EP3323902B1 - Matériau en acier contenant des particules dures, produit de la métallurgie des poudres, procédé de production d'un composant à partir d'un tel matériau d'acier et composant ainsi fabriqué - Google Patents

Matériau en acier contenant des particules dures, produit de la métallurgie des poudres, procédé de production d'un composant à partir d'un tel matériau d'acier et composant ainsi fabriqué Download PDF

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Publication number
EP3323902B1
EP3323902B1 EP16200060.8A EP16200060A EP3323902B1 EP 3323902 B1 EP3323902 B1 EP 3323902B1 EP 16200060 A EP16200060 A EP 16200060A EP 3323902 B1 EP3323902 B1 EP 3323902B1
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EP
European Patent Office
Prior art keywords
steel
content
steel material
contents
weight
Prior art date
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Not-in-force
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EP16200060.8A
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German (de)
English (en)
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EP3323902A1 (fr
Inventor
Dr. Horst Hill
Dr. André van Bennekom
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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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Application filed by Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG filed Critical Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
Priority to EP16200060.8A priority Critical patent/EP3323902B1/fr
Priority to PCT/EP2017/079968 priority patent/WO2018095928A1/fr
Priority to US16/349,463 priority patent/US20200190638A1/en
Priority to JP2019547782A priority patent/JP2020501027A/ja
Publication of EP3323902A1 publication Critical patent/EP3323902A1/fr
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Classifications

    • 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%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon

Definitions

  • the invention relates to a steel material which is produced by powder metallurgy and contains hard material particles.
  • steel materials are also referred to in technical terms as metal matrix composites.
  • the invention also relates to a method for producing such a steel material.
  • the invention also relates to components made from a steel material of the type according to the invention.
  • the invention aims at a steel material which is suitable for the production of components that are exposed to the highest surface loads in practical use and are simultaneously moved quickly.
  • An example of such components are roll guide rollers that are used in machines (roll stands) for wire rolling.
  • the wire to be rolled and moved at a high conveying speed is guided on these rollers in the hot state at temperatures of more than 1000 ° C. Due to its high temperature, a layer of scale forms on the wire.
  • the roller guide rollers are therefore also exposed to high abrasive loads on their surfaces that come into contact with the wire.
  • the wear resistance in particular the resistance to abrasive wear, the corrosion resistance, the resistance to thermal shock stress and the weight of the steels from which roller guide rollers and other components that are subjected to comparable loads in practical use are made posed.
  • the steel has an Mn content of 0.2 - 2.0%, a P content of max. 0.1%, an S content of max. 0.1%, a Si content of max. 2.0%, a Cr content of 11.5 - 14.5%, a Mo content of max. 3.0%, a V content of 8.0 - 15.0 %, an N content of 0.03-0.46% and a C content that should be 1.47-3.77%.
  • steel materials produced by powder metallurgy for the production of components of the type in question is, for example, in U.S. 4,249,945 A described.
  • these steels have a steel matrix consisting of 0.1-1% by weight Mn, up to 2% by weight Si, 4.5-5.5% by weight Cr, 0.8-1 , 7% by weight Mo, up to 0.14% by weight S, 8-10.5% by weight V, 2.2-2.6% by weight C, the remainder being iron and unavoidable impurities , and contain 13.3 - 17.3% by volume of vanadium carbides.
  • the steel reaches a hardness of up to 63 HRC.
  • the particles consist of a cold work steel alloy with a vanadium carbide dispersion of the MC type with a carbide particle size which is essentially completely below 6 ⁇ m, the content of the vanadium dispersion in the particles being 18.5-34.0% by volume.
  • the particles are made by atomizing a molten tool steel alloy at a temperature above 2910 ° F and rapidly cooling the atomized alloy.
  • a method for the powder-metallurgical production of a steel material in which a matrix made of steel with high Mo and / or W contents is used and in which an additional 2 - 12% hard materials are embedded in the matrix.
  • the hard materials can be nitrides, carbides or carbonitrides.
  • the matrix material contains Mo and W that meet the condition 18% ⁇ W + 2Mo ⁇ 40%.
