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  • 专利说明
  • 权利要求
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    • 专利摘要:
    ABSTRACT 19 A steel alloy intended for cutting applications and hot workingtools, comprising, in weight percent (wt. %), 5 C:Si: Mn: Cr: Mo: 10 W: Nb: V: Co: 15 S:N: 0.40-1.2 wt. %,0.30-2.0 wt. %,max 1.0 wt. %,3.0-6.0 wt. %, 0-4.0 wt. %, 0-8.0 wt. %, wherein (Mo+W/2) 2 3.5 wt. %, 0-4.0 wt. %, 0-4.0 wt. %, wherein 1.0 wt. % s (Nb+V)4.0 wt. %, 25-40 wt. %, max 0.30 wt. %, max 0.30 wt. %, the balance being Fe and unavoidable impurities.
    公开号:SE1650353A1
    申请号:SE1650353
    申请日:2016-03-16
    公开日:2017-09-17
    发明作者:Sandberg Fredrik；Rébois Delphine；Sundin Stefan
    申请人:Erasteel Sas；
    IPC主号:
    专利说明:

    A steel allov and a tool TECHNICAL FIELD OF THE INVENTION The present invention relates to a steel alloy suitable for cuttingapplications and to a tool comprising such a steel alloy. Thesteel alloy is preferably manufactured using powder metallurgy.
    The steel alloy is suitable for use in applications that require ahigh toughness in combination with hardness and strength, inparticular hot hardness and thermal stability. Such applicationsinclude cutting tools for chip removing machining, such as endmills, gear cutting tools or milling tools formed for hobbing ofworkpieces, thread-cutting taps, boring tools, drilling tools,turning tools, etc. The steel alloy is also suitable for hot-workingtools, such as extrusion dies, rollers for hot rolling, press rollersfor stamping of patterns in metal, etc. The tools may be providedwith a coating applied using physical vapour deposition (PVD) orchemical vapour deposition (CVD).
    BACKGROUND AND PRIOR ART A steel alloy suitable for cutting and hot-working applications isknown from WO9302818. The steel alloy is a high speed steelalloy manufactured using powder metallurgy. lt typicallycomprises, in weight percent (wt. %), 0.8 wt. % C, 4 wt. % Cr, 8wt. % Co, 3 wt. % Mo, 3 wt. % W, 1 wt. % Nb, 1 wt. % V, 0.5 wt.% Si, 0.3 wt. % Mn, balance Fe and unavoidable impurities. Thissteel alloy has a high toughness and an excellent grindability.However, the hot hardness, i.e. the hardness at elevatedtemperature, and the thermal stability, i.e. the ability of the alloyto maintain its properties and microstructure over time atelevated temperature, show potential for improvement for theabove mentioned applications. This should preferably be achieved while maintaining a good thermal conductivity at hightemperatures, since a good thermal conductivity is desirable forcutting tools in order to conduct heat away from the cutting edgevia the cutting tool. Moreover, it is desired that the steel alloyhas an adequate machinability prior to hardening.
    SUMMARY OF THE INVENTION lt is a primary objective of the present invention to provide asteel alloy which has improved thermal stability and hothardness in comparison with the above discussed prior art steelalloy, in combination with an improved or at least similar thermalconductivity. lt is a secondary objective to provide a tool whichhas excellent thermal stability and hot hardness in combinationwith a good thermal conductivity.
    According to a first aspect of the present invention, the primaryobjective is achieved by means of a steel alloy according toclaim 1. The steel alloy comprises: C: O.40-1.2 wt. %, Si: O.30-2.0 wt. %, Mn: max 1.0 wt. %, Cr: 3.0-6.0 wt. %, Mo: O-4.0 wt. %, W: O-8.0 wt. %, wherein (Mo+W/2) 2 3.5 wt. %,Nb: O-4.0 wt. %, V: O-4.0 wt. %, wherein 1.0 wt. % S (Nb+V) S 4.0 wt. %,Co: 25-40 wt. %, S: max 0.30 wt. %, N: max 0.30 wt. %, the balance being Fe and unavoidable impurities.
