US20080253919A1 - Powder-Metallurgically Produced, Wear-Resistant Material - Google Patents

Powder-Metallurgically Produced, Wear-Resistant Material Download PDF

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US20080253919A1
US20080253919A1 US11/912,829 US91282906A US2008253919A1 US 20080253919 A1 US20080253919 A1 US 20080253919A1 US 91282906 A US91282906 A US 91282906A US 2008253919 A1 US2008253919 A1 US 2008253919A1
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wear
powder
resistant material
semi
cooling
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Werner Theisen
Andreas Packeisen
Hans Berns
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Koppern Entwicklungs GmbH and Co KG
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Koppern Entwicklungs GmbH and Co KG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals

Definitions

  • the disclosure relates to a powder-metallurgically produced, wear-resistant material from an alloy, as well as to a method for producing the material, the use of said material and a powder material.
  • Wear-resistant alloys on the basis of iron are widely used.
  • the resistance to wear is achieved from the hardness of the martensitic metal matrix and the content of hard carbides, nitrides or borides of the elements chromium, tungsten, molybdenum, vanadium, niobium or titanium.
  • This group includes cold work steel and high-speed tool steels, as well as white cast iron and hardfacing alloys.
  • Powder-metallurgical steel alloys were developed when striving for fine carbides, their homogenous distribution and high contents, in order to improve the resistance to wear.
  • the starting powder of these materials is an alloyed powder that is created by atomizing a melt.
  • Normally powders of this type are filled into thin sheet metal capsules that are compacted into a dense body after the evacuation and seal welding in special autoclaves, using the hot isostatic pressing (HIP) technique at a temperature below the melting point and at an isostatic gas pressure of up to 2,000 bar.
  • HIP hot isostatic pressing
  • the compacted capsules are reworked into semi-finished products of tool steel that are available on the market in various dimensions.
  • the hardening consists of austenitizing and cooling at such a speed that predominantly a hard martensitic structure is formed. As the wall thickness of the workpiece increases, the cooling speed needed for this is no longer reached in the core and the high degree of hardness of the martensite can be regulated only down to a certain depth in the workpiece. This is called the effective hardening depth. In this case, the core is not through-hardened.
  • HIP technology can be used for more than just the production of semi-finished products made of powder-metallurgically produced steel; it is also suitable for applying a layer produced from powder with a thickness in the mm to cm range onto an economical, usually resistant steel substrate.
  • This technology known as HIP cladding, is being more and more widely used for the production of components that are subject to heavy wear and that are used in processing technology and polymer processing.
  • Some examples of substances used in this case as wear-resistant layer substances are atomized steel powder, to which hard material powder is additionally added in some cases, with a view to a high level of wear-resistance.
  • the objective of this heat treatment is the martensitic through-hardening of the layer substance, which, in operation, is largely consumed by wear and which consequently must be through-hardened. Because of the high risk of cracks and distortions in alloys containing hard material and the sudden cooling in water or oil, these cooling media are ruled out, particularly in the case of thick wall thicknesses, because of the associated large thermal tensions. For this reason, there is a demand for layer substances that can be converted to the martensite phase that is needed for a high level of wear-resistance, even in the case of the slow cooling of large composite components, e.g., in the air, vacuum ovens with nitrogen pressure ⁇ 6 bar or in the HIP system.
  • the steel powders known today are not suitable for this purpose, because they have been optimised for semi-finished products and workpieces with smaller wall thicknesses.
  • the object of the present disclosure is therefore to provide alloys for the production of materials that allow for their matrix to be converted into hard, wear-resistant martensite, even in the event of very slow cooling.
  • a wear-resistant material comprising an alloy that contains: 1.5-5.5 wt. % carbon, 0.1-2.0 wt. % silicon, max. 2.0 wt. % manganese, 3.5-30.0 wt. % chromium, 0.3-10 wt. % molybdenum, 0-10 wt. % tungsten, 0.1-30 wt. % vanadium, 0-12 wt. % niobium, 0.1-12 wt. % titanium and 1.3-3.5 wt. % nickel, the remainder being comprised of iron and production-related impurities, whereby the carbon content fulfils the following condition:
