COATED CEMENTED CARBIDE CUTTING TOOL AND METHOD OF COATING IT WITH DIAMOND

Abstract: According to the present invention there is now provided a body of cemented carbide provided with at least one wear resistant layer, which body contains a zone in the cemented carbide and adjacent to the applied layer, containing triangular WC platelets with a specific orientation. Different binder phase gradients are possible. The body is in particular suited for application of CVD diamond layers.

Description: COATED CEMENTED CARBIDE CUTTING TOOL AND METHOD OF COATING IT WITH DIAMOND The present invention relates to coated cemented carbide cutting tools with improved properties obtained by a heat treatment of the cemented carbide before the application of a wear resistant coating. The invention is in particular related to a body coated with diamond. However, the method can also be used for other wear resistant coatings, such as any CVD- or PVD wear resistant coatings. The adhesion of wear resistant coatings on cemented carbide is due to several mechanisms of which mechanical adhesion constitutes one part, i.e. a rough surface grips mechanically into the applied coating. Several approaches have been made in order to achieve good mechanical adhesion see EP-A-500 283. For the case of diamond layers, the achievement of adhesion is particularly difficult since the presence of binder metal deteriorates the adhesion. A common method for achieving good diamond layer adhesion on cemented carbide is to etch away the binder metal from a surface region, see EP-A-0 500 253. This, however, increases the risk of bad adhesion due to loosely bound carbide grains. Other methods involve carburising sintering of an eta phase containing body (US 4,843,039) so as to deplete a surface region of binder phase. The treatment gives a relatively brittle surface zone together with a likewise brittle core which is less adequate for certain toughness demanding cutting applications. Another method for preparing a cemented carbide for diamond coating is described in WO 95/15258 according to which a rough surface is obtained through a heat treatment in N2 containing atmosphere . The surfaces treated in this way are free of binder phase. However, during a heat treatment as described in WO 95/15258 grain growth occurs not only at the surface but also within the body generally resulting in formation of large WC-grains in the structure. US 4,830,886 describes a method to avoid the presence of the eta phase layer formed during a CVD deposition of a TiCN layer by carburizing the eta phase layer through the TiCN-layer after the CVD process. EP-A-759 480 describes a cemented carbide body containing triangular WC-platelets . The platelets are oriented with their triangular surfaces parallel to the surface of the body. The toughness of the body is said to be improved. US 5,100,703 describes a diamond-coated sintered body, comprising a film of diamond and/or diamond-like carbon deposited on the surface of a sintered body of a hard phase composed mainly of a mixture of W2C and WC and inevitable impurities. It has now surprisingly been found that within a surface zone of a cemented carbide body, a controlled change in WC grain orientation, size and shape can be obtained by an initial decarburization or decarburization + heat treatment in neutral gas atmosphere or vacuum through which an eta phase containing surface zone is obtained and then a complete recarburization of said zone in order to completely transform the eta phase therein to WC+Co . (Eta phase is a common name for low carbon content containing carbides usually comprising W-Co-C in proportions MgC or M12C, = W and Co and/or Fe and/or Ni such as Mχ2 c = CogWgC and MgC = C03W3C, W4C02C) . The shape of the WC grains is triangular platelets. The platelet containing region can be combined with different binder phase gradient zones. The adhesion of a subsequently deposited wear resistant coating to this body is found to be excellent. Fig la shows a triangular WC platelet for which L is