    With the steel alloy according to the present invention, animproved hot hardness and thermal stability can be achieved incomparison with a similar steel alloy with a lower amount of cobalt, such as the one described above. Although the steelalloy according to the invention comprises a limited amount ofexpensive alloying elements such as molybdenum and tungsten,it is still possible to achieve the desired properties of the steelalloy at hot-working conditions after hardening and tempering.The steel alloy is therefore suitable for cutting machining andhot-working applications, wherein e.g. a good thermal stability iscrucial. The steel alloy according to the invention has alsoproved to have adequate machinability in soft annealedcondition, i.e. the condition in which the steel alloy is subjectedto machining for forming a tool. The steel alloy also has arelatively high thermal conductivity, thus being suitable forcutting applications in which it is desired to conduct generatedheat away from the cutting edge.
    According to one embodiment, the steel alloy comprises 27-33wt. % Co. This helps achieving a good hot hardness and thermalstability without having problems with hardening the steel alloy.
    According to another embodiment, the steel alloy comprises 28-30 wt. % Co. Within this interval, the hot hardness and thermalstability are optimised.
    According to another embodiment, the steel alloy comprises0.60-0.90 wt. % C. Within this range, a fine grain structure anda good wear resistance can be achieved without causingbrittleness.
    According to another embodiment, the steel alloy comprisesO.30-1.1 wt. % Si. This reduces the risk of forming large MeCcarbides and impaired hardness, while still maintaining thefluidity of the steel alloy during the melt metallurgical process.
    According to another embodiment, the steel alloy comprises3.5-5.0 wt. % Cr. ln this range, Cr will contribute to a sufficient hardness and toughness after hardening and tempering, withoutrisking retained austenite in the steel matrix.
    According to another embodiment, the steel alloy comprises0.10-0.50 wt. % Mn. At these levels, Mn can put sulfuricimpurities out of action by the formation of manganese sulfides,improving the machinability of the steel alloy.
    According to another embodiment, the steel alloy comprises2.0-4.0 wt. % Mo and 2.0-4.0 wt. % W. ln these amounts, Moand W contribute to an adequate hardness and toughness of thesteel matrix after hardening and tempering.
    According to another embodiment, the steel alloy comprises0.90-1.3 wt. % Nb and 0.90-1.3 wt. % V. The grindability of thesteel alloy can thereby be optimised.
    According to another embodiment, the steel alloy comprises max0.080 wt. % S. ln this embodiment, the steel alloy is notintentionally alloyed with sulfur, but S may be present as animpurity without effect on the mechanical properties of the steelalloy.
    According to another embodiment, the steel alloy comprises lessthan 1.0 wt. % unavoidable impurities, preferably less than 0.75wt. % unavoidable impurities, and more preferably less than0.50 wt. % unavoidable impurities. Below these levels, theimpurities have very little effect on the properties of the steelalloy.
    According to another embodiment, the steel alloy is a powdermetallurgy steel alloy. Preferably, the steel alloy is in the form ofa powder metallurgy steel alloy produced by gas atomisation.Using gas atomisation, it is possible to obtain a powdermetallurgy steel alloy with high purity, low level of inclusionsand very fine dispersed carbides. Gas atomised powder is spherical and may be densified into a homogeneous materialusing for example hot isostatic pressing (HIP).
    According to another aspect of the present invention, the abovementioned secondary objective is achieved by means of a toolcomprising the proposed steel alloy. Such a tool has a goodthermal stability, hot hardness and thermal conductivity and istherefore suitable for hot-working and cutting applications.
    According to one embodiment of this aspect of the invention, thetool is a cutting tool configured for chip removing machining.
    According to one embodiment of this aspect of the invention, thetool is provided with a coating applied using physical vapourdeposition or chemical vapour deposition. The PVD or CVDcoating forms a wear resistant outer layer.