  • the alloy content in the metal matrix is decisive for achieving the martensitic structure even in the event of slow cooling.
  • all alloy elements that are dissolved in the metal matrix and that shift the “perlite notch” to the right in the time-temperature transformation diagram (TTT diagram) shown in the following have a favorable effect.
  • this includes the elements chromium, molybdenum and vanadium, but particularly nickel, which is used in the alloys according to the disclosure for this reason.
  • the austenite-stabilizing effect of nickel is known, it has not been used to any appreciable degree in the PM alloys known until now.
  • the regulation of a desired nickel content in the metal matrix is relatively simple, because nickel does not participate in the carbide formation necessary for a high level of wear-resistance. Because of the presence of the carbides deposited from the melt, the nickel content is somewhat higher in the matrix than in the alloy. The nickel content primarily acts in the metal matrix and increases the austenite range as the content increases. It can be assumed that the nickel content in the metal matrix per volume percent of carbide lies above the content of nickel in the alloy by 0.025 wt %. The austenite-stabilizing effect of the nickel makes it possible to convert the alloys into the hard, wear-resistant martensite, even in the case of very slow cooling.
  • the carbon is particularly significant for the austenite stabilization, but particularly due to the fact that this is bound in various carbide types to various degrees, it must be related to the remaining alloy elements with a view to the desired hardenability.
  • the C content calculated in the summands S1 and S2 stands for the proportion of carbon that is indissolubly bound in the various carbide types.
  • the summand S3 represents a portion of carbon that can be dissolved, if there is sufficient molybdenum content in the alloy, by means of the selection of the austenitizing temperature in the metal matrix. As the hardening temperature increases, more molybdenum-containing carbides are dissolved. As a result, the austenite becomes richer in molybdenum and carbon, which expand the austenite range and consequently increase the critical cooling rate.
  • the factors a, b and c were introduced because the carbide formation functions with each of the elements Cr, Mo, V and W in a certain bandwidth.
  • TTT diagram time-temperature transformation diagram
  • the material according to the disclosure can be economically hardened by known measures, whereby even thick-walled components are through-hardened without increased costs.
  • the wear-resistant material can be made of an alloy with the chemical composition: 1.5-5.5 wt. % carbon, 0.1-2.0 wt. % silicon, max. 2.0 wt. % manganese, 3.5-30.0 wt. % chromium, 0.3-10 wt. % molybdenum, 0-10 wt. % tungsten, 0.1-30 wt. % vanadium, 0-12 wt. % niobium, 0.1-12 wt. % titanium and 1.3-3.5 wt. % nickel, the remainder being comprised of iron and production-related impurities, whereby the carbon content fulfils the following condition:
  • the proportion of vanadium in the alloy of the wear-resistant material can be less than 11.5 wt. %, preferably less than 9.5 wt. %, and particularly preferably less than 6.0 wt. %. In this case, it is particularly preferred if the volume content of the vanadium carbide in the alloy amounts to less than 18.5 vol. %. Corresponding ranges have proven particularly suitable in the implementation of the disclosure.
  • the alloy of the wear-resistant material can comprise 2.0-2.5 wt. % carbon, max. 1.0 wt. % silicon, max. 0.6 wt. % manganese, 12.0-14.0 wt. % chromium, 1.0-2.0 wt. % molybdenum, 1.1-4.2 wt. % vanadium and 2.0-3.5 wt. % nickel, the remainder being comprised of iron and unavoidable impurities.
  • This specific composition has proven particularly satisfactory in practice.
  • the alloy can advantageously additionally have 1-6 wt. % Co.
  • the alloy can additionally have 0.3 to 3.5 wt. % N.
  • the addition of nitrogen has proven advantageous.
  • the proportion of nickel can advantageously amount to between 2.0 and 3.5%.
  • a corresponding nickel content has proven to be particularly suitable, particularly in quenching the material with static air.
  • the Ni content can lie between 1.3 and 2.0 %.
  • An alloy with a corresponding nickel content is particularly suitable for cooling by means of gas ⁇ 6 bar.
  • a Ni content of 1.0 to 1.3% is suitable.
  • S2K (Mo+W/2+Cr ⁇ b ⁇ 12)/5 with 6 ⁇ b ⁇ 8 and Cr>12.
  • This condition can particularly be used in the case that a corrosion-resistant alloy is desired.
  • the summand S2 of the above equation the summand S2K is used, which takes the necessary chromium content into consideration.
  • the wear-resistant material can be produced by means of a method whereby first a melt is produced and the melt is further processed by means of one of the following methods: atomization of the melt into a powder or spray compaction of the melt.
