EP1917376B1 - Powder metallurgically manufactured steel, a tool comprising the steel and a method for manufacturing the tool - Google Patents

Powder metallurgically manufactured steel, a tool comprising the steel and a method for manufacturing the tool Download PDF

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EP1917376B1
EP1917376B1 EP06769668.2A EP06769668A EP1917376B1 EP 1917376 B1 EP1917376 B1 EP 1917376B1 EP 06769668 A EP06769668 A EP 06769668A EP 1917376 B1 EP1917376 B1 EP 1917376B1
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Prior art keywords
steel
tool
carbides
contents
niobium
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German (de)
English (en)
French (fr)
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EP1917376A1 (en
EP1917376A4 (en
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Stefan Sundin
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Erasteel Kloster AB
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Erasteel Kloster AB
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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
    • 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
    • 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
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium 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

Definitions

  • the invention relates to a new steel, preferably a powder metallurgically manufactured high speed steel having improved grindability and being suitable for tools for chip removal, preferably coated tools such as gear cutting tools, taps and end-cutters with shaving separators for which a large toughness is required in combination with a good hardness, especially hot hardness.
  • tools for hot-working such as dies for extrusion of aluminium profiles and rollers for hot-rolling, advanced machine elements and press rollers, i.e. tools for the stamping of patterns or profiles in metals etc.
  • Yet another field of application can be cold-working tools for which a good grindability and a good hardness are important properties.
  • the steel has a high tempering resistance, which means that it should be able to be exposed to high temperatures for a long time without losing the hardness that the steel has gained from hardening and tempering.
  • this hardness does not need to be extremely high, suitably in the magnitude of 50-55 HRC.
  • the primary properties are a higher hardness and strength in combination with a high toughness and there are also strict requirements on homogeneous properties.
  • the hardness after tempering may typically lie in the range of 55-60 HRC.
  • the invention also relates to tools for hot working or chip cutting removal or cold working, or an advanced machine element manufactured from the steel, as well as a method for the manufacturing of such.
  • One type of steel that is used for cutting operations is the high speed steel that is marketed under the trade name ASP® 2052 and that is characterised by the following nominal composition in % by weight: 1.6 C, 4.8 Cr, 2.0 Mo, 10.5 W, 8.0 Co, 5.0 V, balance iron and unavoidable impurities.
  • Another high speed steel is ASP® 2030 having the nominal composition 1.28 C, 4.2 Cr, 5.0 Mo, 6.4 W, 3.1 V, 8.5 Co, balance iron and unavoidable impurities
  • Yet another high speed steel is ASP® 2060 having the nominal composition 2.3 C, 4.2 Cr, 7.0 Mo, 6.5 W, 6.5 V, 10.5 Co, balance iron and unavoidable impurities, All contents are in % by weight.
  • US5403372 discloses a vane material, vane and method of producing a vane to be used in a compressor using a substitute freon, improving the wear resistance thereof.
  • the vane material has a composition consisting of by weight: 1.0-2.5% of C; not more than 1.5% of Si; not more than 1.0% of Mn; 3-6% of Cr; one or two of not more than 20% W and not more than 12% Mo where "W+2Mo" being 15-28%; 3.5-10% of one or two of V and Nb; and the balance of Fe and incidental impurities.
  • Carbides are uniformly dispersed in the matrix thereof where their average diameter does not exceed 1.5 ⁇ m and the maximum diameter thereof does not exceed 6 ⁇ m.
  • a method of producing a vane is also disclosed, in which an atomized powder having the composition as described is compacted and it is then subjected to hot working, or to hot working and cold working.