    Further advantages and advantageous features of the inventionwill appear from the following description of the invention andembodiments thereof.
    BRIEF DESCRIPTION OF THE DRAWINGS The present invention will now be described in detail with reference to the attached drawings, wherein: Fig.1 shows hardness as a function of ageing time forexemplary alloys, Fig. 2 shows decrease in hardness as a function of ageingtime for exemplary alloys, and Fig. 3 shows thermal conductivity as a function oftemperature for exemplary alloys, Fig. 4 shows hot hardness as a function of temperature for exemplary alloys, and Fig. 5 shows hardness as a function of hardeningtemperature for a number of a|oys with different Co content.
    DETAILED DESCRIPTION OF EMBODIMENTS OF THEINVENTION The importance of the various alloying elements will now beexplained in greater detail.
    Carbon (C) has several functions in the steel alloy. Above all, acertain amount of carbon is needed in the matrix in order toprovide a suitable hardness through the formation of martensiteby cooling from the dissolution temperature. The amount ofcarbon should be sufficient for the combination of carbon withon one hand molybdenum/tungsten, and on the other handvanadium/niobium, such that precipitation hardening can beachieved by the formation of carbides. The carbides provideresistance to wear and also limit grain growth, therebycontributing to a fine grained structure of the steel alloy.Therefore, the carbon content in the steel shall be at least 0.40wt. % and preferably at least 0.60 wt. %, suitably at least 0.70wt. %. However, the carbon content must not be so high that itwill cause brittleness. The carbon content should therefore notexceed 1.2 wt. %, and preferably not exceed 0.90 wt. %.
    Silicon (Si) may exist in the steel as a residue from thedeoxidation of the steel melt. Silicon improves the fluidity of theliquid steel, which is important in the melt metallurgical process.By increased addition of silicon the steel melt will be more fluid,which is important in order to avoid clogging in connection withgranulation. The silicon content should for this purpose be atleast 0.30 wt. % and even more preferred at least 0.40 wt. %.Silicon also contributes to increased carbon activity and in asilicon alloyed embodiment it can be present in amounts of up to 2.0 wt. %. Problems with brittleness will arise at contents above2.0 wt. % and may affect the mechanical properties already atlower contents. Accordingly, the steel a|oy should suitably notcontain more than 1.2 wt. % Si as the risk of formation of largeIVISC carbides and impaired hardness in the hardened conditionwill be larger at silicon contents above this level. lt is even morepreferred to limit the silicon content to not more than 1.1 wt. %.
    Manganese (Mn) can also be present in the steel a|oy, primarilyas a residual product from the metallurgical melt process. ln thisprocess, manganese has the known effect of putting sulfuricimpurities out of action by the formation of manganese sulfides.For this purpose, it should preferably be present in the steel at acontent of at least 0.10 wt. %. The maximum content ofmanganese in the steel is 1.0 wt. %, but preferably the contentof manganese is limited to a maximum of 0.50 wt. %. ln apreferred embodiment, the steel contains 0.20 to 0.40 wt. % Mn.
    Chromium (Cr) shall be present in the steel a|oy in an amountof at least 3.0 wt. %, preferably at least 3.5 %, in order tocontribute to a sufficient hardness and toughness of the steelmatrix after hardening and tempering. Chromium can alsocontribute to the wear resistance of the steel a|oy by beingincluded in primarily precipitated carbides, mainly IVISC carbides.Too much chromium, however, will cause a risk for retainedaustenite, which may be difficult to transform. The chromiumcontent is therefore limited to max 6.0 wt. %, preferably to max5.0 wt. %.
