Patent Application
20240207943
The present invention relates to a coated cutting tool comprising a substrate and a coating, wherein the coating comprises a Ti(C,N) layer with an average grain size between 25 nm and 35 nm.
In the technical area of cutting tools for metal machining, the usage of CVD coatings is a well-known method to enhance the wear resistance of the tools. CVD coatings of ceramic materials such as TiN, TiC, Ti(C,N) and Al2O3 are commonly used.
EP2791387 discloses a coated cutting tool provided with a fine-grained titanium carbonitride layer. The coating is advantageous in showing high resistance to flaking in turning of nodular cast iron and in high speed cutting. A columnar MTCVD Ti(C,N) layer is described with an average grain width of 0.05-0.4 μm.
There is a continuous need of finding cutting tool coatings that can prolong the lifetime of the cutting tool and/or that can withstand higher cutting speeds than the known cutting tool coatings.
One object of the present invention is to provide a coated cutting tool with improved resistance to wear in metal cutting applications. A further object is to improve its resistance in turning operations, especially in turning of steel and hardened steel. It is a further object to provide a wear resistant coating that provides a high crater and flank wear resistance in turning of steel and hardened steel.
At least one of these objects is achieved with a coated cutting tool according to claim 1.
Preferred embodiments are listed in the dependent claims.
The present disclosure relates to a cutting tool for metal cutting, wherein said cutting tool comprise a substrate at least partially coated with a 3-30 μm coating, said substrate is of cemented carbide, cermet or ceramic, said coating comprise one or more layers, wherein at least one layer is a Ti(C,N) layer with a thickness of 3-25 μm, wherein said Ti(C,N) layer being composed of columnar grains wherein the average grain size D422 of the Ti(C,N) layer, as measured with X-ray diffraction with CuKα radiation, the grain size D422 is calculated from the full width at half maximum (FWHM) of the (422) peak according to Scherrer's equation:
wherein D422 is the mean grain size of the Ti(C,N) grains in the Ti(C,N) layer, K is the shape factor here set at 0.9, λ is the wavelength for the CuKα1 radiation here set at 1.5405 Å, B422 is the FWHM value for the (422) reflection and θ is the Bragg angle, wherein D422 is ≥25 nm and ≤35 nm.
It has surprisingly been found that a cutting tool provided with a very fine grained Ti(C,N) layer shows a very high resistance to wear when used in metal cutting applications such as turning in high alloyed steel. It is believed that the combination of a crystallinity and columnar grains with a high amount of grain boundaries contributes to the high wear resistance.
In one embodiment of the present invention said at least one Ti(C,N) layer exhibits an X-ray diffraction pattern, as measured using CuKα radiation and θ-2θ scan, wherein the TC(hkl) is defined according to Harris formula:
where I(hkl) is the measured intensity (integrated area) of the (hkl) reflection, 10 (hkl) is the standard intensity according to ICDD's PDF-card No. 42-1489, n is the number of reflections, reflections used in the calculation are (1 1 1), (2 0 0), (2 2 0), (3 1 1), (3 3 1), (4 2 0) and (4 2 2), wherein TC(422)≥3.
In one embodiment of the present invention the said at least one Ti(C,N) layer is 6-25 μm in thickness and exhibits an X-ray diffraction pattern, wherein TC(422)≥4.
In one embodiment of the present invention the said at least one Ti(C,N) layer is 4.5-25 μm in thickness and exhibits an X-ray diffraction pattern, wherein TC(422) is the highest and TC(311) is the second highest. In one embodiment of the present invention the ratio C/(C+N) in the Ti(C,N) layer is 50% to 70%, preferably 55% to 65%. This composition is advantageous in that this Ti(C,N) layer shows a high chemical stability.
In one embodiment of the present invention the coating comprises an innermost layer of TiN.
In one embodiment of the present invention the Ti(C,N) layer is the outermost layer of the coating.
The present invention also relates to the use of the cutting tools described above in metal cutting.
In one embodiment of the present invention the cutting tool is used in metal cutting in high alloyed steel, hardened steel, cast iron or stainless steel, preferably used in metal cutting in high alloyed steel.
In one embodiment of the present invention the cutting tool is a drill, a milling insert or a turning insert, preferably a turning insert.
The coated cutting tools described herein can be subjected to post-treatments such as blasting, brushing or shot peening in any combination. A blasting post-treatment can be wet blasting or dry blasting for example using alumina particles.
Still other objects and features of the present invention will become apparent from the following definitions and examples considered in conjunction with the accompanying drawings.
Embodiments of the invention will be described with reference to the accompanying drawings, wherein:
The term “cutting tool” is herein intended to denote cutting tools suitable for metal cutting applications such as inserts, end mills or drills. The application areas can for example be turning, milling or drilling in metals such as steel.
