscheidungen in der Matrix bildet.To optimize the hardness and wear resistance of 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. Alternatively or additionally, 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.

Gegenüber dem aus der oben schon erwähnten Dissertation von H. Hill bekannten Stahl sind beim erfindungsgemäßen Stahl die Gehalte an Mo und Co deutlich erhöht sowie die Gehalte an Ni und Ti deutlich vermindert. Zudem sind die Vorgaben für die Cu-, Al-, TiC- und NbC-Gehalte einer erfindungsgemäßen Legierung gegenüber dem bekannten Stahl variiert worden. Durch die erfindungsgemäße Einstellung der Legierungsgehalte ist es gelungen, einen Stahl im industriellen Maßstab zu erzeugen, der einen hohen Hartphasenanteil besitzt, der in einer Stahlmatrix von ebenfalls hoher Härte eingebettet ist. Ausgehend von den bekannten Stahlkonzepten erforderte dies aufwändige Untersuchungen und Versuche, weil die Wirkweise und die Wechselwirkungen der einzelnen Elemente und Phasen bei Stählen der hier in Rede stehenden Art sehr komplex sind. Der so erhaltene erfindungsgemäße Stahl weist mit seiner hohen Verschleißbeständigkeit, hohen Härte, guten Korrosionsbeständigkeit und niedrigen Wärmeleitfähigkeit eine optimierte Eigenschaftskombination auf.In contrast to the steel known from the above-mentioned thesis of H. Hill, 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. In addition, 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. By setting the alloy contents according to the invention, it has been possible to produce a steel on an industrial scale, which has a high proportion of hard phase, which is embedded in a steel matrix of likewise high hardness. Starting from the known steel concepts, this required extensive investigations and experiments, because the mode of action and the interactions of the individual elements and phases are very complex in steels of the type in question here. The steel according to the invention thus obtained has an optimized combination of properties with its high wear resistance, high hardness, good corrosion resistance and low thermal conductivity.

Die Ausscheidungen, die sich in der Stahlmatrix des erfindungsgemäßen Stahls bilden, sind intermetallische Ausscheidungen, an deren Entstehung vor allem die Elemente Ni, Al und Ti beteiligt sind. Diese Elemente bilden Ni3Al und Ni3Ti oder auch Mischformen. Diese intermetallischen Phasen liegen im Gefüge mit Korngrößen in der Größenordnung von 10 nm vor und werden nicht zum Gesamthartphasengehalt gezählt. Aufgrund ihrer geringen Größe leisten sie im Vergleich zu den groben Hartphasenpartikeln, wie sie erfindungsgemäß in der Matrix des erfindungsgemäßen Stahls eingebettet sind, keinen größeren Beitrag zur Beständigkeit gegen abrasiven Verschleiß. Jedoch bewirken die intermetallischen Ausscheidungen eine Steigerung der Härte und Festigkeit der Metallmatrix und tragen so ebenfalls zur Verbesserung der Gebrauchseigenschaften bei.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.

Chrom ist im erfindungsgemäßen Stahl in Gehalten von 9,0 - 15,0 Gew.-% vorhanden, um die geforderte Korrosionsbeständigkeit zu sichern. Optimalerweise liegt dazu der Cr-Gehalt bei 12,5 - 14,5 Gew.-%.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 .-%.

Molybdän ist im erfindungsgemäßen Stahl in Gehalten von 5,0 - 9,0 Gew.-% enthalten, um einerseits eine ausreichende Korrosionsbeständigkeit insbesondere im Hinblick auf die Lochkorrosion zu gewährleisten und andererseits die Bildung intermetallischer Phasen zu unterstützen, durch die die Härte der Stahlmatrix, in der die Hartphasen eingelagert sind, erhöht wird. Optimalerweise beträgt der Mo-Gehalt des erfindungsgemäßen Stahls 6,5 - 7,5 Gew.-%.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. Optimally, the Mo content of the steel according to the invention is 6.5-7.5% by weight.

Kobalt ist im erfindungsgemäßen Stahl in Gehalten von 6,0 - 11,0 Gew.-% enthalten, um zum einen die Martensitstarttemperatur zu erhöhen und zum anderen die Löslichkeit von Mo in der Metallmatrix zu reduzieren. Auf diese Weise kann sich das in der erfindungsgemäßen Stahlmatrix enthaltene Mo verstärkter an der Bildung intermetallischer Phasen beteiligen. Optimalerweise beträgt der Co-Gehalt des erfindungsgemäßen Stahls 8,0 - 10,0 Gew.-%.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. In this way, the Mo contained in the steel matrix according to the invention can participate more intensively in the formation of intermetallic phases. Optimally, the Co content of the steel according to the invention is 8.0-10.0% by weight.