    Molybdenum (Mo) and tungsten (W) contribute to an adequatehardness and toughness of the steel matrix after hardening andtempering. l/lolybdenum and tungsten can also be included inprimarily precipitated IVISC carbides and will as such contributeto the wear resistance of the steel. Also other primarilyprecipitated carbides contain molybdenum and tungsten,although not to the same extent. The limits for the contents of molybdenum and tungsten are chosen in order to, by adaptationto other alloying elements, result in suitable properties. lnprinciple, molybdenum and tungsten can partially or completelyreplace each other, which means that tungsten can be replacedby half the amount of molybdenum, or molybdenum can bereplaced by double the amount of tungsten. By experience, it ishowever known that about equal amounts of molybdenum andtungsten are preferred, since this result in certain advantages inproduction technology, or more specifically in heat treatmenttechnology. When using raw material in the form of scrap steel,about equal amounts of molybdenum and tungsten are preferredsince this puts less restraints on the type of scrap steel used.Properties suitable for the purpose will be achieved incombination with other alloying elements at a molybdenum andtungsten content such that (Mo + W/2) equals at least 3.5 wt. %,but not more than 8.0 wt. %. The content of molybdenum shouldbe within the range 0 to 4.0 wt. % and the content of tungstenshould be within the range 0 to 8.0 wt. %. Preferably, the steelalloy comprises within the range of 2.0 to 4.0 wt. % of each ofmolybdenum and tungsten, respectively.
    Vanadium (V) and niobium (Nb) are to some degreeinterchangeable and in small amounts contribute to keepingdown the size of carbides. By properly balancing the amounts ofniobium and vanadium, the size of primarily precipitated MCcarbides can be limited, thereby improving the grindability of thesteel alloy. The total content of niobium and vanadium shouldfulfil the condition 1.0 wt. % S (Nb+V) S 4.0 wt. %, preferably 1.5wt. % S (Nb+V) S 3.0 wt. %. ln a preferred embodiment, thesteel should contain 0.90 to 1.3 wt. % Nb and 0.90 to 1.3 wt. %V. The content of each of the elements Nb and V should bewithin the range 0-4.0 wt. %, i.e., it is possible to omit one ofthe elements and replace it with the other.
    Cobalt (Co) contributes to the hot hardness and the thermalstability of the steel alloy necessary for cutting applications.
    Cobalt is known to reduce the toughness of steel alloys andlarge amounts of cobalt in steel alloys have therefore previouslybeen avoided. However, according to the present invention, ithas been found that the amount of cobalt can be increased withrespect to the amount present in previously known steel alloyssuch as the one disclosed in WO9302818. Cobalt is in thepresent steel alloy present in an amount of at least 25 wt. %,preferably at least 27 wt. % and most preferably at least 28wt. %. This provides the requested hot hardness and thermalstability. The amount of cobalt should be limited to max 40wt. %, since above this level, the steel alloy becomes verydifficult to harden to the desired hardness due to retainedaustenite. Preferably, the amount of cobalt is for this reasonlimited to max 33 wt. %, or more preferably max 31 wt. %, andeven more preferably max 30 wt. %.
    Sulfur (S) may be present in the steel alloy as a residual productfrom the manufacturing process. ln amounts of less thanapproximately 800 ppm, i.e. 0.080 wt. %, the mechanicalproperties of the steel alloy are largely unaffected. Sulfur canalso be deliberately added as an alloying element in order toimprove the machinability of the steel alloy. However, sulfurreduces the weldability and may also cause brittleness. lfalloyed with sulfur, the amount of sulfur should be limited to max0.30 wt. %, preferably max 0.2 wt. %. ln sulfur alloyedembodiments, the manganese content of the steel shouldpreferably be somewhat higher than in non-sulfuredembodiments of the steel alloy. ln non-sulfured embodiments,care should be taken not to exceed 0.080 wt. % S.
    Nitrogen (N) can to some extent replace carbon in the steel alloyand could be present in an amount of max 0.3 wt. %, but shouldpreferably be limited to max 0.1 wt. %. The amounts of carbonand nitrogen should be balanced to achieve a desired amount ofcarbides, nitrides and carbonitrides, contributing to the wearresistance of the steel alloy.
