WO2007021243A1 - 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 PDFInfo
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- WO2007021243A1 WO2007021243A1 PCT/SE2006/050290 SE2006050290W WO2007021243A1 WO 2007021243 A1 WO2007021243 A1 WO 2007021243A1 SE 2006050290 W SE2006050290 W SE 2006050290W WO 2007021243 A1 WO2007021243 A1 WO 2007021243A1
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- 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%
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- 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
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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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/30—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
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- 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, hi this case, the hardness after tempering may typically lie in the range of 55-60 HRC.
- 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.
- 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:
- Fig. 1 shows the relation between on the one hand the total contents of Nb and V
- Fig. 2 shows a graph over the size of MX-carbides as a function of the volume
- Fig. 3 shows a graph over the size of M 6 X-carbides as a function of the volume
- Fig. 4 shows a graph over the distribution in carbide size for various heat treatments and Nb/V ratios
- Fig. 5 shows a chart over the lattice spacing in the plane d ⁇ w ) for d ( m ) MX- and d( 33 i).
- Fig. 6 shows a photo of the microstructure of the steel F according to the invention, after heat treatment no. 6,
- Fig. 7 shows a graph over grindability, G ratio, as a function of the size of MX- carbides
- Fig. 8 shows a graph over energy consumption during grinding in relation to chip excavation rate.
- 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, hi order to avoid clogging during 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 above mentioned 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
- 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. For this reason 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 %. hi the fields of application intended for the steel the steel need not contain more than 6 % in order to achieve the desired property profile, hi a preferred embodiment 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, hi 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. More preferably, 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:
- 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.
- 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-C arbides 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. LABORATORY SCALE EXPERIMENTS
- Table 1 Chemical composition in % by weight for the examined steels; balance iron and im urities at normal contents
- 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:
- MX-carbides in the examined steels vary depending on which of the heat treatments in Table 2 that the steel has been exposed to. This is clear from Table 3 below.
- Table 3 The contents of MX-carbides in the steel, the size of these in dependence of heat treatment
- Fig. 1 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 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 (hk i ) for MX- and M 6 X- carbides as a function of the Nb/V ratio.
- MX-carbides the (11 l)-spacing was measured, and for M 6 C-carbides the (331)-spacing was measured.
- niobium seem 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 0 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 7x7x 150 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.
- values of the highest chip excavation rate could be compared for the steel according to the invention, called PUD 169 and having the following composition 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, and a reference steel having the following composition: 1.6 C, 4.8 Cr, 2.0 Mo, 10.5 W, 8.0 Co, 5.0 V, balance iron and unavoidable impurities, called ASP 2052.
- the result is shown in Fig. 8 and it is clear there from that the steel according to the invention can be milled at a chip excavation rate that is about 60 % higher than for the reference material at the same energy consumption, which is a considerable advantage from a
- 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 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 large toughness. In this case, 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 0 C, typically 1150-1200 0 C, and is tempered at a tempering temperature of 550-600 0 C, 3x1 h.
- an austenitizing temperature 1000-1250 0 C, typically 1150-1200 0 C
- a tempering temperature 550-600 0 C, 3x1 h.
- Even higher demands on hardness, 60-70 HRC, still in combination with a large toughness however, are put on steels for tools for the stamping of patterns or profiles in metals etc., as well as on steels for chip removal, such as gear cutting tools, taps and end-cutters with shaving separators.
- Taps should have a hardness in the range of 60-67 HRC
- end-cutters should have a hardness in the range of 62-70 HRC.
- the steel is heat treated suitably at an austenitizing temperature of 1000-1250 °C, typically 1150-1200 °C for tools for chip removal and 1000-1200 0 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.