Kupfer ist im erfindungsgemäßen Stahl in Gehalten von 0,3 - 1,5 Gew.-% enthalten, um die Ausscheidungshärtung zu beschleunigen. Optimalerweise beträgt der Cu-Gehalt des erfindungsgemäßen Stahls 0,5 - 1,0 Gew.-%.Copper is contained in the steel of the present invention at levels of 0.3-1.5 weight% to accelerate precipitation hardening. Optimally, the Cu content of the steel according to the invention is 0.5-1.0% by weight.

Nickel ist im erfindungsgemäßen Stahl in Gehalten von 3,0 - 7,0 Gew.-% vorhanden. Nickel wird in der Stahlmatrix in ausreichender Menge benötigt, um bei einem Lösungsglühen, das typischerweise bei ca. 850 °C durchgeführt wird, die austenitische Phase zu stabilisieren. Dies ist vor allem dann wichtig, wenn der erfindungsgemäße Werkstoff ausgehend von der Lösungsglühtemperatur abgeschreckt wird. Durch die Anwesenheit von Nickel wird hier der Austenit so weit stabilisiert, dass bei der Abschreckung sicher Martensit entsteht. Ist zu wenig Nickel in der erfindungsgemäß vorgesehenen Stahlmatrix vorhanden, so wird dieser Effekt nicht mit der notwendigen Sicherheit erreicht. Ist dagegen zu viel Nickel in der Stahlmatrix vorhanden, bildet sich kein Martensit, da die austenitische Phase dann auch bei Raumtemperatur stabil ist. Die zweite Aufgabe von Nickel im erfindungsgemäßen Stahl ist die Ausscheidungshärtung durch Bildung intermetallischer Phasen mit Elementen wie Al und Ti. Daher sind in der Stahlmatrix des erfindungsgemäßen Stahls die Gehalte an Ni, Al und Ti so aufeinander abgestimmt, dass zum einen die Martensitbildung gegeben ist und zum anderen die Ausscheidungshärtung ermöglicht wird. Optimalerweise beträgt dazu der Ni-Gehalt des erfindungsgemäßen Stahls 4,5 - 5,5 Gew.-%.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.

Titan ist im erfindungsgemäßen Stahl in Gehalten von 0,1 - 2,0 Gew.-% vorhanden, um, wie voranstehend schon erläutert, in Kombination mit Ni die Ausscheidungshärtung zu ermöglichen. Optimalerweise beträgt dazu der Ti-Gehalt des erfindungsgemäßen Stahls 0,8 - 1,2 Gew.-%.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. Optimally, the Ti content of the steel according to the invention is 0.8 to 1.2% by weight.

Auch Aluminium ist im erfindungsgemäßen Stahl in Gehalten von 0,1 - 2,0 Gew.-% enthalten, um in Kombination mit Ni die Ausscheidungshärtung zu bewirken. Optimalerweise beträgt dazu der Al-Gehalt des erfindungsgemäßen Stahls 1,0 - 1,4 Gew.-%.Also, 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. Optimally, the Al content of the steel according to the invention is 1.0 to 1.4% by weight.

Der erfindungsgemäße Stahl lässt sich äußerst verzugsarm härten, da Titankarbid eine geringe Wärmeausdehnung und keine Umwandlung besitzt.The steel according to the invention can be hardened with extremely low distortion, since titanium carbide has a low thermal expansion and no transformation.

Durch die Zugabe von bis zu 4,5 Gew.-% NbC-Partikeln wird der Verschleißwiderstand des erfindungsgemäßen Stahls erhöht. Gleichzeitig haben die NbC-Partikel eine geringere Wärmeleitfähigkeit als TiC, was sich günstig auf die Gebrauchseigenschaften des erfindungsgemäßen Stahls auswirkt. Darüber hinaus sind TiC und NbC isomorphe Karbide und daher untereinander mischbar. Dies führt bei Diffusionsreaktionen zur Bildung von Mischkarbiden. In Folge dessen ergibt sich im Vergleich zur alleinigen Verwendung von TiC eine Änderung der Valenzelektronenkonzentration und somit die Bildung von Leerstellen im Zwischengitter des Kohlenstoffes. Auch auf diesem Weg wird die Wärmeleitfähigkeit des erfindungsgemäßen Stahls herabgesetzt und die Gebrauchseignung verbessert. Diese Wirkung wird dadurch erzielt, dass im erfindungsgemäßen Stahl mindestens 2,0 Gew.-% NbC vorhanden sind. Ein optimaler Einfluss ergibt sich dabei dann, wenn der NbC-Gehalt 2,0 - 3,0 Gew.-% beträgt.By adding up to 4.5 wt .-% NbC particles, the wear resistance of the steel according to the invention is increased. At the same time, 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. In addition, TiC and NbC are isomorphic carbides and therefore miscible with each other. This leads to the formation of mixed carbides in diffusion reactions. As a result, compared to the exclusive use of TiC a change in the Valence electron concentration and thus the formation of vacancies in the interstitial carbon. Also in this way, the thermal conductivity of the steel according to the invention 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.