  • the C content of the matrix material is matched to the high Mo and W contents so that the matrix material can develop a high level of hardness even through the precipitation of carbides.
  • the hardness is further increased by adding large amounts of Co.
  • the material produced in this way has a maximum hardness of more than 70 HRC.
  • the invention has achieved this object by means of the steel provided according to claim 1.
  • the solution according to the invention to the object set above in relation to the method consists in that at least the work steps mentioned in claim 11 are run through in the production of components from a steel according to the invention.
  • steel according to the invention is particularly suitable for the production of components which, in practical use, execute movements with high acceleration or speed and are in particular exposed to high surface and temperature loads.
  • hard material particles are titanium carbide particles TiC.
  • the steel according to the invention is thus composed in such a way that, with a minimized density, in addition to good wear resistance and an associated long service life, it has a maximized resistance to extreme temperature changes and an equally optimized corrosion resistance.
  • the alloy ranges are selected so that a broad and, for the use of hard material particles, also called metal matrix composites ("MMCs"), meaningful range for vanadium-alloyed, high-strength and wear-resistant materials are available.
  • MMCs metal matrix composites
  • the two most important alloying elements in this alloy system are carbon and vanadium.
  • Carbon is responsible for both martensitic hardening and the formation of hard vanadium carbide, which in combination with high hardness and the associated high strength results in optimized wear resistance.
  • C is therefore present in the steel according to the invention in contents of 1.5-5.0% by weight.
  • the carbon has two main tasks: On the one hand, C is required for the martensitic hardening of the metal matrix. On the other hand, the presence of sufficient amounts of C leads to the formation of hard carbides with the alloying elements present, in particular with V, Cr and, if present, Nb. If there is too little C in the alloy of the steel matrix, the formation of martensite does not occur, if too much C residual austenite is stabilized. Both effects can reduce hardness and wear resistance. So the ratio of carbon to the carbide-forming elements is always important.
  • silicon is used for deoxidation in the melting of the primary materials which are part of the steel alloy powder alloyed according to the invention and provided for the production of components according to the invention.
  • the presence of silicon increases the carbon activity and thus leads to a lowering of the melting temperature. Without the targeted addition of at least 0.3% by weight of Si, in particular at least 0.7% by weight of Si, higher C contents would be necessary.
  • the atomization process is in turn facilitated by the lowered melting point. Silicon also reduces the viscosity of the metal melt, which also helps to simplify the powder atomization process.
  • silicon increases the hardenability of the steel material, since the transformation noses in the ZTU diagram are shifted for longer times.
  • the strength of the austenite at the hardening temperature is increased by the dissolved proportion of Si, which explains the greater stability of the austenite and enables longer cooling times.
  • Si contents of up to 2.0% by weight, in particular up to 1.5% by weight. Excessive Si contents would lead to a stabilization of the ferrite, as a result of which the proportion of martensite present in the structure of the steel after hardening would be reduced and thus the hardness and wear resistance of the steel material according to the invention would also decrease.
  • Manganese is present in the steel material according to the invention in order to optimize the atomizability of the steel during the production of the steel powder and its hardness.
  • the presence of sufficient Mn contents similar to the presence of Si, lowers the melting point of the steel and lowers the viscosity of the metal melt, so that the targeted addition of Mn contributes to the simplification of the atomization process.
  • manganese also increases the hardenability of the steel material.
  • the dissolved Mn also contributes to the stabilization of the austenite.
  • Mn binds sulfur by forming MnS, which reduces the risk of hot cracks and improves machinability.
  • Too high a manganese content could, on the one hand, stabilize the austenitic phase to such an extent that the soft annealing time would be significantly increased.
  • the Mn content is too high, the austenitic phase could also be stabilized to such an extent that residual austenite would remain in the structure after hardening. This microstructure would be significantly softer than martensite, which would reduce hardness and wear resistance.
  • Mn contents of a steel material according to the invention of about 1.2% by weight have proven to be particularly practical.
  • chromium is used in combination with Mo and V to adjust the tempering resistance, corrosion resistance and hardenability.
