Method of manufacturing a sintered carbonitride alloy with improved toughness behaviour

Abstract: According to the invention there is now provided method of manufacturing a sintered body of titanium based carbonitride alloy comprising hard constituents in 5-25 % binder phase where the hard constituents contain, in addition to Ti, one or more of the metals V, Nb, Ta, Cr, Mo or W and the binder phase is based on cobalt and/or nickel by powder metallurgical methods, i.e., milling, pressing and sintering. The composition of the hard constituent is: 0.88<a<0.96, 0.04<b<0.08, 0≦c<0.04, 0≦d<0.04, 0.60<f<0.73 0.80<x<0.90, and 0.31<h<0.40. if the overall composition of the hard constituent phase is expressed by the formula: (Ti a , Ta b , Nb c , V d ) x (Mo e , W f ) y (C g , N h ) z . Favourable properties are obtained if the alloy is made from a powder mixture comprising 23-28 % by weight Ti(C,N) with a nitrogen content between 9 and 13% by weight, 13-17 % by weight (Ti,Ta) (C,N) with a Ti/Ta ratio of 80/20 14-18 % by weight (Ti,Ta)C with a Ti/Ta ratio of 50/50 and 15-20% by weight WC and 3-7 % by weight Mo₂C provided that the total amount of said five powders is >78 % by weight and <83 % by weight.

Description: The present invention relates to a sintered carbonitride alloy with titanium as main component, so called cermets, intended for milling, drilling and turning which alloy has very good toughness behaviour in combination with good wear resistance. Classic titanium based cutting tool material was based on titanium carbide, molybdenum carbide and nickel. These materials were used for high speed finishing owing to their extraordinary wear resistance at high cutting temperatures. The toughness behaviour and resistance against plastic deformation were not satisfactory, however, and so the area of application was rather limited. Development has proceeded and the range of application for sintered titanium carbonitride based alloys has been considerably enlarged. The toughness behaviour and the resistance against plastic deformation have been considerably improved. An important development of titanium based hard alloys is substitution of carbon by nitrogen in the hard constituents. This decreases, e.g., the grain size, usually 1-2 µm, of the hard constituent in the alloy which leads to the possibility of increasing the toughness behaviour. In general, nitrides are more chemically stable than carbides which results in lower tendencies to sticking of workpiece material or wear by dissolution of the tool, so called diffusional wear. For the binder phase, the metals of the iron group are used, often Co and Ni in combination. The amount of binder phase is generally 5-25% by weight. Besides titanium, the other metals of the group IVA, VA, VIA are normally used as hard phase formers such as carbides, nitrides and/or carbonitrides. There are also other metals used, for example Al, which sometimes are said to harden the binder phase and sometimes improve the wetting behaviour between hard phase and binder phase. A very common or even normal microstructure of sintered carbonitride alloy consists of a core-rim structure. For example, US 3,971,656 discloses a sintered carbonitride alloy which comprises Ti- and N-rich cores and rims rich in Mo, W and C. From Swedish patent application SE 8902306-3 it is known that different combinations of duplex core-rim structures in well balanced proportions give improved wear resistance or toughness behaviour properties. The distribution of hard constituent particles containing titanium, tantalum and tungsten especially affects the cutting properties for different sintered titanium based carbonitride alloys with the same overall chemical composition. The difference in cutting behaviour remains even when the overall carbon content varies. From the literature on titanium based carbonitride alloys, it is apparent that the trend of substituting carbon by nitrogen is very common. It has been shown that properties related to toughness behaviour in metal cutting operations (turning, milling and drilling) in general have been improved by substituting titanium carbide by titanium nitride or titanium carbonitride. This holds for a nitrogen content up to a certain level where the wetting properties no longer permit a sintered material without pores. Although diffusional wear (crater wear) resistance is improved with increasing nitrogen content, wear resistance in general