Indem der erfindungsgemäße Stahl in konventioneller Weise pulvermetallurgisch hergestellt wird, lässt sich gewährleisten, dass sein Gefüge frei von Seigerungen und Faserverläufen ist. Die erfindungsgemäß als Hartphasen verwendeten Karbid-, Nitrid- und Oxidpartikel werden während der pulvermetallurgischen Fertigung bereits als "fertige" Partikel zugeführt.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.

Für die pulvermetallurgische Herstellung lassen sich sowohl die Sinter-, als auch die HIP- (Heiß-Isostatisches Pressen) Route nutzen. Beispielsweise eignet sich auch das Supersolidus Flüssigphasensintern auf Basis gasverdüster Stahlpulver für die Erzeugung erfindungsgemäßer Stähle. Eine Beschreibung der üblicherweise bei der pulvermetallurgischen Herstellung von Stählen der hier in Rede stehenden Art angewendeten Arbeitsschritte findet sich beispielsweise in Foller, M.; Meyer, H.; Lammer, A.: Wear and Corrosion of Ferro-Titanit and Competing Materials. In: Tool steels in the next century: Proceedings of the 5th International Conference on Tooling, September 29th - October 1st, University of Leoben, Austria, 1999, S. 1 - 12 , in H. Hill, S. Weber, W. Theisen, A. van Bennekom, Optimierung korrosionsbeständiger MMC mit hohem Verschleißwiderstand, 30. Hagener Symposium, 24. - 25.11.2011 oder in der oben schon erwähnten Dissertation von Horst Hill.For the powder metallurgical production, both the sintering, as well as the HIP (hot isostatic pressing) route can be used. For example, 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. In: Tool steels in the next century: Proceedings of the 5th International Conference on Tooling, September 29th - October 1st, University of Leoben, Austria, 1999, p. 1 - 12 , in H. Hill, S. Weber, W. Theisen, A. van Bennekom, Optimization of Corrosion Resistant MMC with High Wear Resistance, 30th Hagen Symposium, 24. - 25.11.2011 or in the already mentioned dissertation by Horst Hill.

Der erfindungsgemäße Stahl kann zur Einstellung seiner mechanischen Eigenschaften einer konventionellen Wärmebehandlung unterzogen werden, bei der er für 2 - 4 Stunden erwärmt, anschließend unter einer mit einem Druck von 1 - 4,5 bar beaufschlagten Stickstoffatmosphäre abgeschreckt und schließlich über 6 - 8 Stunden bei 480 °C ausgelagert wird. Erfindungsgemäßer Stahl weist nach einer derartigen Wärmebehandlung regelmäßig eine Härte von mehr als 62 HRC auf. Durch eine Erwärmung unter Vakuum und eine Abschreckung in einer Inertgasatmosphäre werden negative Einflusszonen im Randbereich des für die Wärmebehandlung jeweils aus dem Stahl geformten Halbzeugs vermieden.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. By heating under vacuum and quenching in an inert gas atmosphere negative influence zones are avoided in the edge region of the semi-finished for the heat treatment in each case from the steel.

Beschränkt sich die Wärmebehandlung auf eine Weichglühung bei 850 °C über 2 - 4 Stunden, so besitzt der erfindungsgemäße Stahl eine Härte von mehr als 50 HRC.If the heat treatment is limited to soft annealing at 850 ° C. for 2 to 4 hours, the steel according to the invention has a hardness of more than 50 HRC.