  • Cr primarily has a positive influence on the tempering resistance and hardenability.
  • the Cr content here is not yet sufficient for increased demands on corrosion resistance.
  • the steel matrix is already harder as a result of increasing Cr carbide formation.
  • the steel material according to the invention With contents of at least 11.0% by weight of Cr, in particular at least 12.0% by weight, in the steel material according to the invention, with maximized hardness and strength, tempering and corrosion resistance are achieved which also meet the highest requirements.
  • the advantageous effects of Cr can be used particularly reliably in that the Cr content is set to at least 12.5% by weight. Too high a Cr content would cause more Cr carbides to form. However, the formation of Cr carbides would set C, which would reduce the martensite formation, so that the desired high hardness of the martensite could no longer be achieved. If the Cr content is significantly higher than the upper limit specified in accordance with the invention, the ferritic phase would also be stabilized, whereby the required hardness and wear resistance would likewise not be achieved. Therefore, according to the invention, the maximum content of Cr is limited to 15.0% by weight, in particular at most 14.0% by weight, with Cr contents of up to 13.5% by weight being particularly suitable in practice have turned out.
  • the C content% C should be around 30% higher than the target content% C target determined using the above formula.
  • % V denotes the respective V content of the alloy of the steel matrix.
  • a C content is accordingly advantageously chosen which lies between the minimum C contents, which according to the two above formulas for the low Cr and high Cr contents can be determined.
  • The% C target content is in each case a target value that should be aimed for in the production of the alloy powder in an optimal way for the C content. It goes without saying that this target content is considered to have been achieved when the actual C content% C, within the tolerances specified for alloy engineering or customary, corresponds to the target content% C target of the respective steel material according to the invention.
  • % C % C target ⁇ 0.2% by weight should then apply.
  • the C content set in accordance with the stipulation explained above compensates for the fact that carbon is bound by Cr as a result of the Cr carbide formation. In this way it can be ensured that sufficient C is always available for the formation of martensite and that an optimized hardness and wear resistance are achieved, which are sufficient for most applications.
  • a tolerance range of the V content of, for example, +/- 0.5% by weight is permitted, so that its actual V content can vary between 14.5-15.5% by weight.
  • a tolerance of +/- 0.2% by weight around the target value% C target is permitted for the actual C content.
  • the actual C content of the steel material V15 can thus be 3.2-3.6% by weight.
  • molybdenum increases the corrosion resistance, hardenability and tempering resistance of components made from steel according to the invention if Mo contents of at least 0.5% by weight, in particular at least 0.9% by weight, are present.
  • Mo contents impair the formability of the steel, since the high-temperature strength is significantly increased.
  • high contents of Mo would also stabilize the ferritic phase.
  • the maximum Mo content in the steel according to the invention is therefore limited to 2.0% by weight, in particular a maximum of 1.5% by weight.
  • the Mo content of a steel according to the invention, which is particularly suitable for the purposes according to the invention, is accordingly in the range of 1.2% by weight.
  • Vanadium is present in the steel according to the invention in contents of 6.0% by weight to 18.0% by weight in order to achieve optimized wear resistance through the formation of vanadium-rich carbides or carbonitrides.
  • vanadium is increasingly involved in the formation of carbides during tempering in the secondary hardness maximum.
  • High V contents of at least 16% by weight lead to particularly high wear resistance, so that steel materials according to the invention with such high V contents are particularly suitable for use as a material for roller guide rollers, the maximum in use Are exposed to loads.
  • the fact that the V content is limited to 17.4% by weight or 17.0% by weight, to 16.0% by weight or in particular at most 15.5% by weight can be reliably avoided that too much carbon is bound by carbide formation.
  • the steel material according to the invention can be machined more easily than with the higher V and C contents. Simplified machinability is accordingly achieved when the V content is reduced to a maximum of 12% by weight, in particular a maximum of 10% by weight, and thus also the C content determined as a function of the V content in the manner described above is limited.
  • Niobium is optionally present in contents of up to 2.0% by weight in the steel according to the invention.