length, T is thickness and A is rectangular area defined by the side L and thickness T. Fig lb shows the orientation of a platelet with respect to the surface of the body where α is the angle between the normal of the side A and the surface plane as measured in the plane of the triangular side of the platelet and β is the angle between the normal of surface A and the surface plane as measured in a plane perpendicular to the triangular surface of the platelet. Fig 2a shows a drawing of a body according to the invention after decarburization resulting in a surface zone Al containing essentially eta phase, or W + Cθ7Wg, or W 4- eta phase and adjacent to this zone an optional zone A2 containing lower amount of eta phase (and possibly WC and/or Co. Zone A3 contains no eta phase but decreased binder phase content compared to zones Al , A2 and the zone B4 represents the unaffected part of the body. Fig 2b shows the body after carburization where the zone Bl contains WC platelets. Inner zones B2 and B3 comprise different binder phase gradients. Zone B4 represents the unaffected part of the body Fig 3a shows in 3000X a scanning electron micrograph of an uncoated WC-Co cemented carbide surface according to the invention. Fig 3b shows in 3000X a scanning electron micrograph of a cross-section of the same body as in Fig 3a coated with a diamond layer. Fig 4a shows in 3000X a scanning electron micrograph of an uncoated WC-Co cemented carbide surface according to the invention but with a different binder phase distribution compared to Fig 3a. Fig 4b shows in 1750X a scanning electron micrograph of the cross-section the body in Fig 4a. Fig 5a shows in 3000X a scanning electron micrograph of an uncoated cemented carbide surface of a WC-Co-gamma phase grade according to the invention. Fig 5b shows a in 150OX a scanning electron micrograph of a cross-section of the body in Fig 5a. Figs 6a-d show examples of various binder phase distributions together with position of zones B1-B4 obtained after carburizing treatment. In one method according to the present invention, a cemented carbide bodies is first decarburized to form a surface zone of eta phase, for example CogWgC, C03W3C, A1+A2. This eta phase containing surface zone shall be 3-100 μm thick and consist of at least partially interconnected eta phase. The amount of eta phase shall be >60% by volume within the zone. In a preferred embodiment the surface zone Al contains no WC phase . The decarburization is made by heating the bodies to a temperature between 900 and 1350°C, preferably between 950 and 1250°C, in a decarburizing atmosphere such as H2+H2O. The time for the treatment is preferably 1-10 h. Decarburization at lower temperatures-between 950 and 1000°C gives more even thickness of the decarburized zones comprising eta phase along the entire surface of the treated bodies. Decarburization performed at higher temperatures - between 1200 and 1250°C gives thicker decarburized zones comprising eta phase at the edges and corners than at the plane faces of the bodies. Prior to the carburizing heat treatment other phases than eta phase, if present, such as W, Cθ7Wg in the surface zone, shall be transformed to eta phase. This may be done in a separate heat treating step at elevated temperature 1050-1350°C and in a neutral gasatmosphere or vacuum, during which W and Cθ g phases react with carbon present in the cemented carbide and form eta phase, preferably MgC phase. In an alternative method, oxidation of the bodies can be made whereby the preferred treatment comprises the following steps: Step 1: Heat treatment at 500-900°C in air, C0 2 or O2 , preferably air whereby oxides such as WO3 or C0WO4 are formed Step 2 (optional) : Heat treatment at 500-900°C in reducing atmosphere, for example comprising H2 , whereby the oxides are transformed into metals, for example W and Co 7 Wg . Step 3: Heat treatment at 1000-1400°C in vacuum or in Ar such that eta phase is formed. Such oxidation treatment is more suitable for the WC-Co grades, or grades with low gamma