Nachfolgend wird die Erfindung anhand von Ausführungsbeispielen näher erläutert. Die Figuren zeigen:

Fig. 1
einen Ausschnitt einer rasterelektronenmikroskopischen Aufnahme eines Schnitts einer erfindungsgemäßen Probe;
Fig. 2
ein Diagramm, in dem die Ergebnisse der Messung der Wärmeleitfähigkeit von erfindungsgemäßen und zum Vergleich erzeugten Stahlproben dargestellt sind;
Fig. 3
ein Diagramm mit dem Ergebnis einer an erfindungsgemäßen und zum Vergleich erzeugten Stahlproben durchgeführten Stromdichte-Potenzial-Messung;
Fig. 4
ein Diagramm, das das Ergebnis einer Dilatometermessung an einer aus erfindungsgemäßem Stahl erzeugten Probe wiedergibt.
The invention will be explained in more detail by means of exemplary embodiments. The figures show:
Fig. 1
a section of a scanning electron micrograph of a section of a sample according to the invention;
Fig. 2
a diagram in which the results of the measurement of the thermal conductivity of steel samples according to the invention and produced for comparison are shown;
Fig. 3
a diagram showing the result of an inventively made and compared steel samples current density potential measurement;
Fig. 4
a diagram showing the result of a Dilatometermessung on a sample produced from steel according to the invention.

Zum Vergleich der Eigenschaften eines erfindungsgemäßen Stahls, der für die Herstellung von Lochplatten oder Messern für eine Unterwasser-Granuliermaschine bestimmt ist, mit den Eigenschaften eines bekannten, für denselben Verwendungszweck vorgesehenen Stahls sind der erfindungsgemäße Stahl E und der bekannte Stahl V erzeugt worden. Die Zusammensetzung beider Stähle E und V ist in Tabelle 1 angegeben.To compare the properties of a steel according to the invention, intended for the production of perforated plates or knives for an underwater pelletizer, with the characteristics of a known steel intended for the same purpose, the steel E according to the invention and the known steel V have been produced. The composition of both steels E and V is given in Table 1.

Die Zusammensetzung des Stahls V entsprach dabei der Zusammensetzung des unter der Bezeichnung "Ferro-Titanit Nikro 128" bekannten, beispielsweise in der oben bereits genannten Veröffentlichung dokumentierten Stahls. Die bei der pulvermetallurgischen Herstellung beider Stähle E,V absolvierten Arbeitsschritte entsprachen den Arbeitsschritten, die üblicherweise bei der pulvermetallurgischen Erzeugung des Stahls "Ferro-Titanit Nikro 128" ausgeführt werden. Sie sind in der oben bereits erwähnten Fachliteratur erläutert.The 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.

Nach der pulvermetallurgischen Erzeugung sind Proben PE1,PV1 der Stähle E und V einer Wärmbehandlung unterzogen worden, die ebenfalls der beim Stahl Ferro-Titanit Nikro 128 standardmäßig absolvierten Wärmebehandlung entsprach. Dazu sind die Proben PE1 und PV1 zunächst über eine Dauer von zwei bis vier Stunden im Vakuum bei einer Temperatur von 850 °C gehalten worden und anschließend unter einer mit 1 - 4,5 bar druckbeaufschlagten Stickstoffatmosphäre abgeschreckt worden. Anschließend erfolgt eine Aushärtebehandlung, bei der die Proben PE1,PV1 jeweils für sechs bis acht Stunden bei einer Temperatur von 480 °C ausgelagert worden sind.After powder metallurgy production, 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. For this purpose, 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 zeigt einen Ausschnitt einer rasterelektronenmikroskopischen Aufnahme eines Schnitts einer Probe PE1 des derart standardmäßig wärmebehandelten erfindungsgemäßen Stahls E. Die Metallmatrix ist durch die hellen Bereiche erkennbar, wogegen die von der Matrix umgebenen TiC-Einschlüsse dunkel wiedergegeben sind. 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.

Andere aus den Stählen E und V bestehende Proben PE2, PV2 sind einer über ebenfalls 2 - 4 Stunden sich erstreckenden Weichglühung bei 850 °C unterzogen worden.Other samples PE2, PV2 consisting of steels E and V have been subjected to soft annealing at 850 ° C., also for 2 to 4 hours.

An den Proben PE1, PV1, PE2, PV2 sind die Hartphasengehalte bestimmt worden. Sie lagen bei den aus dem erfindungsgemäßen Stahl PE1, PE2 erzeugten Proben im Mittel bei mehr als 30 Gew.-%, wogegen die aus dem Vergleichsstahl V erzeugten Proben PV1,PV2 im Mittel nur 30 Gew.-% Hartphasen aufwiesen.On the samples PE1, PV1, PE2, PV2 the hard phase contents have been determined. They were in the samples produced from the steel according to the invention PE1, PE2 in Mean at more than 30 wt .-%, whereas the samples produced from the comparison steel V PV1, PV2 had on average only 30 wt .-% hard phases.