  • the material according to the disclosure can therefore be produced by means of various methods, and so allows, firstly, the manufacture of powders and, secondly, by the use of spray compaction, the production of a very wide range of semi-finished products, as well as end products.
  • Another preferred embodiment comprises a production method in which first a melt is formed and then this melt is cast into a semi-finished product, whereby the semi-finished product is further processed for creating chips and/or powder.
  • the powder can advantageously be compacted into a semi-finished product or end product under high pressure and/or increased temperature.
  • a number of possible compaction methods again present themselves here, with cold isostatic pressing, uniaxial pressing, extrusion, powder forging, hot isostatic pressing, diffusion alloying and sintering being named as examples. In practice, it is consequently possible to select a suitable method without limitation in order to produce an end product.
  • the powder can also advantageously be further processed by means of thermal injection.
  • the semi-finished product or an end product can be heated to the hardening temperature and subsequently quenched.
  • a method for quenching can be chosen from the group comprising: quenching in an oil bath, salt bath or polymer bath, quenching in a fluidized bed or drizzle and low and high pressure gas quenching.
  • the semi-finished product or an end product can be heated to the hardening temperature and subsequently cooled.
  • the preferred methods for cooling include cooling in slightly moving air, cooling in static air, oven cooling in a standard atmosphere or inert gas and cooling in an HIP system.
  • the quenching or cooling in this connection primarily serves the purposes of hardening.
  • the cooling can advantageously be interrupted by an isothermal maintenance stage (interrupted hardening).
  • tempering in the temperature range 150-750° C. can be performed one or more times, in order to achieve a desired combination of characteristics with respect to hardness and toughness.
  • the material according to the disclosure is used as a powder.
  • the material can be converted into a desired semi-finished product form or end form by means of a multitude of various methods. This also includes use in the form of a layer element of composite components, particularly also as a matrix powder for hard material metal matrix composites.
  • corresponding rolls are for the purpose of crush-ing, briquetting and compacting natural, chemical or mineral feedstocks, particularly cement clinker, ore and stone. Furthermore, corresponding rolls can also be used for the purpose of the movement and transport of products that promote wear, particularly of metallic rolled and forged products.
  • a further application area is the use of the wear-resistant material for producing rings which are arranged on solid or hollow roll bodies.
  • the wear-resistant material for producing rings which are arranged on solid or hollow roll bodies.
  • only an outer layer is made of the wear-resistant material, not the entire roll.
  • Corresponding rolls can be deployed in the same scope of functions mentioned above.
  • Solid or segmented rings made of the wear-resistant material can be advantageously arranged on solid or hollow rolls by means of shrinking them on. This is a proven method in practice for placing the rings.
  • the wear-resistant material can advantageously be used for producing thick-walled or compact components.
  • Corresponding components can, for example, be used in the area of wear protection in extraction and processing, as well as in the transport of natural, chemical or mineral goods, as well as metallic goods, polymer goods and ceramic goods.
  • the disclosure relates to a powder for the production of a wear-resistant material comprising: 1.5-5.5 wt. % carbon, 0.1-2.0 wt. % silicon, max. 2.0 wt. % manganese, 3.5-30.0 wt. % chromium, 0.3-10 wt. % molybdenum, 0-10 wt. % tungsten, 0.1-30 wt. % vanadium, 0-12 wt. % niobium, 0.1-12 wt. % titanium and 1.3-3.5 wt. % nickel, the remainder being comprised of iron and production-related impurities, whereby the carbon content fulfils the following condition:
  • S1 (Nb+2(Ti+V ⁇ 0.9))/a
  • S2 (Mo+W/2+Cr ⁇ b)/5
  • S3 c+(TH ⁇ 900) ⁇ 0.0025, where 7 ⁇ a ⁇ 9, 6 ⁇ b ⁇ 8, 0.3 ⁇ c ⁇ 0.5 and 900° C. ⁇ TH ⁇ 1,220° C.
  • the disclosure relates to a powder for the production of a wear-resistant material with the following chemical composition: 1.5-5.5 wt. % carbon, 0.1-2.0 wt. % silicon, max. 2.0 wt. % manganese, 3.5-30.0 wt. % chromium, 0.3-10 wt. % molybdenum, 0-10 wt. % tungsten, 0.1-30 wt. % vanadium, 0-12 wt. % nio-bium, 0.1-12 wt. % titanium and 1.3-3.5 wt. % nickel, the remainder being comprised of iron and production-related impurities, whereby the carbon content fulfils the following condition:
  • the powder can advantageously be used as a semi-finished product.