    Besides the above mentioned elements, the steel alloy maycontain unavoidable impurities and other residual products innormal amounts, derived from the melt-metallurgical treatmentof the steel alloy. Other elements can intentionally be suppliedto the steel alloy in minor amounts, provided they do notdetrimentally change the intended interactions between thealloying elements of the steel alloy and also that they do notimpair the intended features of the steel alloy and its suitabilityfor the intended applications. lmpurities, such as contaminationelements, can be present in the steel alloy at an amount ofmaximum 1.0 wt. %, preferably maximum 0.75 wt. % and morepreferably maximum 0.5 wt. %. Examples of impurities that maybe present are titanium (Ti), phosphorus (P), copper (Cu), tin(Sn), lead (Pb), nickel (Ni), and oxygen (O). The amount ofoxygen should preferably not exceed 200 ppm, and should morepreferably not exceed 100 ppm. The impurities may be naturally-occurring in the raw material used to produce the steel alloy, ormay result from the production process.
    The steel alloy according to the invention may be produced by apowder metallurgic process, in which a metal powder of highpurity is produced using atomisation, preferably gas atomisationsince this results in powder with low amounts of oxygen. Thepowder is thereafter densified using for example hot isostaticpressing (HIP). Typically, a capsule of low alloyed steel is filledwith gas atomised powder. The capsule is sealed andconsolidated to a billet with full density under high pressure andtemperature. The billet is forged and rolled into a steel bar andcomponents/tools of final shape are thereafter produced byforging and machining. Components can also be produced fromsteel alloy powder using a near net shape technique, in whichsteel alloy powder is canned in metal capsules and isconsolidated into components with the desired shape under highpressure and temperature. Components can further be producedusing additive manufacturing techniques. 11 The steel alloy according to the invention is particularly suitablefor forming cutting tools for chip removing machining withintegrated cutting elements. Preferably, the finished tool isprovided with a PVD or a CVD coating having a face centredcubic structure and a thickness of 20 pm or less, typically 5-10pm. Common coatings used in the field are differentcombinations of oxides and nitrides such as TiN, TiAlN, AlCrN,AlCrON, etc.
    EXAMPLES A number of steel alloy test samples, with alloying elementcompositions as listed in Table I, were produced and tested. Thebalance of the listed compositions was Fe and unavoidableimpurities in total amounts of less than 0.5 wt. %. Unavoidableimpurities in this case include e.g. oxygen. Alloy A is a steelalloy according to the present invention while HSS1, HSS2 andHSS3 are comparative alloys falling outside the scope of thepresent invention. HSS1 is a high speed steel alloy as disclosedin WO9302818, while as HSS2 and HSS3 are more high alloyedsteel alloys, containing larger amounts of V, Mo and W as wellas a larger amount of C. HSS2 and HSS3 are examples of themost high performance powder metallurgy high speed steelalloys for cutting applications.
    Alloy C Cr Co Mo W Nb V Si Mn S NA 0.77 4.1 30 2.7 3.1 1.1 1.1 1.1 0.30 <0.06 0-006HSS1 0.80 4.0 8.0 3.0 3.0 1.1 1.1 0.50 0.32 <0.025 -HSS2 2.30 4.2 10.5 7.0 6.5 - 6.5 0.50 0.30 <0.025 -HSS3 2.45 4.0 16.0 5.0 11.0 - 6.3 0.50 0.30 <0.025 - The listed steel alloys were produced by powder metallurgy.First, steel alloy powders were produced using gas atomisation, 12 and thereafter the powders were enclosed in capsules anddensified into solid samples by means of hot isostatic pressing(HIP). The densified samples were soft annealed in a furnace at910°C for a holding time of 3 hours at temperature, followed byslow cooling at a cooling rate of -10°C/h down to 670°C. Thesamples were thereafter slowly cooled to room temperature.
    The Brinell hardness after soft annealing, i.e. the soft annealedhardness, was determined for alloy A using two indents persample. The soft annealed hardness of alloy A was 450 HB, i.e.approximately 47 HRC. By adding a fast quenching in a vacuumfurnace during cooling of the sample after soft annealing, it waspossible to reduce the soft annealed hardness to 390 HB.