  • Nb works very similarly to vanadium. It mainly participates in the formation of hard and wear-resistant monocarbides. Therefore, based in each case on their contents in atomic%, Nb and V in a ratio of 1: 1 can be exchanged alternately if this proves to be expedient, for example with regard to the availability of these alloying elements.
  • Nickel can optionally be present in contents of up to 1.0% by weight in the steel material according to the invention in order to stabilize the austenite content in a similar way to Mn and thus improve the hardenability.
  • the presence of Ni ensures that austenite is actually formed at the respective hardening temperature and that no undesired ferrite is formed in the structure of the steel.
  • an excessively high Ni content increases the cooling time required for martensite formation.
  • the Ni content should not be too high, as there is a risk that retained austenite will be present in the structure after hardening.
  • the Ni content is therefore preferably at least 0.2% by weight, with Ni contents of up to 0.4% by weight resulting in optimized effects of the presence of Ni.
  • Cobalt can also optionally be present in contents of up to 1.0% by weight in the steel material according to the invention. Similar to nickel, Co has a stabilizing effect on austenite formation and the hardening temperature. In contrast to nickel or manganese, Co does not lower the final temperature of the martensite, which is why its presence is less critical with regard to the formation of retained austenite. In addition, cobalt increases the heat resistance. If these positive influences are to be used through the addition of Co, contents of at least 0.3% by weight of Co prove to be particularly expedient, with optimized effects occurring with Co contents of up to 0.5% by weight.
  • tungsten can optionally be added to the steel in contents of up to 1.0% by weight. Above all, tungsten increases the tempering resistance and participates in the formation of carbide, especially during tempering in the secondary hardness maximum. The tempering temperatures are shifted to higher temperatures due to the presence of W. Similar to cobalt, the heat resistance is also increased by W. However, too high a W content would also stabilize the ferritic phase. If the positive influences of W are to be used, contents of at least 0.3% by weight of W therefore prove to be particularly expedient, with optimized effects occurring at W contents of up to 0.5% by weight.
  • the remainder of the steel consists of iron and unavoidable impurities that get into the steel due to the manufacturing process or the raw materials from which the constituents of the steel alloy powder are obtained, but have no effect there in terms of properties.
  • Sulfur can be present in the steel material in contents of up to 0.35% by weight in order to improve the machinability. With higher S contents, on the other hand, the properties of the steel material composed according to the invention are worsened. In order to be able to safely use the beneficial effect of the presence of S, at least 0.035% by weight can be present in the steel material according to the invention. If, on the other hand, the machinability is not to be improved by the targeted addition of S, the S content can accordingly be limited to less than 0.035% by weight.
  • the unavoidably present impurities also include P contents of up to 0.035% by weight and, for example, a total of up to 0.2% by weight of oxygen.
  • Nitrogen is also not added to the steel material according to the invention in a targeted manner, but gets into the steel material during the atomization process due to the nitrogen affinity of the alloy components.
  • the N content should be less than 0.12% by weight, in particular limited to a maximum of 0.1% by weight.
  • the density of steel material according to the invention is typically in the range of 6.4-7.6 g / cm 3 , the density of the pure steel matrix material typically being 7.0-7.6 g / cm 3 .
  • Powder metallurgical production allows the density and wear resistance of steel according to the invention to be further optimized by the targeted addition of hard phases with low density, optionally in the sense of the respective application, if this is desired with regard to the desired property. It has been shown here that the use properties of steel material according to the invention are increased in that it contains 2.5 to 30% by weight of hard material particles which, in the finished steel, are embedded in its steel matrix composed in the manner explained above.
  • the hard materials are in the initial state as a powder.
  • the hard materials can be carbides, nitrides, oxides or borides.
  • the group of suitable hard materials accordingly includes Al 2 O 3 , B 4 C, SiC, ZrC, VC, NbC, TiC, WC, W 2 C, Mo 2 C, V 2 C, BN, Si 3 N 4 , NbN or TiN .