Zur Bestimmung der Härte der verschiedenen Proben PE1,PE2,PV1,PV2 wurden fünf Härtemessungen gemäß DIN EN ISO 6508-1 durchgeführt. Die Mittelwerte der so für die Proben PE1, PE2, PV1, PV2 erfassten Messwerte sind in Tabelle 2 angegeben. Es zeigt sich, dass die Härte der erfindungsgemäßen Proben PE1,PE2 jeweils höher lag als die Härte der Vergleichsproben.To determine the hardness of the different samples PE1, PE2, PV1, PV2, five hardness measurements according to DIN EN ISO 6508-1 were carried out. The mean values of the measured values thus obtained for the samples PE1, PE2, PV1, PV2 are given in Table 2. It turns out that the hardness of the samples according to the invention PE1, PE2 was higher than the hardness of the comparative samples.

Des Weiteren ist die temperaturabhängige Wärmeleitfähigkeit λ(T) mit Hilfe der indirekten Methode bei Raumtemperatur, 100 °C, 200 °C und 300 °C, bestimmt worden: λ T = a T × ρ T × cρ T

Figure imgb0001

mit a(T):
Temperaturleitfähigkeit, gemessen mittels Laserflash, wie in Linseis Messgeräte GmbH: Instruction Manual LFA 1250/1600 - Laser Flash: Thermal constant analyser, 2010, oder ASTM International E 1461-01: Standard Test Method for Thermal Diffusivity by the Flash Method, 2001, erläutert;
ρ(T):
die Dichte der jeweiligen Probe, gemessen mit dem Dilatometer;
cρ(T):
die spezifische isobare Wärmekapazität der Probe, ermittelt durch Dynamische Differenzkalorimetrie ("DSC").
Furthermore, the temperature-dependent thermal conductivity λ (T) was determined by means of the indirect method at room temperature, 100 ° C, 200 ° C and 300 ° C: λ T = a T × ρ T × cρ T
Figure imgb0001
with a (T):
Thermal conductivity measured by laser flash as described in Linseis Instruments: Instruction Manual LFA 1250/1600 - Laser Flash: Thermal constant analyzer, 2010, or ASTM International E 1461-01: Standard Test Method for Thermal Diffusivity by the Flash Method, 2001 ;
ρ (T):
the density of each sample measured with the dilatometer;
cρ (T):
the specific isobaric heat capacity of the sample as determined by Differential Scanning Calorimetry ("DSC").

Das Ergebnis dieser Untersuchung ist für die Proben PE1 und PV1 in Fig. 2 dargestellt. Es zeigt sich, dass die Wärmeleitfähigkeit bei der aus dem erfindungsgemäßen Stahl E erzeugten Probe PE1 jeweils niedriger war als bei der Probe PV1, die aus dem Vergleichsstahl V gefertigt worden ist. Die geringe Wärmeleitfähigkeit der erfindungsgemäßen Probe PE1 ist im Hinblick auf den hier vorgesehenen Verwendungszweck der Stähle E und V vorteilhaft.The result of this study is for samples PE1 and PV1 in Fig. 2 shown. It can be seen that the thermal conductivity in the sample PE1 produced from the steel E according to the invention was in each case lower than in the case of the sample PV1, which was manufactured from the comparison steel V. The low thermal conductivity of the sample according to the invention PE1 is advantageous in view of the intended use of the steels E and V here.

Der TiC-Gehalt der erfindungsgemäßen Proben PE1,PE2 betrug, wie in Tabelle 1 angegeben, jeweils mehr als 30 Gew.-%.The TiC content of the samples according to the invention PE1, PE2 was, as indicated in Table 1, each more than 30 wt .-%.

Die Dichte der aus dem erfindungsgemäßen Stahl E erzeugten Proben PE1,PE2 betrug 6,55 g/cm3, womit die theoretische Dichte erreicht wurde. Wie aus Fig. 1 hervorgeht, weist das Gefüge keine Restporösitäten auf.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.