phase content, <3 wt-%, due to the formation of stable Ti, Ta and Nb oxides . The decarburization treatment results in a surface zone Al which consists of eta phase (or W and Cθ7Wg) . A zone A2 also exists which contains eta phase and WC. The amount of eta phase in A2 is less than in Al . In case of weaker decarburization the Al will not be present only A2. If the decarburized zone mainly comprises eta phase the invention comprises a subsequent carburizing step following the initial decarburization. In this step the eta phase is completely transformed into WC+Co . The carburizing treatment comprises heat treatment for 20 min-10 h depending on the thickness of the eta phase layer in an atmosphere of 0.5-10% CH4 in H2 , preferably 2-4%, preferably at atmospheric pressure and at a temperature of 1275-1340°C, preferably 1320-1340°C. A preferred process involves carburizing the cemented carbide bodies on a carbon free support or on graphite support provided with Zrθ2- 2θ3 coatings. When graphite support is used and the decarburized zone comprises W phase, the W phase is transformed directly to WC using the graphite support as carbon source. No WC platelets are formed in this case since no eta phase is present before carburization. The carburizing heat treatment preferably performed in a H2 + CH4 gasatmosphere results in a surface zone Bl of thickness up to 100 μm, preferably 5-50 μm thick, which zone contains essentially triangular WC platelets. The size of the platelets is mainly governed by the thickness of Al and A2. Thicker A1+A2 gives larger platelets. To a certain extent the WC platelets are partially intergrown into each other. The WC platelets are present on at least 30%, preferably more than 50% and most preferably more than 75% of the surface of the cemented carbide body. At least 30% of the WC platelets, preferably more than 50% have a length (L) : hickness (T) ratio larger than 2:1, more preferably larger than 3:1. The average size of the platelets is length L<= 50 μm, preferably L<=10 μ m, but >=2 μm. Preferably, the WC platelets protrude above the level of the surface by 1/5-4/5 of their length. In a preferred embodiment, the majority of the WC platelets are oriented so that the angles α and β as defined in Fig lb are within 90 ± 45° for at least 30%, of the platelets. Based on XRD diffraction measuiements, a Texture Coefficient, TC, can be defined as: where 7( /) = measured intensity of the (hkl) reflection I 0 (hkl) = standard intensity of the ASTM standard powder pattern diffraction data n = number of reflections used in the calculation, (hkl) WC reflections used are: 001, 100, 101, 110, 002, 111, 200, 102 Furthermore, a texture coefficient ratio (TCR) can be defined such that: TCR(100:001) = TC (100) :TC (001) According to the invention the average WC texture coefficient ratio TCR (100 : 001) , calculated from at least 10 randomly related bodies is larger than 1.75, preferably larger than 2.0, more preferably larger than 2.5 and most preferably larger than 3.0. Several binder phase gradients are possible. In a first embodiment the binder phase gradient is obtained by a treatment at 1200-1330°C for 0.5h in vacuum, then 1330-1375°C, 0.2h to lh in CH 4 +H 2 atmosphere, using an eta phase containing body with A1+A2 of width 5-50 μm. After carburizing treatment, the binder phase content in zone Bl increases from <20% of the nominal content up to <70% in zone B2 and further up to a maximum of >10% above the nominal binder phase content in zone B3. The total thickness of B1+B2+B3 is 25-500 μm. An example of the binder phase distribution is shown in Fig 6a. Another preferred embodiment is obtained by heat treatment at 1200-1330°C for l/2h in vacuum, then at 1320-1340°C for 0.2-lh in CH4+H2, using an essentially stoichiometric WC-Co body with A1+A2 of width 5-20 μm. The binder phase content for the carburized body increases from <20% of the nominal content in Bl to >10% of the nominal binder phase content in B2 and in B3 up to 5-10% less than the nominal binder phase content