  • EP0483668 discloses a high speed tool steel produced by sintering powder, consisting essentially, by weight, of more than 1.5% but not more than 2.2% C, not more than 1.0% Si, not more than 0.6% Mn, 3.0 to 6.0% Cr, W and/or Mo in which the content of W + 2Mo is in the range of 20 to 30% and in which the ratio of W/2Mo is not less than 1, not more than 5.0% V, 2.0 to 7.0% Nb, the ratio of Nb/V being not less than 0.5, and the balance Fe and incidental impurities, the value of C-Ceq, which Ceq is defined by 0.24 + 0.033 X W + 0.063 X Mo + 0.2 X V + 0.1 X Nb, being in a range of -0.20 to 0.05, the density of carbides having grain size of 2 to 5 ⁇ m being in a range of 10,000 to 30,000 pieces/mm 2 .
  • JPH05163551 describes a powder high-speed tool steel resistant to high-temperature capable of coping with the high speed at which the tool is used and also having high toughness.
  • the powder high-speed tool steel contains by weight, 0.7-2.0% C, ⁇ 1.0% Si, ⁇ 0.6% Mn, 3.0-6.0% Cr, 14-20% of (W+2Mo), ⁇ 5.0% V, 2.0-7.0% Nb where Nb/V ⁇ 0.5, ⁇ 15.0% Co and the balance Fe with inevitable impurities.
  • the C eq 0.24+0.033W+0.063Mo+0.2V+0.1Nb is controlled to -0.30 to 0.05.
  • WO00/26427 discloses a steel with a high wear resistance, high hardness and good notched bar impact strength, useful for the manufacture of products, in the use of which at least some of said features are desirable, preferably for the manufacture of tools intended to be used at temperatures up to at least 500 °C.
  • the steel is produced powder-metallurgically and consists in percent by weight essentially of 0.55-0.65 C, 0.7-1.5 Si, 0.1-1.0 Mn, 3.5-4.5 Cr, 1.5-2.5 Mo, 1.5-2.5 W, 1.2-1.8 V, 0-0.2 Nb, balance iron and impurities in normal amounts.
  • the steel After hardening and tempering the steel contains 1.5-2.5 percent by volume of MC carbides, in which M consists essentially only of vanadium, said carbides being evenly distributed in the steel matrix.
  • the invention also relates to use of the steel, manufacture and products manufactured from the steel.
  • the object of the invention is to provide a novel steel, preferably a high speed steel, having the same beneficial properties as the above mentioned prior art steels but for which the grindability of the material has been improved. More specifically, the steel should have the following properties:
  • carbon should exist at a content of at least 1.1 % and 2.3 % at the most, preferably at least 1.4 % and 2.0 % at the most, and even more preferred between 1.60 and 1.90 %, in order to, when dissolved in the martensite, give the material a hardness in the hardened and tempered condition that is suitable for its purposes.
  • Carbon and nitrogen should furthermore, in combination with niobium and vanadium, contribute to an adequate amount of primary precipitated MX-carbides, - nitrides, -carbonitrides of the type (Nb,V)X, and, in combination with tungsten, molybdenum and chromium to contribute to the achievement of an adequate amount of primary precipitated M 6 X-carbides, -nitrides, -carbonitrides in the matrix.
  • Such hard phase particles are mentioned as carbides in the continued description, but it should be understood that if the steel contains nitrogen the term carbides also relates to nitrides and/or carbonitrides. The purpose of such carbides is to give the material its desirable resistance to wear.
  • the steel contains between 1.65 and 1.80 % carbon and nitrogen, which, in combination with a balanced amount of other alloying elements, in particular silicon, chromium, vanadium and niobium, will give the steel a property profile well suitable for its purpose, which can be achieved by a standard manufacturing process, i.e. the manufacturing does not require any extraordinary efforts but proceeds in accordance with standard methods.
  • the nitrogen content is not more than 0.1 %, but by the powder metallurgical manufacturing technique it is possible to dissolve much higher contents of nitrogen in the steel.
  • One embodiment of the steel is accordingly characterised by the steel containing a large amount of nitrogen, 2,3 % at the most, which can be obtained by solid phase nitration of the manufactured powder.