    The machinability of the soft annealed samples was tested foralloy A and for HSS2. The soft annealed hardness for the testedsamples was 425 HB for alloy A and 355 HB for HSS2. The softmachining was carried out by milling with a coated cementedcarbide milling insert. 2 mm deep cuts were formed with onemilling insert mounted in a milling head of the tool. The feed waskept constant at 0.15 mm per turn and the cutting speed wasvaried between 80 to 120 rpm. The number of cuts until themilling insert broke down was recorded and are shown in Tablell.
    Cutting speed (rpm) Alloy A (no. of cuts) HSS2 (no. of cuts)80 7 12 100 10 7 120 5.2 5.5 As can be seen from Table ll, the machinability in soft annealedcondition is comparable for alloy A according to the inventionand for HSS2, even though the soft annealed hardness of alloyA is higher, as discussed above. From the higher soft annealedhardness, a reduced machinability would normally be expected. 13 For an increase in soft annealed hardness of 70 HB, it wouldnormally be expected that the possible cutting speed would bereduced by 50 %. However, for alloy A according to theinvention, the possible cutting speed is comparable with that ofHSS2.
    Soft annealed samples from alloy A, HSS1 and HSS3 were alsosubjected to hardening and tempering at different temperatures.The samples were tempered for 3 x 1 hour.
    The Vickers hardness with a 10 kg load (HV10) of the heattreated samples was measured on one sample from eachcombination of alloy and heat treatment. Five indents weremade per sample. The Vickers hardness with a 30 kg load(HV30) was further measured for some of the heat treatedsamples with ten indents per sample. lndents that wereobviously affected by porosity were disregarded whenmeasuring the Vickers hardness with a 30 kg load. Results ofthe Vickers hardness test are shown in Table lll. The hardnessvalues HV10 and HV30 shown are average hardness values. - 725.5 -A 1150 560 919.6 918.7580 893.8 884.9- 854.2 -HSS1 1180 560 864.4 873.5580 818.4 -- 847.4 -HSS3 1180 560 105015 10484580 1004.0 - For alloy A, the hardening at 1150°C results in a microstructurewith carbides of MC type and IVISC type, having an mean size ofapproximately 0.5 pm, wherein the MC carbides constitutearound 2 volume percent (vol. %) of the total structure, andwherein the IVISC carbides constitute about 2-3 vol. % of the 14 total structure, as measured using image analysis of scanningelectron microscopy (SEM) images. Corresponding values forHSS1 are 0.25 um and 1.9 vol. % (MC) and 1.7 vol. % (IVIeC),respectively. For HSS3, corresponding values are 1.1 um and 17vol. % (MC) and 5.4 vol. % (IVIGC), respectively.
    Samples from each of the alloys listed in Table I were subjectedto an elevated temperature of 600°C for different durations oftime in a tempering furnace. Prior to being held at thistemperature, the samples were subjected to heat treatmentsincluding tempering as described above, with a hardeningtemperature of 1180°C and tempering temperatures of 560°C (allsamples) and 580°C (only alloy A samples). The samples wereheld at a temperature of 600°C for 1 h, 3 h, 5 h and 22 h,respectively. ln addition, one sample per combination of alloyand heat treatment was not subjected to the elevatedtemperature in order to get a reference point. After being held at600°C, all samples were cast in plastic moulds and ground. TenVickers hardness indents were made per sample at roomtemperature with a 30 kg load. lndents that were obviouslyaffected by porosity in the materials were disregarded.
    Results of the trials are shown in fig. 1, where hardness valuesHV3O as a function of time held at 600°C are plotted for thedifferent samples. The tempering temperatures of the differentsamples are shown in the legend. As can be seen, alloy A has aclearly higher hardness than HSS1.