within at distance of 5-300 μm. An example of the binder phase distribution is shown in Fig 6b. Yet another preferred embodiment is obtained by heat treatment at 1200-1330°C for 0.5h in vacuum, then at 1320- 1340°C for 0.2-lh in CH 4 +H 2 , using a WC-Co body with a stoichiometric carbon content up to free graphite. A1+A2 is 15-60 μm for a body with essentially or just below stoichiometric carbon content and 10-40 μm for a body with free graphite. In B1+B2 there is a maximum in binder phase content of more than 10% above the nominal binder phase content . In B3 the binder phase content is 10% lower than the nominal Co content. An example of the binder phase distribution is shown in Fig 6c. Yet another preferred embodiment is obtained by heattreatment at 1320-1340°C for 0.1-5 h in CH 4 +H 2 , using a body with a carbon content corresponding to an essentially stoichiometric or just below stoichiometric WC-Co. A1+A2 is 5-15 μm thick. The binder phase content in Bl is <20% of the nominal Co content. In B2 and B3 the Co content is somewhat lower or equal to the nominal Co content. B2+B3 can be up to 300 μm thick. An example of the binder phase distribution is shown in Fig 6d. A body according to the invention is coated with a wear resistant coating using any known coating method. For the case of a diamond coated body according to the invention, there may exist phases in the region between the diamond layer and the body which contain binder metal combined with any of the elements B, Si, Al, C, N or combinations thereof, preferably Al and C. In a preferred embodiment said region contains the phases CoAl , C03AIC0.5. The size of the WC platelets should be selected with respect to the coating thickness. Preferably, the average platelet size is L<l/2 of the coating thickness. Preferably, the WC grain size is <10 μm, and most preferably between 1 and 5 μm. The binder phase content shall be 4-12 wt-%. The binder phase should contain at least one of the following elements Co, Ni and Fe . The bodies suited for growing WC platelets may consist of cemented carbide containing WC-Co, WC-Co-eta phase, WC-Co-graphite and WC-Co-cubic phase carbides, carbonitrides (usually solid solution phase of Ti, Ta, Nb, ) with or without eta phase or graphite. If bodies comprising WC-Co-eta phase are used a 30 to 600 μm thick eta phase free zone will be formed close to the surface after carburizing heat treatment. The inner part of the body will however comprise an eta phase containing core. Gamma phase containing grades gradient sintered prior to decarburizing treatment with Co enriched surface zones between 5 and 50 μm can also be used. The WC platelets are more easily formed when carburizing is performed by carbon from external source (CH4) , besides CH4 , other carbon-hydrogen comprising gases can be used. However, sometimes WC platelets may also form using internal carbon source . EXAMPLE 1 Cutting tool inserts SPUN120308 WC-6 wt-% Co, 20 vol-% eta phase) were oxidised for 2 minutes in air at 850-900°C. X-ray diffraction analysis of the insert surface showed the presence of WO3 and C0WO4 phases . The inserts were then heat treated at 1300°C for 0.5 h in vacuum in order to obtain eta phase comprising zone, and finally carburized for 1 h at 1330°C in an atmosphere consisting of 2% CH4 + H2. The insert surface consisted essentially of WC platelets of with a size L within 2.5- 5 μm. At a position at the cutting edge the Co content increased from a level of <0.5 wt-% at the surface to a maximum of 40% above the nominal Co content at a depth of about 300 μm. Co distribution was similar to that shown in Fig 6a. The eta phase free zone was between 200 to 450 μm thick. The WC texture coefficient ratio TCR (100: 001) measured at the surface was found o be 3.77. Reference inserts, WC-6 wt-% Co-with the same eta phase content, were heat treated at 1300°C for 0.5 h in vacuum, and then carburized for 1 h at 1330°C in H+CH4 atmosphere according to US 4,843,039). The WC texture coefficient ratio was TCR (100 : 001) =1.43. Inserts