  • nitrogen can replace carbon in the hard materials that are to be part of the steel of the final tool.
  • the steel will also be easier to temper, which means that the tempering temperature can be lowered, which can be advantageous. Contents lower than 1.1 % carbon + nitrogen will not result in adequate hardness and resistance to wear, while contents of more than 2.3 % may lead to brittleness problems.
  • Silicon is added to the steel at a content of at least 0.1 % in order to improve the steel's fluidity, which is important in the melt metallurgical process.
  • the steel melt will be more fluid, which is important in order to avoid clogging in connection with granulation.
  • the silicon content should be at least 0.2 % and even more preferred at least 0.4 %.
  • Silicon also contributes to increased carbon activity an in a silicon alloyed embodiment it can be present in amounts of up to about 2 %.
  • the steel should suitably not contain more than 1.2 % Si as the risk of formation of large M 6 X-carbides and impaired hardness in the hardened condition will be larger at contents there above, which means that it is even more preferred to limit the silicon content to not more than 1.0 %.
  • the silicon content is between 0.55 % and 0.70 %, which, in addition to the abovementioned advantages, has proven to result in a steel that in combination with the carbon content preferred for the steel is easy to heat treat. By that it is meant that the steel can be heat treated within a broad temperature range while retaining its property profile, which gives advantages in manufacturing.
  • Manganese can also be present primarily as a residual product from the metallurgical melt process in which manganese has the known effect of putting sulphuric impurities out of action by the formation of manganese sulphides and for this purpose it should be present in the steel at a content of at least 0.1 %.
  • the maximum content of manganese in the steel is 3.0 % but preferably the content of manganese is limited to a maximum of 0.5 %.
  • the steel contains 0.2 to 0.4 % Mn.
  • Sulphur may be present in the steel as a residual product from the manufacturing of the steel, at contents of up to 800 ppm, without affecting the mechanical properties of the steel. Sulphur can be deliberately added as an alloying element, up to 1 % at the most, thus contributing to improved machinability and workability. In one embodiment of the invention, having sulphur deliberately added for this purpose, the sulphur content should be between 0.1 and 0.3 % and the content of manganese should then be chosen to be somewhat higher than in the non-sulphur alloyed embodiment, suitably from 0.5 % to a maximum of 1.0 %.
  • phosphorus may be present in the steel as a residual product from the manufacturing of the steel, at contents of up to 800 ppm, without affecting the mechanical properties of the steel.
  • Chromium should exist in the steel at a content of at least 3 %, preferably at least 3.5 %, in order to, when dissolved in the matrix of the steel, contribute to the steel achieving adequate hardness and toughness after hardening and tempering. Chromium can also contribute to the resistance to wear of the steel by being included in primarily precipitated hard phase particles, mainly M 6 X-carbides. Also other primarily precipitated carbides contain chromium, however not to the same extent. Too much chromium will however result in a risk of residual austenite that can be hard to convert. By deep freezing of the material, the residual austenite content can be eliminated or at least minimized.
  • the steel can be allowed a content of chromium of up to about 20 % but preferably the content of chromium is limited to a maximum of 12 %.
  • the steel need not contain more than 6 % in order to achieve the desired property profile.
  • the steel contains between 3.5 and 4.5 % Cr and most preferred between 3.8 and 4.2 % Cr.
  • Molybdenum and tungsten will, just like chromium contribute to the matrix of the steel getting adequate hardness and toughness after hardening and tempering. Molybdenum and tungsten can also be included in primarily precipitated carbides of the M 6 X-type of carbides and as such it will contribute to the resistance to wear of the steel. Also other primarily precipitated carbides contain molybdenum and tungsten, however not to the same extent. The limits are chosen in order to, by adaptation to other alloying elements, result in suitable properties. In principle, molybdenum and tungsten can partially or completely replace each other, which means that tungsten can be replaced by half the amount of molybdenum, or molybdenum can be replaced by double the amount of tungsten.