In order to investigate the texture or orientation of the layer(s) and also the average grain size, X-ray diffraction (XRD) was conducted on the flank face using a PANalytical CubiX3 diffractometer equipped with a PIXcel detector. The coated cutting tools were mounted in sample holders to ensure that the flank face of the samples are parallel to the reference surface of the sample holder and also that the flank face is at appropriate height. Cu-Kα radiation was used for the measurements, with a voltage of 45 kV and a current of 40 mA. Anti-scatter slit of ½ degree and divergence slit of ¼ degree were used. The diffracted intensity from the coated cutting tool was measured in the 20 range 20° to 140°, i.e. over an incident angle θ range from 10 to 70°. The data analysis, including background fitting, Cu-Kα2 stripping and profile fitting of the data, was done using PANalytical's X′Pert HighScore Plus software.
The integrated peak full width at half maximum for the profile fitted curve achieved from PANalytical's X′Pert HighScore Plus software was used to calculate the grain size of the layer according to the Scherrer equation (Eq1) (Birkholz, 2006).
The average grain size D422 is calculated from the full width at half maximum (FWHM) of the (422) peak according to Scherrer's equation:
wherein D422 is the mean grain size of the Ti(C,N), K is the shape factor here set at 0.9, λ is the wave length for the CuKα1 radiation here set at 1.5405 Å, B is the FWHM value for the (422) reflection and θ is the Bragg angle i.e the incident angle.
β is the line broadening (in radians) at FWHM after subtracting the instrumental broadening (0,00174533 radians), θ is the incident angle. For the calculation of the broadening with subtraction of the instrumental broadening, a Gaussian approximation was used (Eq2)(Birkholz, 2006):
β=√((FWHMobs)2−(FWHMins)2)
Where β is the real broadening (in radians) used for the grain size calculation, FWHMobs is the measured broadening (in radians), FWHMins is the instrumental broadening (in radians).
The texture or orientation of the layer(s) was defined based on the X-ray diffraction pattern, measured using CuKα radiation and θ-2θ scan, wherein the TC(hkl) was defined according to Harris formula:
where I(hkl) is the measured intensity (integrated area) of the (hkl) reflection, I0(hkl) is the standard intensity according to ICDD's PDF-card No. 42-1489, n is the number of reflections, reflections used in the calculation are (1 1 1), (2 0 0), (2 2 0), (3 1 1), (3 3 1), (4 2 0) and (4 2 2).
Since possible further layers above the Ti(C,N)-layer will affect the X-ray intensities entering the Ti(C,N)-layer and exiting the whole coating, corrections need to be made for these, taken into account the linear absorption coefficient for the respective compound in a layer. Alternatively, a further layer, above the Ti(C,N)-single-layer can be removed by a method that does not substantially influence the XRD measurement results, e.g. chemical etching.
It is to be noted that peak overlap is a phenomenon that can occur in X-ray diffraction analysis of coatings comprising for example several crystalline layers and/or that are deposited on a substrate comprising crystalline phases, and this has to be considered and compensated for by the skilled person. It is also to be noted that for example WC in the substrate can have diffraction peaks close to the relevant peaks of the present invention.
Elemental analysis is performed by electron microprobe analysis using a JEOL electron microprobe JXA-8530F equipped with wavelength dispersive spectrometer (WDS) in order to determine C/(C+N) ratio of the Ti(C,N) layers presented in
Exemplifying embodiments of the present invention will now be disclosed in more detail and compared to reference embodiments. Coated cutting tools (inserts) were manufactured, analyzed and evaluated in cutting tests.
Cemented carbide substrates were manufactured utilizing conventional processes including milling, mixing, spray drying, pressing and sintering. The sintered substrates were CVD coated in a radial CVD reactor of Ionbond Type size 530 capable of housing 10.000 half inch size cutting inserts. The substrates were placed on the plates and the samples to be tested and analysed further were selected from the middle of the chamber and at a position along half the radius of the plate. The ISO-type geometry of the cemented carbide substrates (inserts) were CNMG-120408-PM. The composition of the cemented carbide was 7.2 wt % Co, 2.9 wt % TaC, 0.5 wt % NbC, 1.9 wt % TiC, 0.4 wt % TiN and the rest WC.
A first innermost coating of about 0.2 μm TiN was deposited on all substrates in a process at 400 mbar and 885° C. A gas mixture of 48.8 vol % H2, 48.8 vol % N2 and 2.4 vol % TiCl4 was used. Thereafter the Ti(C,N) layers were deposited as disclosed below.
On the sample A the Ti(C,N) layer was deposited in one step at 80 mbar at 870° C. in a gas mixture of 2.95 vol % TiCl4, 0.45 vol % CH3CN and balance H2.