  • One result of this is to make it possible for a buyer to convert the semi-finished product into the desired end form.
  • a further application area is the use of the powder in powder form or as a semi-finished product as a layer substance or layer element of composite components.
  • Another further application area is the use of the powder as a matrix powder for hard material metal matrix composite elements.
  • Corresponding hard material metal matrix composite elements are particularly suitable for the production of semi-finished products and composite components.
  • FIG. 1 a and FIG. 1 b Time-temperature transformation diagram (TTT diagram) of an alloy according to the disclosure (PM1) as well as a commercially available PM steel;
  • FIG. 2 Hardness tempering temperatures of an alloy according to the disclosure (PM1) as well as a commercially available PM steel (X230CrVMo13-4);
  • FIG. 3 a The structure of a commercially available PM steel (X230CrVMo13-4);
  • FIG. 3 b A micrograph of an alloy according to the disclosure (PM).
  • the heat treatment characteristic of hardenable steels and alloys is generally evaluated on the basis of time-temperature transformation diagrams (TTT diagrams).
  • TTT diagrams time-temperature transformation diagrams
  • the TTT diagram shown in FIG. 1 serves to compare an alloy according to the disclosure with a commercially available powder metallurgical steel with the composition X230CrVMo13-4 (material no. 1.2380). Because the martensite formation for the mentioned material group is indispensable, the cooling from the hardening temperature (in this case, 1,050° C.) must take place so quickly that the ferrite and perlite soft structure phases are avoided in the layer substance. For this reason, the cooling rate deserves increased attention, which is described in heat treatment technology by the cooling time from 800° C. to 500° C.
  • the cooling parameter ⁇ which is noted as a numerical value for several cooling curves in FIG. 1 , is formed by dividing the cooling time (in seconds) by 100.
  • the mode of operation of the alloy according to the disclosure and particularly the addition of nickel and molybdenum can be described using the TTT diagram in FIG. 1 b , which was determined for an alloy variant PM1 with 12.5% Cr, 3% Ni, 1.5% V, 2% Mo, 2.5% C and 0.2% Ti, with the remainder iron (X250CrNiVMo13-3-2-2).
  • the perlite field is shifted far to the right on the logarithmically depicted time axis due to the addition of nickel and molybdenum, and the beginning of the martensitic transformation (martensite start temperature) is shifted downwards.
  • the addition of nickel and molybdenum, in conjunction with a high hardening temperature leads to an increase in the residual austenite, because the martensite finish temperature is pressed further down below room temperature.
  • FIG. 1 b shows a macro-hardness between 763 and 814 HV30 for such cooling of the alloy PM1, in comparison to the hardness of the conventional powder-metallurgical steel of only 345 HV30. Therefore, considerably larger layer or wall thicknesses can also be through-hardened in air, without it being necessary to call on brusque quenching means (Table 1).
  • the vacuum hardening with compressed gas quenching frequently used today can be replaced with the considerably more economical and also safe cooling in static air.
  • the alloys according to the disclosure open up the possibility of martensitically hardening even thick-walled components with the normally existing slow cooling from the HIP temperature ( ⁇ approximately 130) (see FIG. 1 b ). By means of this measure, the process of the subsequent, expensive vacuum hardening can be completely spared. Because in many HIP systems, the cooling can also take place under pressure, isostatic pressure can additionally be used against the risk of cracks, which increases with the hard-phase content.
  • FIG. 2 shows hardness tempering curves for the PM steel X230CrVMo13-4 and for a variant PM1 alloyed according to claim 1 .
  • the commercially available powder-metallurgical steel was hardened in oil with ⁇ >9 because of the desired quick cooling
  • the steel PM1 according to the disclosure was cooled with a value of approximately 80 for ⁇ .
  • the hardness after quenching is somewhat less in the alloy according to the disclosure than in the conventional comparison steel due to the high residual austenite content, the same hardness is reached as in the conventional steel by means of repeated tempering in the range of the secondary hardness maximum and the residual austenite transformation and special carbide precipitation associated with this.
  • FIG. 3 depicts corresponding structures of the corresponding commercially available steel and the alloy according to the disclosure.
  • Cooling Designation Alloy parameter Air Oil 1.2380 X230CrVMo13-4 9 65 320 PM1 X250CrNiVMo13-3-2-2 55 300 900 1.2380 X230CrVMo13-4 9 65 320 PM1 X250CrNiVMo13-3-2-2 55 300 900