decreases with increasing nitrogen content. The microstructure and the metal cutting properties of sintered titanium based carbonitrides with the same overall chemical composition vary. For a production process similar to the process generally used in the production of cemented carbides, including pressing and vacuum sintering, different hard constituents behave differently during the liquid phase sintering. Some of the hard constituent particles remain as cores in the sintered carbonitride alloy and inherit more or less completely their metallic composition, while others are completely dissolved and affect the rim-structure formation. EP 417 333 discloses a method of making a titanium based carbonitride alloy characterized by the steps of preparing a first powder for forming the core, preparing second powders for forming the rims and preparing a third powder for forming the binder phase. Said powders are milled, compacted and sintered. The first powder is formed of at least one compound selected from the group consisting of TiC, TiCN, (Ti,Ta)C and (Ti,Ta) (C,N). It has now surprisingly been found that it is possible to obtain a sintered titanium based carbonitride alloy with high nitrogen content sintered in vacuum with an excellent metal cutting toughness behaviour and at the same time with a very good wear resistance and reduced porosity. The cutting properties mainly in milling and drilling but also in turning have been balanced and the resulting cutting life time has been improved. These balanced cutting properties for the titanium based carbonitride alloy according to the invention have been possible to obtain only in a very narrow compositional range in combination with a certain combination of raw materials. It is convenient to represent the composition of the hard constituent phase in titanium based carbonitride alloys with the formula (Ti a , Ta b , Nb c , V d ) x (Mo e , W f ) y (C g , N h ) z where the indexes a-f are the molar index of respective element of the carbide, carbonitride or nitride formers, and the indexes g-h are the molar index of carbon and nitrogen respectively. The following relations apply: a+b+c+d=1, e+f=1, g+h=1, x+y=1 and z<1. The titanium based sintered alloy according to the present invention is characterized by the following relations: 0.88<a<0.96, preferably 0.90<a<0.94 0.04<b<0.08, preferably 0.05<b<0.07 0≤c<0.04, preferably 0≤c<0.03 0≤d<0.04, preferably 0≤d<0.03 0.60<f<0.73 preferably 0.66<f<0.72 0.80<x<0.90, preferably 0.82<x<0.88 and 0.32<h<0.40, preferably 0.34<h<0.38 Oxygen is present as impurity. The total amount of binder which consists of Co+Ni is 12-17%, preferably 14-17% by weight with 0.6<Co/(Co+Ni)<0.7, preferably Co/(Co+Ni)=2/3. When manufacturing carbonitride alloys it is possible to obtain very different microstructures after sintering, although the overall chemical composition is kept constant. Usually used terms for the microstructure are hard cores, surrounding structure and binder phase. It is known that the volume fraction of the cores and the surrounding structure varies with the type of raw materials used, when comparing the sintered microstructure for titanium based carbonitride alloys of the same overall chemical composition. A titanium based carbonitride alloy according to the invention is manufactured by mixing powders forming hard cores, surrounding structure and binder phase. Powders are mixed at the same time to a mixture with desired composition. After forming the mixture a titanium based carbonitride alloy according to the invention is manufactured with powder metallurgical methods. In order to obtain the favourable properties of an alloy according to the invention the powder mixture has to contain the following in percent of the whole mixture including Co and/or Ni: 23-28 % by weight Ti(C,N) with a nitrogen content between 9 and 13% by weight, 13-17 % by weight (Ti,Ta)(C,N) with a Ti/Ta ratio of 80/20 14-18 % by weight (Ti,Ta)C with a Ti/Ta ratio of 50/50 15-20 % by weight WC and 3-7 % by weight Mo 2 C. The total amount of said powders shall be >78 and <83 % by weight. Remaining starting materials are added as VC, TiN and/or NbC. In titanium based alloy according to the invention, the titanium could be replaced by niobium and/or vanadium in an amount not greater than 4 atomic percent. In a preferred embodiment the grains of at least one of said Ti-containing powders are rounded, non-angular with a logarithmic