from each of the groups were coated by an about 8 μm thick diamond coating in a DC arc plasma CVD coating process. Five inserts of each of the groups from example 1 were tested in a machining test at the following conditions: Material: Al 18%Si Longitudinal turning, wet cutting v = 300 m/min f = 0.1 mm/rev a = 1.5 mm In this test the inserts according to the invention lasted 9 min without any visible wear while the reference inserts showed coating wear through after 7 min. EXAMPLE 2 Cutting tool inserts VCGX160412 WC-6 wt-% Co-25 vol- % eta phase were oxidised for 3 minutes in air between 850 and 900°C. The X-ray diffraction analysis of the surface showed the presence of W0 3 and CoW0 4 phases . The inserts were heat treated at 1300°C for 0.5 h in vacuum and then carburized for 1 h at 1330°C in H+CH 4 atmosphere. The surface consisted of essentially WC platelets of with size L= 6-10 μm. The Co content at the cutting edge increased from a level of < 0.5 wt-% at the surface to a maximum of 25% above the nominal Co content at a depth of about 300 μm below the surface zone consisting of WC platelets. The WC texture coefficient ratio was TCR (100 : 001) =25.2. The inserts were coated with a diamond layer with a thickness of 20 μm using a DC arc CVD plasma method. Reference inserts were prepared as in Example 1 with TCR(100:001) =1.43. The inserts were tested in a machining test at the following conditions: Material: Al 9%Si Facing of bearing component, wet cutting rpm = 2500 m/min f = 0.25 mm/rev a = 3 mm In this test the inserts according to the invention lasted 15 components without any visible wear while the reference inserts showed flaking after eight components. EXAMPLE 3 Cutting tool inserts VCGX160412 of a WC-6 wt-% Co grade, without eta phase, were decarburized at 950°C in H2+H2O atmosphere for 6 hours. X-ray diffraction analysis of the insert surface showed the presence of W, Cθ7Wg, CogWgC and WC phases. The inserts were heat treated at 1300°C for 0.5 h in vacuum in order to transform W and Cθ7Wg phase to eta phase, and then in order to obtain WC platelets carburized for 0.5 h at 1330°C in H2+CH 4 atmosphere containing 2 vol-% CH4 _ In order to further decrease the Co content on the surface the inserts were electrochemically etched. Metallographic examination showed that the surface consisted of essentially WC platelets with size L=3-7μm. The Co distribution was similar to that shown in Fig 6b. The WC texture coefficient ratio was TCR(100:001) = 14. Reference inserts were prepared 1) as in Example 1, with TCR (100: 001) = 1.43 and 2) according to US 4,843,039 using a 2.5 wt-% Co grade for which TCR (100:001) = 1.25. Ten inserts of each group were diamond coated to a layer thickness of 20 μm using a DC arc CVD plasma method. The inserts were tested in a machining test at the following conditions: Material: Al 9%Si, age hardened Facing of bearing component, wet cutting rpm = 2500 m/min f = 0.7 mm/rev a = 3 mm In this test the inserts according to the invention lasted ten components without any visible wear or cracking while the reference inserts of both types showed nose cracking after four components or less. EXAMPLE 4 Cutting tool inserts were produced as in Example 3 except for decarburizing and carburizing step. Decarburizing was performed for 3 h at 950°C in H2+H2O atmosphere. The carburizing was performed for 20 minutes at 1330°C in H2+CH4 atmosphere containing 2 vol-% CH4. The average length of the WC platelets was L=2-4μm and TCR (100:001) = 6.0. The inserts were coated by an about 20 μm thick TiAlN coating in a magnetron sputtering PVD process . Two references were produced. The first reference, Reference No 1 , was produced from the same grade as the reference in Example 1. The second reference, Reference No 2 , was prepared from a grade with composition WC-6 wt-% Co without eta phase and with no decarburizing and carburizing treatment. The WC texture coefficient ratio was TCR(100:001)= 0.58. The inserts according to the invention showed good coating adhesion while