    Fig. 2 shows the decrease in hardness HV3O as a function oftime held at 600°C for the different samples, wherein thedecrease is relative to the hardness of the correspondingsamples not being held at 600°C. The tempering temperaturesof the different samples are shown in the legend. As can beseen from the results, for both tempering temperatures, thedecrease in hardness is significantly smaller for alloy Aaccording to the invention than for the comparative alloys HSS1, HSS2 and HSS3. The alloy according to the invention thusshows an improved thermal stability with respect to all of thecomparative alloys.
    The hot hardness of samples that were subjected to hardeningwas also measured. For each combination of alloy, heattreatment and test temperature, two Vickers hardness indentswere made with a 5 kg load. Results of the hot hardness test areshown in Table IV, showing Vickers hardness (HV5) at differenttemperatures. All samples were hardened at 1180°C, buttempering was performed at 580°C for alloy A and at 560°C forHSS1 and HSS2. As can be seen, alloy A exhibits increased hothardness with respect to HSS1 at all temperatures, and a slightimprovement in hot hardness at temperatures of 650°C andabove with respect to HSS2. The hot hardness is also shown infig. 4, in which hardness is plotted as a function of temperaturefor all three alloys.
    Alloy 400°C 500°C 550°C 600°C 650°C 700°C 750°CA 785 703 636 541 409 161 89HSS1 714 626 589 521 303 143 68HSS2 798 741 671 570 337 155 75 The thermal conductivities of samples from alloy A and HSS2were determined using a laser flash technique. Results from themeasurements are shown in fig. 3, showing that the thermalconductivity of alloy A according to the invention is improvedwith respect to the alloy HSS2.
    Experiments with alloys comprising 1.3 wt. % C, 4.2 wt. % Cr,5.0 wt. % Mo, 6.4 wt. % W, 3.1 wt. % V, and with a Co content of30 wt. %, 40 wt. % and 50 wt. %, respectively, balance Fe, haveshown that a Co content of 40 wt. % and above renders thesteel alloy difficult or impossible to harden to the demandedhardness. Results from such experiments are shown in fig. 5,showing hardness in HRC as a function of hardening 16 temperature in degrees Celsius for the three different alloys. ltis expected that a corresponding reduction in hardenabilitywould result for a composition according to the invention, butwith a higher Co content.
    The invention is of course not limited to the embodimentsdisclosed, but may be varied and modified within the scope ofthe following claims.
    权利要求:
    Claims (15)
    [1] 1. A steel alloy comprising, in weight percent (wt. %), C: O.40-1.2 wt. %, Si: O.30-2.0 wt. %, Mn: max 1.0 wt. %, Cr: 3.0-6.0 wt. %, Mo: O-4.0 wt. %, W: O-8.0 wt. %, wherein (Mo+W/2) 2 3.5 wt. %,Nb: O-4.0 wt. %, V: O-4.0 wt. %, wherein 1.0 wt. % s (Nb+V) S 4.0 wt. %, Co: 25-40 wt. %, S: max 0.30 wt. %, N: max 0.30 wt. %, the balance being Fe and unavoidable impurities.
    [2] 2. The steel alloy according to claim 1, comprising 27-33 wt. % Co.
    [3] 3. The steel alloy according to claim 1, comprising 28-30 wt. % Co.
    [4] 4. The steel alloy according to any one of the precedingclaims, comprising 0.60-0.90 wt. % C.
    [5] 5. The steel alloy according to any one of the precedingclaims, comprising O.30-1.1 wt. % Si.
    [6] 6. The steel alloy according to any one of the precedingclaims, comprising 3.5-5.0 wt. % Cr.
    [7] 7. The steel alloy according to any one of the precedingclaims, comprising 0.10-0.50 wt. % Mn. 18
    [8] 8. The steel alloy according to any one of the precedingclaims, comprising 2.0-4.0 wt. % Mo and 2.0-4.0 wt. % W.
    [9] 9. The steel alloy according to any one of the precedingclaims, comprising 0.90-1.3 wt. % Nb and 0.90-1.3 wt. % V.
    [10] 10. The steel alloy according to any one of the precedingclaims, comprising max 0.080 wt. % S.