Abstract
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Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2008526909A JP5225843B2 (en) | 2005-08-18 | 2006-08-18 | Steel produced by powder metallurgy, tool including the steel, and method for producing the tool |
BRPI0614983-9A BRPI0614983A2 (en) | 2005-08-18 | 2006-08-18 | metallurgically manufactured powder steel, a tool comprising steel, and a method for tool manufacturing |
CN2006800301426A CN101243199B (en) | 2005-08-18 | 2006-08-18 | Powder metallugically manufactured steel, a tool comprising the steel and a method for manufacturing the tool |
EP06769668.2A EP1917376B1 (en) | 2005-08-18 | 2006-08-18 | Powder metallurgically manufactured steel, a tool comprising the steel and a method for manufacturing the tool |
KR1020087001681A KR101333740B1 (en) | 2005-08-18 | 2006-08-18 | Powder metallugically manufactured steel, a tool comprising the steel and a method for manufacturing the tool |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE0501827-0 | 2005-08-18 | ||
SE0501827A SE529041C2 (en) | 2005-08-18 | 2005-08-18 | Use of a powder metallurgically made steel |
Publications (3)
Publication Number | Publication Date |
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WO2007021243A1 true WO2007021243A1 (en) | 2007-02-22 |
WO2007021243B1 WO2007021243B1 (en) | 2007-04-19 |
WO2007021243A9 WO2007021243A9 (en) | 2007-06-14 |
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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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EP (1) | EP1917376B1 (en) |
JP (1) | JP5225843B2 (en) |
KR (1) | KR101333740B1 (en) |
CN (1) | CN101243199B (en) |
BR (1) | BRPI0614983A2 (en) |
RU (1) | RU2415961C2 (en) |
SE (1) | SE529041C2 (en) |
WO (1) | WO2007021243A1 (en) |
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WO2014096047A1 (en) | 2012-12-21 | 2014-06-26 | Skf Aerospace France | A method for manufacturing a ball bearing, notably for a butterfly valve in an aeronautical environment |
WO2014187738A1 (en) * | 2013-05-21 | 2014-11-27 | Aktiebolaget Skf | Bearing component |
CN104250709A (en) * | 2013-06-28 | 2014-12-31 | 江苏天工工具有限公司 | High quality TG42 saw blade high speed steel |
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- 2006-08-18 JP JP2008526909A patent/JP5225843B2/en active Active
- 2006-08-18 CN CN2006800301426A patent/CN101243199B/en active Active
- 2006-08-18 RU RU2008104934/02A patent/RU2415961C2/en not_active IP Right Cessation
- 2006-08-18 WO PCT/SE2006/050290 patent/WO2007021243A1/en active Application Filing
- 2006-08-18 KR KR1020087001681A patent/KR101333740B1/en active IP Right Grant
- 2006-08-18 EP EP06769668.2A patent/EP1917376B1/en active Active
- 2006-08-18 BR BRPI0614983-9A patent/BRPI0614983A2/en not_active Application Discontinuation
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Cited By (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1922430A4 (en) * | 2005-09-08 | 2011-03-02 | Erasteel Kloster Ab | Powder metallurgically manufactured high speed steel |
US10844448B2 (en) | 2005-09-08 | 2020-11-24 | Erasteel Kloster Aktiebolag | Powder metallurgically manufactured high speed steel |
EP1922430A1 (en) * | 2005-09-08 | 2008-05-21 | Erasteel Kloster Aktiebolag | Powder metallurgically manufactured high speed steel |
WO2010044740A1 (en) * | 2008-10-16 | 2010-04-22 | Uddeholm Tooling Aktiebolag | Steel material and a method for its manufacture |
US9855603B2 (en) | 2012-05-08 | 2018-01-02 | Boehler Edelstahl Gmbh & Co. Kg | Material with high resistance to wear |
EP2662166A1 (en) * | 2012-05-08 | 2013-11-13 | Böhler Edelstahl GmbH & Co KG | Material with high wear resistance |
US20130343944A1 (en) * | 2012-05-08 | 2013-12-26 | Boehler Edelstahl Gmbh & Co. Kg | Material with high resistance to wear |
EP2935918B1 (en) | 2012-12-21 | 2019-05-01 | SKF Aerospace France | A method for manufacturing a ball bearing, notably for a butterfly valve in an aeronautical environment |
WO2014096047A1 (en) | 2012-12-21 | 2014-06-26 | Skf Aerospace France | A method for manufacturing a ball bearing, notably for a butterfly valve in an aeronautical environment |
WO2014187738A1 (en) * | 2013-05-21 | 2014-11-27 | Aktiebolaget Skf | Bearing component |
CN104250709A (en) * | 2013-06-28 | 2014-12-31 | 江苏天工工具有限公司 | High quality TG42 saw blade high speed steel |
NO20220593A1 (en) * | 2022-05-19 | 2023-11-20 | Hydro Extruded Solutions As | A method of producing a die for extrusion of aluminium profiles, and an extrusion die |
NO347610B1 (en) * | 2022-05-19 | 2024-01-29 | Hydro Extruded Solutions As | A method of producing a die for extrusion of aluminium profiles, and an extrusion die |
Also Published As
Publication number | Publication date |
---|---|
KR101333740B1 (en) | 2013-11-28 |
EP1917376A4 (en) | 2017-05-17 |
SE529041C2 (en) | 2007-04-17 |
EP1917376B1 (en) | 2019-06-19 |
WO2007021243A9 (en) | 2007-06-14 |
CN101243199B (en) | 2011-03-30 |
RU2415961C2 (en) | 2011-04-10 |
CN101243199A (en) | 2008-08-13 |
EP1917376A1 (en) | 2008-05-07 |
JP5225843B2 (en) | 2013-07-03 |
SE0501827L (en) | 2007-02-19 |
BRPI0614983A2 (en) | 2011-04-26 |
KR20080038130A (en) | 2008-05-02 |
JP2009504922A (en) | 2009-02-05 |
WO2007021243B1 (en) | 2007-04-19 |
RU2008104934A (en) | 2009-09-27 |
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