  • the total content of molybdenum + tungsten should be in the range of 5 to 20 %, more preferred not more than 15 %. Properties suitable for the purpose will be achieved in combination with other alloying elements at a content of between 9 and 12 % (Mo + W/2). Within these ranges the content of molybdenum should, in a preferred embodiment, be chosen in the range of 4.0 to 5.1 % and the content of tungsten should suitably be chosen in the range of 5.0 to 7.0.
  • the nominal content of molybdenum is 4.6 % and for tungsten it is 6.3 %.
  • cobalt in the steel depends on the intended use of the steel.
  • the steel should not contain deliberately added cobalt, since cobalt reduces the toughness of the steel and the risk of chipping in use of the tool.
  • the hardness in a soft annealed condition will increase with an increased content of cobalt and at contents above about 14 % the tools become markedly difficult to machine, i.e. to turn, mill, drill, saw etc.
  • the steel is to be used in chip cutting tools, for which hot hardness is of prominence, it is however suitable for it to contain considerable amounts of cobalt, which in that case can be allowed at contents of up to 20%, but a desired hot hardness can be achieved at a content of cobalt in the range of 7 to 14 %.
  • the steel according to the invention should even more preferred contain between 8.0 and 10.0 % Co and even more preferred between 8.8 and 9.3 % Co.
  • Niobium is an element that plays an important role in the steel according to the invention. It is previously known that small additions of niobium, of up to 1 %, can contribute in keeping down the size of carbides, which is positive inter alia for the toughness and hardness of the material. According to previously known arguments, niobium may replace vanadium. This will however affect the resistance to wear and the material will also be hard to grind, especially if the steel contains niobium and/or vanadium at contents of about 4 % or more.
  • the total content of niobium and vanadium on the one hand should be balanced in relation to the ratio between the content of niobium and vanadium (Nb/V) on the other hand, such that the content of those elements as well as the ratio them between will lie within an area that is defined by the coordinates A, B, C in the system of coordinates in Fig. 1 .
  • the total content of these elements (Nb+V) and the ratio them between (Nb/V) is balanced within an area that is defined by the coordinates D, E, F, and even more preferred within an area that is defined by the coordinates G, H, I, where: [(Nb+V); (Nb/V)]
  • a steel according to the invention will get less growth of MX-carbides in the various hot-working operations that the steel undergoes during manufacturing, such as HIP:ing, forging, rolling, the higher the ratio of Nb/V of the steel.
  • a steel can be provided that fulfils the highly put demands on toughness and hardness in combination with a high yield point, a high fatigue strength, a high flexural strength and a relatively good resistance to wear, and that also has improved grinding properties. This is achieved if the steel is given a composition according to present claim 1, where the composition has been balanced in respect of the total content of niobium and vanadium in combination with a certain ratio between niobium and vanadium.
  • the total content of niobium and vanadium should fulfil the condition 4.0 ⁇ Nb + V ⁇ 7.0, preferably 4.25 ⁇ Nb + V ⁇ 6.7 and even more preferred 4.5 ⁇ Nb + V ⁇ 6.4, at the same time as the ratio between niobium and vanadium should fulfil the condition 0.55 ⁇ Nb/V ⁇ 4.0, preferably 0.55 ⁇ Nb/V ⁇ 3.5 and even more preferred 0.55 ⁇ Nb/V ⁇ 3.0.
  • the steel should contain 2.0 to 2.3 % Nb and 3.1 to 3.4 % V.
  • the steel should have a content of MX-carbides of not more than 15 % by volume, preferably not more than 13 % by volume, and even more preferred not more than 11 % by volume, where at least 80 %, preferably at least 90 %, and even more preferred at least 95 % of the MX-carbides have a carbide size in the longest extension of the carbide of not more than 3 ⁇ m, preferably not more than 2.2 ⁇ m, and even more preferred not more than 1.8 ⁇ m.