  • Titanium carbide TiC has proven to be particularly suitable for the purposes according to the invention. Titanium carbide has a hardness of 3200 HV and thus increases the hardness and wear resistance of the steel particularly effectively. At the same time, TiC is chemically resistant and has no negative impact on corrosion resistance. The low density of TiC also has a beneficial effect.
  • steel according to the invention achieves hardness values which are typically in the range of 58-70 HRC.
  • the typical soft annealing hardness of steel material according to the invention is typically up to 65 HRC due to the presence of the hard material particles provided according to the invention.
  • the powder can be produced in a conventional manner, for example by gas atomization or any other suitable method.
  • the alloy powder can be produced, for example, by gas or water atomization or a combination of these two atomization processes. Atomization of a melt alloyed in accordance with the invention to form the alloy powder is conceivable.
  • those with an average diameter of less than 500 ⁇ m are selected from the powder particles for further processing according to the invention by sieving, powders with average particle sizes of less than 250 ⁇ m, in particular less than 180 ⁇ m, having proven particularly suitable.
  • the alloy powder provided according to the invention optimally has a bulk density of 2-6 g / cm3 (determined according to DIN EN ISO 3923-1) and a tap density of 3-8 g / cm3 (determined according to DIN EN ISO 3953).
  • the steel alloy powder provided in step a) is mixed with the hard material powder selected in each case.
  • the amount of admixed hard material particles is determined taking into account the information given above with regard to the optimized selection of the hard material content so that the hard material particles content of the finished mixture is in the range of 2.5-30% by weight.
  • the alloy powder produced in step a) or step b) can be dried in a conventional manner in order to remove residues of liquids and other volatile components that could hinder the subsequent shaping process.
  • a raw part is now formed from the alloy powder containing hard material particles.
  • the alloy powder can be brought into the respective shape in a manner known per se by a suitable sintering process, in particular by hot isostatic pressing ("HIPen").
  • HIPen hot isostatic pressing
  • Typical pressures during HIPing are in the range from 900 to 1500, in particular 1000 bar, at a temperature of 1050 to 1250 ° C., in particular 1080 to 1200 ° C.
  • austenite, VC and Cr carbide are formed in the structure of the steel material.
  • the respective component can also be produced in an additive process from the alloy powder procured and provided according to the invention.
  • additive encompasses all manufacturing processes in which a material is added to produce a component, this addition usually taking place in layers.
  • “Additive manufacturing processes”, which are often referred to as “generative processes” in technical terms, are in contrast to the classic subtractive manufacturing processes, such as machining processes (e.g. milling, drilling and turning), in which material is removed in order to remove the material to give each component to be produced its shape.
  • the additive construction principle makes it possible to manufacture geometrically complex structures that cannot be realized or can only be realized at great expense using conventional manufacturing processes, such as the machining processes or primary forming processes (casting, forging) mentioned above (see VDI status report "Additive Manufacturing Processes", September 2014) from the Association of German Engineers, Department of Production Technology and Manufacturing Processes, www.vdi.de/statusadditiv). More detailed definitions of the processes, which are summarized under the generic term "additive processes”, can be found in VDI guidelines 3404 and 3405, for example.
  • the semifinished product obtained after step d) still requires finishing in order to give it the desired properties on the one hand and the required final shape on the other. Finishing includes, for example, mechanical, in particular machining, processing of the semifinished product, and heat treatment, which can consist of hardening and tempering.
  • Alloy powders composed according to the invention in the manner explained above are formed into a raw part (semi-finished product), for example by hot isostatic pressing or another suitable sintering process.
  • the respective alloy powder can be filled into a suitable form, for example a cylindrical capsule, and then at typical pressures of 900-1500 bar (90-150 MPa), in particular 1000 bar (100 MPa), at a temperature of 1050-1250 ° C , in particular 1150 ° C, be held for a sufficient period of time until a solid body is formed.
  • the pressure in hot isostatic pressing is in the range of 102-106.7 MPa and the heating to the target temperature, typically 1150-1153 ° C, which is above a A duration of typically 200-300 min, in particular 245 min, is also typically carried out at a heating rate of 3 K / min - 10 K / min.