spontaneous flaking of the coating was obtained for both references No 1 and No 2. EXAMPLE 5 Five cutting tool inserts of style N151.2-300-5E were prepared according to example 4 but the applied layer was 10 μm CVD TiN-Ti (C,N) -TiN. An improved adhesion was observed for the inserts according to the invention. The inserts were subject to a cutting tool life test using the parameters: Material: SS2343 Grooving of bar v = 300 m/min f = 0.2 mm/rev wet cutting The inserts according to the invention were used for machining 30 grooves before edge-line flaking was observed while reference inserts prepared by the application of the same layer on a WC-6 wt-% Co grade, showed flaking after machining of ten grooves. EXAMPLE 6 Cutting tool inserts of WC-6 wt-% Co grade, without eta phase and graphite were decarburized at 1250°C in H2+H2O atmosphere for 4h. X-ray diffraction analysis of the insert surface showed the presence of the eta phase (CogWgC and C02W4C) . The inserts were carburized for 1 h at 1330°C in H2+CH4 atmosphere containing 2 vol-% CH4 (heating up to carburizing temperature was performed in vacuum) . The insert surface consisted of WC platelets and Co. At the insert surface, the Co content was >50% of the nominal Co content as measured at the cutting edge. The average length of the WC platelets was L=5-10 μm. The Co rich zone containing WC platelets was about 40 μm thick. The Co distribution was similar to that shown in Fig 6c . The WC texture coefficient TCR (100 : 001) =61.6. The inserts were electrochemically etched. The inserts were coated with 10 μm CVD TiCN+5μm A1 2 0 3 . EXAMPLE 7 Cutting tool inserts of WC-6 wt-% Co grade, without eta phase and graphite were decarburized for lOh at 950°C in H2+H2O atmosphere. X-ray diffraction showed the presence of the W, Cθ7Wg and eta phase (CogWgC) . The inserts were heat treated at 1330°C in vacuum and then carburized at 1330°C for 0.5 in an atmosphere containing 2 vol-% CH4. The insert surface contained more than 50 vol-% WC platelets. The average length of the WC platelets was 5-10 μm. The Co content on the insert surface was <5% of the nominal Co content. The Co distribution was similar to that shown in Fig 6d. The WC texture coefficient TCR (100 : 001) =4.15 Reference inserts were prepared from the same grade but without decarburizing and carburizing treatment as in Example 7. The WC texture coefficient TCR (100:001)= 1.23. Ten inserts of each group were diamond coated to a layer thickness of 18 μm using a DC arc CVD plasma method. EXAMPLE 8 Cutting tool inserts of a WC-6 wt-% Co grade containing free graphite were decarburized at 950°C in H2+H2O atmosphere for 4 hours. The X-ray diffraction analysis of the insert surface showed the presence of W, Cθ7 g, CogWgC and WC phases. The inserts were heat treated at 1300°C for 0.5 h in vacuum and then carburized for 1.0 h at 1330°C in H2+CH4 atmosphere. The surface consisted of 30-40 vol-% WC platelets of with size L=5-10 μm. The Co content in zone Bl (see Fig 2b) was >100% of the nominal value and the width of the zone was 50 μm. The texture coefficient ratio TCR (100 : 001) = 11.2. The inserts were coated with 7 μm thick TiN+Ti(C,N) + 5 μm Al 2 0 3 . EXAMPLE 9 Cutting tool inserts of a composition 86 wt-% WC, 5.8 wt-% Co, 3.5 wt-% TiC, 2.3 wt-% TaC and 3.5 wt-% NbC without eta phase or graphite were decarburized at 1250°C in H2+H2O atmosphere for 4 hours. X-ray diffraction analysis showed presence of W, Cθ7 , eta phase and cubic carbide phase (gamma phase) . The inserts were heat treated in vacuum at 1330°C for 0.5 h and then carburized for 1 hour at 1330°C in H2+CH4 atmosphere containing 2 vol-% CH4. The cutting edge consisted of essentially WC platelets of with size L=10-20 μm. Minor amounts of gamma phase and Co were present at the surface. There was an enrichment of Co of >50% of the nominal Co content within a 25 μm thick zone, Bl, close to the surface. The WC texture coefficient ratio was TCR (100 :001) =23.6. The inserts were coated with a 10 μm TiN-Ti (C,N) layer + 8 μm AI2O3 layer.