  • the composition of the steel should also be balanced in respect of the M 6 X-carbide-forming elements chromium, molybdenum and tungsten, such that the content in the steel of M 6 X-carbides will be not more than 15 % by volume, preferably not more than 13 % by volume and even more preferred not more than 12 % by volume, where at least 80 %, preferably 90 %, and even more preferred at least 95 % of the M 6 X-carbides have a carbide size in the longest extension of the carbide of not more than 4 ⁇ m, preferably not more than 3 ⁇ m, and even more preferred not more than 2.5 ⁇ m.
  • the steel according to the invention should not contain any deliberately added additional alloying elements. Copper, nickel, tin and lead and carbide-formers such as titanium, zirconium and aluminium may be allowed at a total content of not more than 1 %. Besides these and the above mentioned elements, the steel contains no other elements than unavoidable impurities and other residual products from the metallurgical melt treatment of the steel.
  • Table 1 Chemical composition in % by weight for the examined steels; balance iron and impurities at normal contents Steel C Si Mn Cr Mo W Co V Nb Nb/V A 1.74 0.60 0.31 3.95 4.07 4.15 10.5 3.97 1.87 0.47 B 1.85 0.62 0.39 4.23 5.05 7.18 12.0 3.50 1.67 0.48 C 1.77 0.56 0.29 3.94 4.99 5.09 0.63 3.94 1.96 0.50 D 1.86 0.63 0.40 4.20 7.02 7.14 12.0 3.25 1.74 0.54 E 1.98 0.41 0.28 2.98 2.99 1.14 7.80 4.08 2.63 0.64 F 1.73 0.62 0.39 4.20 6.99 7.00 11.9 2.63 1.98 0.75 G 1.92 0.41 0.30 4.28 1.00 3.24 8.33 3.76 3.25 0.86 H 1.28 0.6 0.3 4 5 6.4 8.5 3.1 - 0 I 2.30 0.6 0.3 4.2 7.0 6.5 10.5 6.5 - 0
  • Powder was manufacture from the steels by gas atomizing.
  • the respective steel powders were consolidated by fast hot isostatic pressing, so called HIP/QIH, in small test capsules on top of larger production capsules.
  • Samples were taken out from the small test capsules, which samples were heat treated in several ways in order to simulate typical conditions for production, according to Table 2 below:
  • Table 2 Heat treatment for simulation of typical conditions for production in the ASP process Heat treatment Temperature (°C), Dwell time (h) 0 1150/2h 1 1150/2h + 1100/12h 2 1150/2h + 1130/3h 3 1150/2h + 1130/6h 4 1150/2h + 1130/12 h 5 1150/2h + 1150/3h 6 1150/2h + 1100/12h + 1130/6h +1150/3h
  • Fig. 2 shows a graph over the size of MX-carbides for heat treatment no. 6.
  • steels with an addition of niobium have been marked by solid black dots, while steel without addition of niobium have been marked by rings. It can be seen in the figure 2 that the MX-carbides for Nb-containing steels are considerably smaller in size than they are in steels without addition of Nb.
  • the maximum content at which an addition of niobium has a positive effect on the size of MX-carbides varies in dependence of dwell time and temperature during processes such as HIP:ing, rolling and forging, at temperatures that are typical to high speed steels.
  • One conclusion from the investigation is that for a steel having a content of MX-carbides of not more than 15 % by volume, preferably not more than 13 % by volume, and even more preferred not more than 11 % by volume, the addition of niobium seems to be advantageous, while the addition of niobium on the contrary seems to result in larger MX-carbides for steels having a larger portion of MX-carbides.
  • Fig. 3 shows a graph over the size of M 6 X-carbides for heat treatment no. 6, for the steels in Table 4.