  • the respective semi-finished product is heated at a heating rate of typically 5 K / min to a hardening temperature (austenitizing temperature) of 1050-1200 ° C, at which it is kept until it is completely warmed through. Typically 30 - 60 minutes are required for this.
  • the semi-finished products heated in this way are then quenched. They are cooled to room temperature within 5-30 minutes with a suitable quenching medium, for example with water, oil, a polymer bath, moving or still air or, if the cooling is carried out in a vacuum furnace, with gaseous nitrogen.
  • a suitable quenching medium for example with water, oil, a polymer bath, moving or still air or, if the cooling is carried out in a vacuum furnace, with gaseous nitrogen.
  • tempering can be carried out in which the semifinished product is kept at the respective tempering temperature, which is typically 450-550 ° C., for a period of, for example, 90 minutes.
  • the tempering conditions are selected in a manner known per se, depending on the respective hardening temperature and the desired level of hardness, i.e. the desired strength.
  • the heating and cooling rates during tempering are generally of the order of 10 K / min. In contrast to hardening, the heating and cooling speeds during tempering are not critical. Tempering causes the brittle martensite to relax through diffusion of carbon. Together with e.g. V, Cr and Mo this forms the so-called "tempered carbides". This increases the toughness. At the same time, the strength and hardness of the steel material decrease only slightly, since these properties are increased again by the formation of carbide.
  • cylindrical semi-finished products have been produced from four steel materials V10a-V10d according to the invention.
  • the steel matrix of the steel materials V10a, V10b, V10c and V10d each contained (in% by weight) 2.5% C, 0.9% Si, 0.9% Mn, 4.5% Cr, 1.2% Mo and 10.0% V, the remainder iron and unavoidable impurities.
  • the steel material V10a was alloyed with 5% by weight TiC
  • the austenitizing temperature AT, the hardness HRC ("HRC_v”) present before the subsequent heat treatment step, either the tempering temperature ST and the tempering duration St, if a tempering has been carried out, or the soft annealing temperature WT and the soft annealing duration Wt, if a soft annealing has been carried out , the hardness HRC ("HRC_n") after the previous heat treatment step and the density ⁇ of the samples V1 - V8 are given in Table 1.
  • the heating to the respective austenitizing temperature AT took place in a vacuum furnace.
  • the samples V1-V8 were kept at the austenitizing temperature AT for an austenitizing time At. This was followed by cooling to room temperature in a vacuum furnace by applying gaseous nitrogen applied at a pressure of 3.5 bar.
  • samples 1-8 were subjected to either a tempering or a soft annealing treatment. During the tempering treatment, samples 1, 3, 5, 7 were held at the tempering temperature ST for the tempering duration St. This tempering treatment was carried out twice in order to obtain an optimal starting result.
  • samples 2, 4, 6, 8 were held at the soft annealing temperature WT for a period Wt. After the annealing time had elapsed, the furnace was switched off and samples 2, 4, 6, 8 were slowly cooled to room temperature in the switched off furnace. Table 1 sample material added TiC content AT At HRC_v ST St.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)

Claims (14)

  1. Matériau à base d'acier produit par métallurgie des poudres et ayant une matrice d'acier composée comme suit (en % en poids): C: 1,5 - 5,0 %, Si: 0,3 - 2,0 %, Mn: 0,3 - 2,0 %, P: 0 < 0,035 %, S: 0 < 0,35 %, N: 0 < 0,1 %, Cr: 3,0 - 15,0 %, Mo: 0,5 - 2,0 %, V: 6,0 - 18,0 %,
    dans chaque cas, éventuellement un ou plusieurs éléments du groupe « Nb, Ni, Co, W»,
    où chaque teneur en Ni, Co et W est au plus 1,0 % et la teneur en Nb est au plus 2,0 %,
    le reste étant du fer et des impuretés inévitables,
    où des particules dures de TiC sont incorporées dans la matrice d'acier à des teneurs de 2,5 à 30 % en poids.