Das Ergebnis einer an aus dem erfindungsgemäßen Stahl E erzeugten Proben PE1 und aus dem Vergleichsstahl V erzeugten Proben PV1 durchgeführten Stromdichte-Potenzial-Messung ist in Fig. 3 dargestellt. Darin ist die für die Proben PE1 ermittelte Stromdichte-Potenzialkurve als durchgezogene Linie und die für die Proben PV1 ermittelte Stromdichte-Potenzialkurve als gestrichelte Linie dargestellt. Die Stromdichte-Potenzialkurven wurden in sauerstofffreier 0,5 molarer Schwefelsäure mit in einer Potenzialänderungsgeschwindigkeit von 600 mV/h gegen eine Kalomel-Bezugselektrode bei 20 °C gemessen. Auch die für die erfindungsgemäßen Proben PE1 ermittelten Passivstromdichten lagen jeweils unter 5 µA/cm2.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. Therein, 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. Also the passive current densities determined for the samples according to the invention PE1 were in each case below 5 μA / cm 2 .

Für die aus dem erfindungsgemäßen Stahl E erzeugten Proben PE1 ist das E-Modul mittels Ultraschall in Abhängigkeit von der Schallausbreitungsgeschwindigkeit auf 318 GPa bestimmt worden. Das E-Modul der konventionellen Proben PV1 lag dagegen bei 294 GPa.For the samples PE1 produced from the steel E according to the invention, the E modulus has been determined by means of ultrasound as a function of the sound propagation speed to 318 GPa. In contrast, the modulus of elasticity of the conventional samples PV1 was 294 GPa.

Tabelle 3 gibt einen Überblick über die thermische Ausdehnung des Stahls E. Gemessen wurde diese mittels eines Bähr Dilatometers in Temperaturschritten von 100 °C bis zu einer Maximaltemperatur von 600 °C. Es ist zu erkennen, dass der thermische Ausdehnungskoeffizient αth in diesem Temperaturbereich zwischen 7 und 12 10-6/K liegt. Ergänzend dazu zeigt Fig. 4 exemplarisch das Ergebnis einer Dilatometermessung an einer aus dem erfindungsgemäßen Stahl erzeugten Probe PE1, die dieses Ergebnis bestätigt. Tabelle 1 Stahl Cr Mo 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 - Angaben in Gew.-%, Rest Eisen und unvermeidbare Verunreinigungen Tabelle 2 Probe mittlere Härte HRC PE1 65 PV1 62 PE2 54 PV2 53 Tabelle 3 Temperatur [°C] αth 100 8,4 200 8,7 300 9,0 400 9,2 500 9,4 600 9,7 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 α th 6 / K is in this temperature range 7-12 10-. In addition to this shows 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 stole 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] α th 100 8.4 200 8.7 300 9.0 400 9.2 500 9.4 600 9.7

Claims (12)

  1. Steel for applications which require high wear resistance, a high degree of hardness, good corrosion resistance and/or low thermal conductivity,
    - wherein the steel has a hardness of at least 56 HRC in the hardened state,
    - wherein in the microstructure of the steel in total at least 30 % wt. of hard phases are present which in addition to TiC particles consist of further carbide particles, oxide particles or nitride particles,
    - wherein the content of TiC particles is at least 20 % wt. and 2 - 4.5 % wt. of NbC particles are present,
    and
    - wherein the hard phases are embedded in a matrix which consists (in % wt.) of
    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,
    with the remainder iron and unavoidable impurities.
  2. Steel according to Claim 1, characterised in that its Cr content is 12.5 - 14.5 % wt.
  3. Steel according to any one of the preceding claims, characterised in that its Mo content is 6.5 - 7.5 % wt.
  4. Steel according to any one of the preceding claims, characterised in that its Ni content is 4.5 - 5.5 % wt.
  5. Steel according to any one of the preceding claims, characterised in that its Co content is 8 - 10 % wt.
  6. Steel according to any one of the preceding claims, characterised in that its Cu content is 0.5 - 1.0 % wt.
  7. Steel according to any one of the preceding claims, characterised in that its Ti content is 0.8 - 1.2 % wt.
  8. Steel according to any one of the preceding claims, characterised in that its Al content is 1.0 - 1.4 % wt.
  9. Steel according to any one of the preceding claims, characterised in that its TiC content is at most 45 % wt.
  10. Steel according to any one of the preceding claims, characterised in that it is produced by powder metallurgy.
  11. Use of a steel constituted according to any one of the preceding claims for producing components which are used during the recycling or reproducing of plastic products.
  12. Use according to claim 11, characterised in that the component is a die plate or a knife for reducing plastic parts to small pieces.
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RU2674174C2 (en) 2018-12-05
BR112017002127A2 (en) 2017-11-21
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US20180119257A1 (en) 2018-05-03
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RU2017106319A3 (en) 2018-08-28

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