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US11/912,829 2005-04-29 2006-05-02 Powder-Metallurgically Produced, Wear-Resistant Material Abandoned US20080253919A1 (en)

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DE102005020081A DE102005020081A1 (de) 2005-04-29 2005-04-29 Pulvermetallurgisch hergestellter, verschleißbeständiger Werkstoff
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PCT/EP2006/004086 WO2006117186A2 (de) 2005-04-29 2006-05-02 Pulvermetallurgisch hergestellter, verschleissbeständiger werkstoff

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US8778259B2 (en) 2011-05-25 2014-07-15 Gerhard B. Beckmann Self-renewing cutting surface, tool and method for making same using powder metallurgy and densification techniques
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US20090010795A1 (en) * 2006-04-13 2009-01-08 Uddeholm Tooling Aktiebolag Cold-Working Steel
US8623108B2 (en) * 2009-01-14 2014-01-07 Boehler Edelstahl Gmbh & Co Kg Wear-resistant material
US20100192476A1 (en) * 2009-01-14 2010-08-05 Boehler Edelstahl Gmbh & Co Kg Wear-resistant material
US20120196149A1 (en) * 2011-01-31 2012-08-02 Fifield Robin William Sinclair Hardbanding alloy
US9540711B2 (en) * 2011-01-31 2017-01-10 Robin William Sinclair FIFIELD Hardbanding alloy
US8778259B2 (en) 2011-05-25 2014-07-15 Gerhard B. Beckmann Self-renewing cutting surface, tool and method for making same using powder metallurgy and densification techniques
RU2477200C1 (ru) * 2011-07-01 2013-03-10 Государственное образовательное учреждение высшего профессионального образования "Оренбургский государственный университет" Способ термической обработки спеченных изделий
WO2013128017A1 (en) 2012-03-01 2013-09-06 Phoenix Product Development Limited Toilet pan body and its method of manufacturing
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US20150007704A1 (en) * 2013-07-08 2015-01-08 Branson Ultrasonics Corporation Ultrasonic steel horn for tire cutting and method of manufacturing
CN103938112A (zh) * 2014-04-10 2014-07-23 铜陵南江鑫钢实业有限公司 一种超高碳钢及其制备方法
CN109576604A (zh) * 2019-01-30 2019-04-05 沈阳大陆激光工程技术有限公司 一种用于激光制造的抗冲击耐磨材料
CN113862575A (zh) * 2021-09-29 2021-12-31 重庆长安汽车股份有限公司 一种铌钒复合微合金化热成形钢及其生产方法

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WO2006117030A1 (de) 2006-11-09
WO2006117186A2 (de) 2006-11-09
EP1882050B1 (de) 2016-04-13
SI1882050T1 (sl) 2016-08-31
DE102005020081A1 (de) 2006-11-09
DK1882050T3 (en) 2016-08-01
WO2006117186A3 (de) 2007-02-01
US20130084462A1 (en) 2013-04-04
US9410230B2 (en) 2016-08-09

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