  • steels with an addition of niobium have been marked by solid black dots, while steel without addition of niobium have been marked by rings. From the figure, it can be seen that the addition of Nb does not have any measurable effect on the size of the M 6 X-carbides.
  • a steel according to the invention will be less affected in respect of the size of the MX-carbides in the various hot-working operations that the steel undergoes during manufacturing, such as HIP:ing, forging, rolling, the higher the ratio of Nb/V of the steel, as is clear from Fig. 4.
  • Fig. 4 shows that the hot-working operations have little effect on the size of the MX-carbides in steels having a Nb/V ratio of about 0.6 or more.
  • Fig. 5 shows a chart over the lattice spacing in the plane d (hkl) for MX- and M 6 X-carbides as a function of the Nb/V ratio.
  • MX-carbides the (111)-spacing was measured
  • M 6 C-carbides the (331)-spacing was measured.
  • niobium seems to have no effect on the spacing between the lattices in the M 6 C-carbides, indicating that an addition of niobium has no effect on the composition of the M 6 C-carbides.
  • the steel according to the invention has a microstructure that in the hardened and tempered condition consists of a structure of tempered martensite containing MX-carbides and M 6 X-carbides that are evenly distributed in the martensite, obtainable by hardening of the product from an austenitizing temperature of between 950 and 1250 °C, cooling to room temperature and tempering at 480-650 °C.
  • the steel according to the invention should have a content of MX-carbides of not more than 15 % by volume, preferably not more than 13 % by volume, and even more preferred not more than 11 % by volume, where at least 80 %, preferably at least 90 %, and even more preferred at least 95 % of the MX-carbides have a carbide size in the longest extension of the carbide of not more than 3 ⁇ m, preferably not more than 2.2 ⁇ m, and even more preferred not more than 1.8 ⁇ m.
  • the composition of the steel should also be balanced in respect of the M 6 X-carbide-forming elements chromium, molybdenum and tungsten, such that the content in the steel of M 6 X-carbides will be not more than 15 % by volume, preferably not more than 13 % by volume and even more preferred not more than 12 % by volume, where at least 80 %, preferably 90 %, and even more preferred at least 95 % of the M 6 X-carbides have a carbide size in the longest extension of the carbide of not more than 4 ⁇ m, preferably not more than 3 ⁇ m, and even more preferred not more than 2.5 ⁇ m.
  • Fig. 6 is a photograph of the microstructure of a steel according to the invention, namely alloy F in Table 2.
  • the figure shows the evenly distributed'MX-carbides as black/dark grey, and the somewhat larger M 6 X-carbides are white/light grey.
  • the steel contains 5.5 % by volume of MX-carbides having an average size of 0.5 ⁇ m, where the 100 largest MX-carbides within an area of about 20,000 ⁇ m have an average size of 1.1 ⁇ m, and 11.8 % by volume of M 6 X-carbides having an average size of 1.2 ⁇ m, were the 100 largest M 6 X-carbides within an area of about 20,000 ⁇ m have an average size of 2.2 ⁇ m.
  • the light areas that surround the MX-carbides come from the etching and there is nothing corresponding to this in the material in reality.
  • the steel should have a good grindability.
  • the size of above all the MX-carbides affects the grindability of a steel such that the grindability gets impaired the larger the carbides in the steel.
  • the grindability of a steel can be given as its G ratio, and it is a measurement on how hard the material is to grind.
  • the G ratio of the steel was measured in the hardened and annealed condition by surface grinding a test piece of 7x7x150 mm by commercial discs of alumina, so called white discs, down to a size of 2x7x150 mm.
  • the G ratio is usually given as the volume of steel material that is ground off in relation to the volume of grinding disc that is consumed.
  • Fig. 7 shows the grindability as a function of the size of the MX-carbides. It is clear that a steel having MX-carbides of small size is considerably improved in grindability as compared to other steels having a content of MX-carbides in the same volume range.