On the sample B the Ti(C,N) layer was deposited in one step at 80 mbar at 830° C. in a gas mixture of 2.95 vol % TiCl4, 0.45 vol % CH3CN and balance H2.
On the sample C the Ti(C,N) layer was deposited in two steps, an inner Ti(C,N) and an outer Ti(C,N). The inner Ti(C,N) was deposited for 10 minutes at 55 mbar at 885° C. in a gas mixture of 3.0 vol % TiCl4, 0.45 vol % CH3CN, 37.6 vol % N2 and balance H2. The outer Ti(C,N) was deposited at 55 mbar at 885° C. in a gas mixture of 7.8 vol % N2, 7.8 vol % HCl, 2.4 vol % TiCl4, 0.65 vol % CH3CN and balance H2.
The layer thicknesses were measured on the rake face of the cutting tool samples using light optical microscope. The layer thicknesses of the coating the samples A-C are shown in Table 1.
The grain size of the Ti(C,N) layers were analysed with X-ray diffraction analysing the 422 peak as disclosed above. The ratios C/(C+N) of the Ti(C,N) layers were analysed using electron microprobe analysis as disclosed above. The resulting grain sizes and carbon contents for the samples A, B and C are presented in Table 2.
The orientation of the Ti(C,N) layers were analysed using X-ray diffraction as disclosed above. The results are presented in Table 3.
The grain size of the Ti(C,N) in the samples were also studied via TEM images of a plane view of the Ti(C,N) layer. Cross-sections of each sample were first prepared by cutting the insert in the middle and thereafter polishing the cross-sections. FIB (focused ion beam) lamellae were then taken from the Ti(C,N) coating parallel to the substrate surface, at about 6 μm from the coating-substrate interface using a lift-out technique. The lamellae were thinned using an ion beam until electron transparency was achieved. Bright-field scanning TEM images were acquired on a ThermoFisherScientific Titan transmission electron microscope operated at 300 kV. TKD (transmission Kikuchi diffraction) maps were collected with an Oxford Aztec system installed on a ThermoFisherScientific Helios FIB-SEM. The IPF (inverse pole figure) maps with grain boundary overlay were produced with AztecCrystal software. The bright field images are shown in
The cutting tools were tested in a longitudinal turning operation in a work piece material of SS2310, a high alloyed steel. The cutting speed, Vc, was 125 m/min, the feed, fn, was 0.072 mm/revolution, the depth of cut, ap, was 2 mm and water miscible cutting fluid was used. The machining was continued until the end of life time criterion was reached. One cutting edge per cutting tool was evaluated.
The tool life criterion was set to: for the primary or secondary flank wear >0.3 mm or for the crater area >0.2 mm2. As soon as any of these criteria were met the lifetime of the sample was considered reached. The result of the cutting test is presented in Table 4.
As can be seen in Table 4 the sample A shows an unexpectedly high wear resistance with a lifetime close to the double as compared to the samples B and C.
The cutting tools were also tested in an intermittent face turning operation in a square bar 100*100 mm work piece material of SS1672 steel. The cutting speed, Vc, was 250 m/min, the feed, fn, was 0.1 mm/revolution, the depth of cut, ap, was 2.5 mm and water miscible cutting fluid was used. The machining was continued until the end of lifetime criterion was reached. One cutting edge per cutting tool was evaluated.
In evaluating the tool wear the % of damage of the primary edge line was measured along the contact length where the primary edge had been in contact with the workpiece material. The tool life criterion was set to >40% damage such that the substrate was exposed along the primary edge line in the area of contact with the work piece material. The tool wear was measured every three cycles, i.e. after three facing passes. As soon as the criteria was met the lifetime of the tool was considered reached. To calculate the final tool life of 40% damage a simple interpolation between the damage before and after reaching 40% of damage was made. The average results of 4 parallel cutting tests per type of sample are presented in Table 5. Occasionally, cutting edge breakage was observed, these were removed from the results. Only samples showing continuous wear and thereby reflecting the contribution from the coating on the tool life, are included here.
While the invention has been described in connection with various exemplary embodiments, it is to be understood that the invention is not to be limited to the disclosed exemplary embodiments, on the contrary, it is intended to cover various modifications and equivalent arrangements within the appended claims. Furthermore, it should be recognized that any disclosed form or embodiment of the invention may be incorporated in any other disclosed or described or suggested form or embodiment as a general matter of design choice. It is the intention, therefore, to be limited only as indicated by the scope of the appended claims appended hereto.
| Number | Date | Country | Kind |
|---|---|---|---|
| 21170080.2 | Apr 2021 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2022/060698 | 4/22/2022 | WO |