    [11] 11. The steel alloy according to any one of the precedingclaims, comprising less than 1.0 wt. % unavoidable impurities,preferably less than 0.75 wt. % unavoidable impurities, andmore preferably less than 0.50 wt. % unavoidable impurities.
    [12] 12. The steel alloy according to any one of the precedingclaims, wherein the steel alloy is a powder metallurgy steelalloy.
    [13] 13. A tool comprising a steel alloy according to any one of thepreceding claims.
    [14] 14. A tool according to claim 8, wherein the tool is a cuttingtool configured for chip removing machining.
    [15] 15. A tool according to claim 13 or 14, wherein the tool isprovided with a coating applied using physical vapour depositionor chemical vapour deposition.
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    US20190078184A1|2019-03-14|
    SE539733C2|2017-11-14|
    JP2019512595A|2019-05-16|
    KR20180125527A|2018-11-23|
    KR102356521B1|2022-01-27|
    CN108779531A|2018-11-09|
    EP3430179A1|2019-01-23|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    GB431248A|1933-11-30|1935-07-03|Krupp Ag|Improvements in iron alloys|
    SE401689B|1974-12-18|1978-05-22|Uddeholms Ab|TOOLS FOR CUTTING PROCESSING AND WAYS TO PRODUCE THIS|
    US4224060A|1977-12-29|1980-09-23|Acos Villares S.A.|Hard alloys|
    EP0599910B1|1991-08-07|1997-03-05|Erasteel Kloster Aktiebolag|High-speel manufactured by powder metallurgy|
    SE500008C2|1991-08-07|1994-03-21|Erasteel Kloster Ab|High speed steel with good hot hardness and durability made of powder|
    JP2697436B2|1991-11-22|1998-01-14|三菱マテリアル株式会社|Two-layer forged valve seat made of iron-based sintered alloy for internal combustion engine|
    AT411441B|2000-06-02|2004-01-26|Boehler Ybbstal Band Gmbh & Co|COMPOSITE TOOL|
    SE519278C2|2001-06-21|2003-02-11|Uddeholm Tooling Ab|Cold Work|
    JP3928782B2|2002-03-15|2007-06-13|帝国ピストンリング株式会社|Method for producing sintered alloy for valve seat|
    JP2006316309A|2005-05-12|2006-11-24|Nachi Fujikoshi Corp|High wear resistant tough steel having excellent fatigue strength|
    AT505221B1|2007-05-08|2009-09-15|Bihler Edelstahl Gmbh|TOOL WITH COATING|
    US8012270B2|2007-07-27|2011-09-06|Vacuumschmelze Gmbh & Co. Kg|Soft magnetic iron/cobalt/chromium-based alloy and process for manufacturing it|
    JP2010144235A|2008-12-22|2010-07-01|Hitachi Powdered Metals Co Ltd|Wear-resistant sintered alloy and method for producing the same|
    JP2010274315A|2009-05-29|2010-12-09|Nippon Piston Ring Co Ltd|Valve seat for cast-in insert of light metal alloy|
    EP2662166A1|2012-05-08|2013-11-13|Böhler Edelstahl GmbH & Co KG|Material with high wear resistance|
    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    SE1650353A|SE539733C2|2016-03-16|2016-03-16|A steel alloy and a tool|SE1650353A| SE539733C2|2016-03-16|2016-03-16|A steel alloy and a tool|
    JP2018545365A| JP7026629B2|2016-03-16|2017-03-15|Alloy steel and tools|
    KR1020187029775A| KR102356521B1|2016-03-16|2017-03-15|Uniform steel alloys and tools|
    US16/085,212| US20190078184A1|2016-03-16|2017-03-15|A steel alloy and a tool|
    CN201780016983.XA| CN108779531A|2016-03-16|2017-03-15|steel alloy and tool|
    EP17711628.2A| EP3430179B1|2016-03-16|2017-03-15|A steel alloy and a tool|
    PCT/EP2017/056170| WO2017158056A1|2016-03-16|2017-03-15|A steel alloy and a tool|
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