  • Table 6 Chemical composition in % by weight for two variants of the steel according to the invention; balance iron and impurities at normal contents Steel C Si Mn Cr Mo W Co V Nb 1 1.70 0.59 0.29 3.98 4.69 6.17 9.03 3.19 2.08 2 1.65 0.54 0.29 3.95 4.60 6.03 8.94 3.15 2.13 Table 6: Hardness of the steel according to the invention for various heat treatments (HRC) Hardening temperatures (°C), dwell time 2-5 min.
  • an optimum hardness is chosen in the hardness range of 50-70 HRC.
  • the content of primarily C is being limited, as well as any existing N and at least some of W, V, Nb, Mo and Co, such that the contents are at about the lower limits for the steel, and the austenitizing temperature during hardening is chosen to be lower than 1100 °C.
  • the steel is slow in tempering, which means that it should be able to be exposed to high temperatures for a long time without losing the hardness that the steel has gained from hardening and tempering.
  • this hardness does not need to be extremely high, suitably in the magnitude of 50-55 HRC.
  • the primary properties are a higher hardness and strength in combination with a large toughness.
  • the hardness after tempering may typically lie in the range of 55-60 HRC.
  • the steel is heat treated suitably at an austenitizing temperature of 1000-1250 °C, typically 1150-1200 °C, and is tempered at a tempering temperature of 550-600 °C, 3x1 h.
  • the steel is heat treated suitably at an austenitizing temperature of 1000-1250 °C, typically 1150-1200 °C for tools for chip cutting removal and 1000-1200 °C for tools for cold working, and is tempered at a tempering temperature of 480-580 °C, typically 550-570 °C, 3x1 h, and has a hardness in the range of 50-55 HRC.
  • the tempering temperature can be lowered according to the above reasoning.
  • the steel has a nominal composition according to the following: 1.69 % (C +N), 0.65 % Si, 0.3 % Mn, 4.0 % Cr, 4.6 % Mo, 6.3 % W, 9.0 % Co, 3.2 % V and 2.1 % Nb, balance iron and impurities.
  • Such as steel is particularly well suited for tools for cutting for which a considerably improved grindability has been noted compared to the materials mentioned in the introduction, other properties being comparable.
  • the steel has also been shown to have improved machinability as compared primarily to ASP 2052.

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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)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
EP06769668.2A 2005-08-18 2006-08-18 Powder metallurgically manufactured steel, a tool comprising the steel and a method for manufacturing the tool Active EP1917376B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE0501827A SE529041C2 (sv) 2005-08-18 2005-08-18 Användning av ett pulvermetallurgiskt tillverkat stål
PCT/SE2006/050290 WO2007021243A1 (en) 2005-08-18 2006-08-18 Powder metallurgically manufactured steel, a tool comprising the steel and a method for manufacturing the tool

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EP1917376A1 EP1917376A1 (en) 2008-05-07
EP1917376A4 EP1917376A4 (en) 2017-05-17
EP1917376B1 true EP1917376B1 (en) 2019-06-19