  2. Matériau à base d'acier selon la revendication 1, caractérisé en ce que, dans le cas de teneurs en Cr allant jusqu'à 8,0 % en poids, la teneur en C de la matrice d'acier correspond, avec un écart d'au plus 0,2 % en poids, à une valeur cible %Ccible, pour laquelle s'applique %Ccible = 0,2 x %V + 0,4 % en poids, %V désignant la teneur en V respective de la matrice d'acier.
  3. Matériau à base d'acier selon la revendication 1, caractérisé en ce que, dans le cas de teneurs en Cr d'au moins 11,0 % en poids, la teneur en C de la matrice d'acier correspond, avec un écart d'au plus 0,2 % en poids, à une valeur cible %Ccible pour laquelle % Ccible = (0,2 x %V + 0,4 % en poids) x 1,3, où %V désigne la teneur en V respective de la matrice d'acier.
  4. Matériau à base d'acier selon la revendication 1, caractérisé en ce que, dans le cas de teneurs en Cr supérieures à 8 % en poids et inférieures à 11 % en poids, la teneur en C de la matrice d'acier est comprise entre les teneurs cibles en %C déterminées selon les revendications 2 et 3.
  5. Matériau à base d'acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Si est d'au moins 0,7 % en poids ou d'au plus 1,5 % en poids.
  6. Matériau à base d'acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Mn est d'au moins 0,7 % en poids ou d'au plus 1,5 % en poids.
  7. Matériau à base d'acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en S est d'au moins 0,035 % en poids.
  8. Matériau à base d'acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Mo est d'au moins 0,9 % en poids ou d'au plus 1,5 % en poids.
  9. Matériau à base d'acier selon l'une des revendications précédentes, caractérisé en ce que, en présence d'un ou plusieurs éléments du groupe « Ni, Co, W », les teneurs en l'élément respectif Ni, Co ou W (en % en poids) sont les suivantes : Ni: 0,2 - 0,4 %, Co: 0,3 - 0,5 %, W: 0,3 - 0,5 %.
  10. Matériau à base d'acier selon l'une des revendications précédentes, caractérisé en ce que les particules de matériau dur sont présentes dans une taille de grain d50 d'au plus 50 µm.
  11. Procédé de fabrication d'un composant constitué d'un acier obtenu selon l'une des revendications précédentes, comprenant les étapes suivantes :
    a) Une poudre d'alliage d'acier est mise à disposition, laquelle se compose de (en % en poids) 1,5 - 5,0 % de C, 0,3 - 2,0 % de Si, 0,3 - 2,0 % de Mn, < 0,035 % de P, < 0,35 % de S, < 0,1 % de N, 3,0 - 15,0 % de Cr, 0,5 - 2,0 % de Mo, 6,0 - 18,0 % de V, dans chaque cas, éventuellement un ou plusieurs éléments du groupe « Nb, Ni, Co, W », où chaque teneur en Ni, Co et W est au plus 1,0 % et la teneur en Nb est au plus 2,0 %, le reste étant du fer et des impuretés inévitables.
    b) La poudre d'alliage d'acier est mélangée à des particules dures de TiC, à condition que la teneur en particules dures de TiC dans le mélange poudre d'alliage d'acier / particules dures obtenu soit de 2,5 à 30 % en poids.
    c) Optionnellement, la poudre d'alliage d'acier ou le mélange poudre d'alliage d'acier / matériau dur est séché.
    d) Un produit semi-fini solide est formé à partir de la poudre d'alliage d'acier ou du mélange poudre d'alliage d'acier/matériau dur par un procédé de frittage, en particulier par pressage isostatique à chaud, ou par un procédé additif.
    e) Le produit semi-fini obtenu est soumis à un traitement de finition pour former le composant.
  12. Procédé selon la revendication 11, caractérisé en ce que, pour l'étape de travail a), les constituants d'alliage de la poudre d'alliage d'acier sont respectivement mis à disposition sous forme de poudre et sont mélangés pour former les poudres d'alliage d'acier.
  13. Procédé selon l'une des revendications 11 ou 12, caractérisé en ce que le traitement de finition (étape de travail e)) comprend un usinage avec enlèvement de matière du produit semi-fini.