normal distribution standard deviation of <0.23 logarithmic µm most preferably produced by directly carburizing or carbonitriding of the metals or their oxides. From the mixture bodies are pressed and sintered in vacuum at a pressure of <10 mbar at 1400-1600°C. The cooling to room temperature takes place in vacuum or inert gas. Example 1 From a powder with a composition (a=0.902, b=0.059, c=0, d=0.039, f=0.667, h=0.384 and x=0.862) with the following mixture of raw material in percent by weight: 15.6 (Ti,Ta)80/20(C,N), 15.4 (Ti,Ta)50/50C, 2.2 TiN, 25,6 Ti(C,N), 1.7 VC, 18 WC, 4.7 Mo 2 C, 11.2 Co and 5.6 Ni, milling inserts SPKN 1203 were pressed and vacuum sintered at 1430°C for 90 min. The porosity after sintering was <A06. The inserts were ground with a negative chamfer of 10°. From another powder with exactly the same elemental chemical analysis as the material above but with simple raw materials (TiC, TaC, TiN, Ti(C,N)), milling inserts of the same style were pressed and sintered at 1430°C for 90 min. The porosity after sintering turned out to be A08 or sometimes >A08. Example 2 SPKN 1203 inserts from the two titanium based alloys in example 1 were tested in milling operations. Toughness tests were performed by using single tooth end milling over a rod made of SS2541 with a diameter of 80 mm. The cutter body with a diameter of 250 mm was centrally positioned in relation to the rod. The cutting parameter used was: speed 130 m/min and depth of cut 2.0 mm. The feed corresponding to 50% fracture after testing 30 inserts per variant was 0.21 mm/rev for the variant with simple raw materials and 0.35 for the alloy according to the invention. Example 3 SPKN 1203 inserts from the two titanium based alloys in example 1 were tested in milling operations. Wear resistance was tested in steel SS1672 with the following cutting parameters: Single tooth milling along a rectangular shaped workpiece with a width of 97 mm, depth of cut 2.0 mm, feed 0.12 mm/rev and cutting speed 370 m/min. The cutter body with a diameter of 125 mm was centrally positioned in relation to the workpiece. The wear results were normalized with the relative value for the variant with simple raw materials set equal to 1.0. The results were: Flank wear: 1.1 Crater wear: 1.0 When summarizing the results in examples 1-3 it is obvious that the alloy according to the invention has obtained an improved overall cutting behaviour compared to an alloy with the same composition but produced with simple raw materials. Example 4 From a powder with a composition according to the invention (a=0.920, b=0.060, c=0.020, d=0, f=0.672, h=0.391 and x=0.861) with the following mixture of raw material in percent by weight: 15.5 (Ti,Ta)80/20(C,N), 15.5 (Ti,Ta)50/50C, 2.2 TiN, 26.0 Ti(C,N), 1.8 NbC, 18 WC, 4.6 Mo 2 C, 10.9 Co and 5.5 Ni, milling inserts SPKN 1203 were pressed and vacuum sintered at 1440°C for 90 min. The porosity after sintering was <A06. The inserts were ground with a negative chamfer of 10°. From another powder with exactly the same elemental chemical analysis as the material above but with simple raw materials (TiC, TiN, Ti(C,N), TaC), milling inserts of the same style were pressed and sintered at 1440°C for 90 min. The porosity after sintering turned out to be >A08. Example 5 SPKN 1203 inserts from the two titanium based alloys in example 4 were tested in milling operations. Toughness test was performed in the same way as described in example 2 and wear resistance tests were performed in the same way as described in example 3. The feed corresponding to 50% fracture after testing 30 inserts per variant was 0.21 mm/rev for the variant with simple raw materials and 0.37 mm/rev for the alloy according to the invention. The normalized wear results, described as in example 3, were: Flank wear: 1.1 Crater wear: 1.1 Example 6 From a powder according to the invention with a composition according to example 4, milling inserts SPKN 1203 were pressed and vacuum sintered at 1440°C for 90 min. From another powder with exactly the same elemental chemical composition but with other types of complex raw materials, the tantalum was added as a titanium-tantalum carbonitride with 21 mole % tantalum and a N/(C+N) ratio of 0.67, milling inserts of the same type were pressed and sintered at 1440°C for 90 min. The milling tests were performed in exactly the same way as in examples 2 and 3. The feed corresponding to 50% fracture after testing 30 