Claims: Cla ms 1. Body of cemented carbide containing 4-12 wt-% binder phase coated with at least one wear resistant layer c h a r a c t e r i s e d in that the body contains a surface zone with a thickness up to 100 μm, which zone contains essentially triangular WC platelets for which the texture coefficient ratio TCR (100 : 001) is >1.75, preferably >2.0, more preferably >2.5 and most preferably >3.0. 2. Body according to claim 1 c h a r a c t e r i s e d in that said WC platelets show a length L to thickness T ratio of >2:1, preferably >3:1 and most preferably >5:1, an average size of length L<= 30 um, preferably L<=10 μm, but larger than 2 μm and, preferably the platelets protrude above the level of the surface by 1/5-4/5 of their length. 3. Body according to claims 1-2 c h a r a c t e r i s e d in the average binder phase content increases from <20% of the nominal binder phase content in zone Bl up to a maximum of >10% above the nominal binder phase content in zone B3 at a depth of 50-500 μm. 4. Body according to claims 1-3 c h a r a c t e r i s e d in that the binder phase content increases from <20% of the nominal binder phase content in zone Bl up to at least nominal binder phase content or higher in zone B2 and then decreases to a minimum of >50% of the nominal binder phase content in zone B3 at a depth of 5-500 μm. 5. Body according to claims 1-3 c h a r a c t e r i s e d in that the binder phase concentration in the zone Bl is >20% of the nominal binder phase content and for zone B2 of width 5-100 μm there exists a maximum of +50 vol-% of the nominal binder phase content . 6. Body according to claims 1-3 c h a r a c t e r i s e d in that the binder phase concentration in the zone Bl is < 20% of the nominal binder phase content and for zones B2 and B3 of width 0- 500 μm is Co level within ± 10% of the nominal binder phase content . 7. Body according to claims 1-5 c h a r a c t e r i s e d in that the applied outer layer is a CVD diamond layer. 8. Body according to claim 6 c h a r a c t e r i s e d in that there exist phases in the region between the diamond layer and the carbide body which contain binder metal combined with any of the elements B, Si, Al, C, N or combinations thereof, preferably Al and C preferably the phases CoAl, Co 3 AlC 0 . 5 . 9. Method for producing a diamond coated cemented carbide body with a surface zone in the cemented carbide being different from the rest of the carbide body c h a r a c t e r i s e d in that the cemented carbide body is - decarburized to form an eta phase (or W + Cθ7Wg phase) containing surface zone 3-100 μm thick and comprising >60% by volume of at least partially interconnected eta phase which eta phase in case of presence of W and Cθ7W phases after the decarburization treatment is obtained by an additional heat treating step transforming W and Cθ7Wg phases to eta phase and then - recarburized whereby the eta phase is completely transformed into WC+Co. 10. Method according to claim 9 c h a r a c t e r i s e d in that the decarburization is made by heating the body to a temperature between 900 and 1350°C, preferably between 950 and 1250°C, in a decarburizing atmosphere, such as H2+H2O, for 1-10 h. 11. Method according to claim 9 c h a r a c t e r i s e d in that the decarburization treatment comprises a series of steps according to: step 1: T = 500-900°C in air, C0 or 0 2 , preferably air whereby oxides such as WO3 or C0WO4 are formed step 2 (optional) : T = 500-900°C in reducing atmosphere, for example comprising H2 , whereby the oxides are transformed into metals, for example W and Cθ7W 6 . step 3: T= 1000-1400°C in vacuum or in Ar such that eta phase is formed which treatment results in a surface zone Al which consists of eta phase+WC or eta phase only and an optional zone A2 which zone contains eta phase+WC in different relative amounts compared to zone Al . 12. Method according to claims 9-11 c h a r a c t e r i s e d by carburising the body for 10 min-10 h in an atmosphere of 0.5-10% CH4 in H2 , preferably 2-4%, preferably at atmospheric pressure and at a temperature of 1250- 1340°C, preferably 1315- 1330°C.

Inventors: MIKUS MARIAN, REINECK INGRID, MIKUS, MARIAN, REINECK, INGRID
Applicants: MIKUS MARIAN, REINECK INGRID, SANDVIK AB, MIKUS, MARIAN, REINECK, INGRID, SANDVIK AB (PUBL)
Application year: 1998
Main classification: C23C16
IPC codes: B23B27, C23C14, C23C16, C23C30