  14. Composant qui, dans l'utilisation pratique, effectue des mouvements avec une accélération élevée ou une vitesse élevée, et est fabriqué à partir d'un matériau à base d'acier obtenu selon l'une quelconque des revendications 1 à 10.
EP16200060.8A 2016-11-22 2016-11-22 Matériau en acier contenant des particules dures, produit de la métallurgie des poudres, procédé de production d'un composant à partir d'un tel matériau d'acier et composant ainsi fabriqué Not-in-force EP3323902B1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
EP16200060.8A EP3323902B1 (fr) 2016-11-22 2016-11-22 Matériau en acier contenant des particules dures, produit de la métallurgie des poudres, procédé de production d'un composant à partir d'un tel matériau d'acier et composant ainsi fabriqué
PCT/EP2017/079968 WO2018095928A1 (fr) 2016-11-22 2017-11-21 Matériau à base d'acier fabriqué par métallurgie des poudres, contenant des particules de matériau dur, procédé de fabrication d'un composant d'un tel matériau à base d'acier et composant fabriqué du matériau à base d'acier
US16/349,463 US20200190638A1 (en) 2016-11-22 2017-11-21 Powder-Metallurgically Produced Steel Material Containing Hard Material Particles, Method for Producing a Component from Such a Steel Material, and Component Produced from the Steel Material
JP2019547782A JP2020501027A (ja) 2016-11-22 2017-11-21 硬質材料粒子を含む粉末冶金的に製造された鋼材料、こうした鋼材料から部品を製造する方法、及び鋼材料から製造された部品

Applications Claiming Priority (1)

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EP16200060.8A EP3323902B1 (fr) 2016-11-22 2016-11-22 Matériau en acier contenant des particules dures, produit de la métallurgie des poudres, procédé de production d'un composant à partir d'un tel matériau d'acier et composant ainsi fabriqué

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EP3323902B1 true EP3323902B1 (fr) 2021-09-15

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CN109402488A (zh) * 2018-10-29 2019-03-01 宁波科森净化器制造有限公司 一种尾气转化器外壳
EP3733326A1 (fr) * 2019-04-30 2020-11-04 Deutsche Edelstahlwerke Specialty Steel GmbH & Co. KG Procédé de fabrication d'un composant d'acier selon un procédé de fabrication additive
CN111438356B (zh) * 2020-04-13 2022-02-22 河北晟华新材料科技有限公司 一种用于物理气相沉积的钛铝靶材及其制备方法
US12123464B2 (en) * 2020-12-17 2024-10-22 Aktiebolaget Skf Bearing component and method of manufacturing thereof
CN114318164B (zh) * 2021-03-22 2023-01-20 武汉钜能科技有限责任公司 耐磨耐蚀工具钢
KR20240047123A (ko) * 2022-10-04 2024-04-12 현대자동차주식회사 알루미늄 다이캐스팅용 소결재 및 그 제조방법
CN116676540A (zh) * 2023-04-12 2023-09-01 重庆材料研究院有限公司 一种用于农机装备的高耐磨合金粉末材料

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US4249945A (en) 1978-09-20 1981-02-10 Crucible Inc. Powder-metallurgy steel article with high vanadium-carbide content
US4880461A (en) * 1985-08-18 1989-11-14 Hitachi Metals, Ltd. Super hard high-speed tool steel
JPH03126844A (ja) * 1989-10-12 1991-05-30 Sumitomo Metal Ind Ltd 耐摩耗性に優れた熱間ロール用鋼材
US5238482A (en) * 1991-05-22 1993-08-24 Crucible Materials Corporation Prealloyed high-vanadium, cold work tool steel particles and methods for producing the same
US5679908A (en) 1995-11-08 1997-10-21 Crucible Materials Corporation Corrosion resistant, high vanadium, powder metallurgy tool steel articles with improved metal to metal wear resistance and a method for producing the same

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JP2020501027A (ja) 2020-01-16
US20200190638A1 (en) 2020-06-18
EP3323902A1 (fr) 2018-05-23

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