inserts per variant was 0.37 mm/rev for the material according to the invention and 0.23 mm/rev for the material with the same chemical composition but with a mixture of complex raw materials outside the invention. Example 7 From the two powder batches described in example 1 turning inserts CNMG 120408 were pressed and sintered at 1440°C for 90 min. A turning toughness test was performed on a slotted bar made of SS2244 with the following cutting data: Speed: 80 m/min Feed: 0.15 mm/rev Depth of cut: 2.0 mm. The time corresponding to 50% fracture was 4.0 min for the material according to the invention and 2.5 min for the material with the same chemical analysis but with simple raw materials. Example 8 From a powder A with a composition according to the invention (a=0.921, b=0.059, c=0.020, d=0, f=0.670, h=0.390 and x=0.860) with the following mixture of raw material in percent by weight: 15.3 (Ti,Ta)80/20(C,N), 15.3 (Ti,Ta)50/50C, 2.2 TiN, 26.2 Ti(C,N), 1.8 NbC, 18 WC, 4.7 Mo 2 C, 11.0 Co and 5.5 Ni, milling inserts SPKN 1203 were pressed and vacuum sintered at 1440°C for 90 min. The porosity after sintering was <A06. The inserts were ground with a negative chamfer of 10°. From another powder B with exactly the same elemental chemical analysis as the material above but made from Ti containing raw materials with rounded non angular grains with a narrow grain size distribution milling inserts of the same style were pressed and sintered. The porosity was A06 or better. From yet another powder C with exactly the same elemental chemical analysis as the material above but with simple raw materials (TiC, TiN, Ti(C,N), TaC), milling inserts of the same style were pressed and sintered at 1440°C for 90 min. The porosity after sintering turned out to be >A08. Example 9 The inserts from the three titanium based alloys in example 8 were tested in milling operations. A toughness test was performed in the same way as described in example 2 and wear resistance tests were performed in the same way as described in example 3. The feed corresponding to 50% fracture after testing 30 inserts per variant was: Alloy Feed, mm/rev A 0.34 B 0.46 C 0.21 The normalized wear results, described as in example 3, were: A B C Flank wear: 1.1 1.2 1 Crater wear: 1.1 1.1 1 It can be seen that not only were alloys A and B of the present invention better than the comparison alloy C but also that alloy B containing the rounded, non-angular grains showed improved properties even over alloy A.

Claims: Method of manufacturing a titanium based carbonitride alloy comprising hard constituents in a binder phase based on cobalt and nickel where the composition of the hard constituent phase is represented by the formula with molar indexes: (Ti a , Ta b , Nb c , V d ) x (Mo e , W f ) y (C g , N h ) z by powder metallurgical methods, i.e., milling, pressing and sintering characterized in that: 0.88<a<0.96, 0.04<b<0.08, 0≤c<0.04, 0≤d<0.04, 0.60<f<0.73 0.80<x<0.90, 0.31<h<0.40, a+b+c+d=1, e+f=1, g+h=1, x+y=1 and z<1. and that said alloy is made from a powder mixture containing the following five powders 23-28 % by weight Ti(C,N) with a nitrogen content between 9 and 13% by weight, 13-17 % by weight (Ti,Ta) (C,N) with a Ti/Ta ratio of 80/20 14-18 % by weight (Ti,Ta)C with a Ti/Ta ratio of 50/50 15-20 % by weight WC and 3-7 % by weight Mo 2 C provided that the total amount of said four powders is >78 % by weight and <83 % by weight and the remaining starting materials added as TiN, NbC, VC, Co and or Ni. Method according to the previous claim characterized in that the binder phase content is 12-17 % by weight with 0.6<Co/(Co+Ni)<0.7. Method according to any of the previous claims characterized in that 0.90<a<0.94 0.05<b<0.07 0≤c<0.03 0≤d<0.03 0.66<f<0.72 0.82<x<0.88 and 0.34<h<0.38. Method according to any of the previous claims characterized in that the binder phase content is 14-17 % by weight and Co/(Co+Ni)=2/3. Method according to any of the previous claims characterized in that the grains of at least one of said Ti-containing powders are rounded, non-angular with a logarithmic normal distribution standard deviation of <0.23 logarithmic µm, preferably produced by directly carburizing or carbonitriding of the metals or their oxides.

Inventors: OESTLUND AKE, OESTLUND, AKE, Östlund, Ake
Applicants: SANDVIK AB, SANDVIK AKTIEBOLAG
Application year: 1993
Main classification: C22C29
IPC codes: C22F1, B22F1, C22C29, C22C1, B23P15, B23B27