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JP (1) JP5225843B2 (sv)
KR (1) KR101333740B1 (sv)
CN (1) CN101243199B (sv)
BR (1) BRPI0614983A2 (sv)
RU (1) RU2415961C2 (sv)
SE (1) SE529041C2 (sv)
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BRPI0603856A (pt) * 2006-08-28 2008-04-15 Villares Metals Sa ligas duras de composição enxuta
SE533988C2 (sv) * 2008-10-16 2011-03-22 Uddeholms Ab Stålmaterial och förfarande för framställning därav
JP5522854B2 (ja) * 2011-06-01 2014-06-18 株式会社日本製鋼所 冷間工具鋼およびその製造方法
RU2558305C2 (ru) * 2012-04-06 2015-07-27 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Самарский государственный технический университет" Способ изготовления сменных режущих пластин
EP2662166A1 (de) * 2012-05-08 2013-11-13 Böhler Edelstahl GmbH & Co KG Werkstoff mit hoher Beständigkeit gegen Verschleiss
CN102994912A (zh) * 2012-11-22 2013-03-27 宁波得利时泵业有限公司 一种均质混合泵的定子及其制备
CN103036371A (zh) * 2012-11-22 2013-04-10 宁波得利时泵业有限公司 一种均质混合泵的定子和转子材料
CN102994913A (zh) * 2012-11-22 2013-03-27 宁波得利时泵业有限公司 一种均质混合泵的定子材料
FR3000149B1 (fr) 2012-12-21 2015-01-16 Skf Aerospace France Procede de fabrication d'un roulement a billes, notamment pour une vanne papillon en environnement aeronautique
US20160076591A1 (en) * 2013-05-21 2016-03-17 Aktiebolaget Skf Bearing component
CN104250709B (zh) * 2013-06-28 2016-06-08 江苏天工工具有限公司 一种高品质tg42锯条高速钢
PT2857126T (pt) * 2013-10-02 2016-08-18 Uddeholms Ab Aço de ferramenta para trabalho a frio resistente à corrosão e ao desgaste
CN103600062B (zh) * 2013-10-10 2016-01-13 铜陵新创流体科技有限公司 一种粉末冶金合金复合材料及其制备方法
CN103667999A (zh) * 2013-11-11 2014-03-26 马鞍山市恒毅机械制造有限公司 一种矿用破碎锤用耐磨合金钢材料及其制备方法
EP2933345A1 (en) * 2014-04-14 2015-10-21 Uddeholms AB Cold work tool steel
CN104294140B (zh) * 2014-05-26 2016-08-24 宁国市鑫煌矿冶配件制造有限公司 一种球磨机用多元高耐磨高韧性高铬衬板
DE102014112374A1 (de) * 2014-08-28 2016-03-03 Deutsche Edelstahlwerke Gmbh Stahl mit hoher Verschleißbeständigkeit, Härte und Korrosionsbeständigkeit sowie niedriger Wärmeleitfähigkeit und Verwendung eines solchen Stahls
CN104894481B (zh) * 2015-05-15 2017-05-03 安泰科技股份有限公司 喷射成形耐磨损耐腐蚀合金
CN104878298B (zh) * 2015-05-15 2017-05-03 安泰科技股份有限公司 粉末冶金耐磨损耐腐蚀合金
CN104878303B (zh) * 2015-05-15 2017-05-03 安泰科技股份有限公司 耐磨损耐腐蚀合金
SE539646C2 (sv) * 2015-12-22 2017-10-24 Uddeholms Ab Hot work tool steel
RU2619537C1 (ru) * 2016-10-31 2017-05-16 Юлия Алексеевна Щепочкина Быстрорежущая сталь
EP3333275B1 (en) * 2016-12-07 2020-11-11 Höganäs AB (publ) Stainless steel powder for producing sintered duplex stainless steel
CN107937803B (zh) * 2017-11-01 2019-09-24 山东钢铁股份有限公司 一种具有低温冲击韧性耐磨钢板及其制备方法
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Also Published As

Publication number Publication date
EP1917376A1 (en) 2008-05-07
WO2007021243B1 (en) 2007-04-19
KR20080038130A (ko) 2008-05-02
WO2007021243A9 (en) 2007-06-14
EP1917376A4 (en) 2017-05-17
KR101333740B1 (ko) 2013-11-28
RU2008104934A (ru) 2009-09-27
SE0501827L (sv) 2007-02-19
CN101243199B (zh) 2011-03-30
JP2009504922A (ja) 2009-02-05
CN101243199A (zh) 2008-08-13
WO2007021243A1 (en) 2007-02-22
JP5225843B2 (ja) 2013-07-03
SE529041C2 (sv) 2007-04-17
RU2415961C2 (ru) 2011-04-10
BRPI0614983A2 (pt) 2011-04-26

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