Patent Application
20200002819
The present invention relates to a tool having a base body of cemented carbide, cermet, ceramics, steel, cubic boron nitride or high-speed steel and a single-layer or multi-layer wear protection coating deposited by a CVD process and having a thickness within the range of 5 μm to 24 μm, wherein the wear protection coating comprises at least a T1-xAlxN layer with 0.40≤x≤0.95 having a thickness in the range of 4 μm to 14 μm and having >90 vol-% face-centered cubic (fcc) crystal structure. The present invention further relates to a process for the production of the inventive tool.
Cutting tools for metal cutting operations such as drilling, milling and turning need to be highly wear resistant and oxidation resistant since they are typically used in very abrasive and heat generating operations. Coated cutting tools are known in the art and hard material layers may be applied by PVD and/or CVD.
U.S. Pat. No. 8,389,134 discloses a CVD coated cutting tool comprising an Al2O3 outer layer and an inner T1-xAlxN layer.
The object of the present invention is to provide coated tools for the chip forming metal machining of steel or cast materials, which exhibit, compared to the prior art, improved wear resistance and improved comb crack resistance in dry machining, as well as under the use of coolant. Another object is to provide a coated cutting tool suitable for turning in steel.
The present invention relates to a coated cutting tool comprising a substrate and a coating, wherein the coating comprises an inner layer of 4-14 μm thick T1-xAlxN, an intermediate layer of 0.05-1 μm TiCN and at least one outer layer of 1-9 μm αt-Al2O3, wherein said α-Al2O3 layer exhibits an X-ray diffraction pattern, as measured using CuKα radiation and theta-2theta scan, and the texture coefficient TC(hkl) is defined according to Harris formula
wherein the (hkl) reflections used are (0 2 4), (1 1 6), (3 0 0) and (0 0 12), I(hkl)=measured intensity (peak intensity) of the (hkl) reflection, 10(hkl)=standard intensity according to ICDD's PDF-card No. 00-042-1468, n=number of reflections used in the calculation, and in that 3<TC(0 0 12)<4.
The cutting tool is a tool for chip metal cutting and can for example be a drill, a mill or an insert for drilling, milling or turning. The cutting tool is preferably an insert for turning, preferably for turning in steel.
The wear resistant coating on the cutting tool of the present invention comprises a highly wear resistant T1-xAlxN layer and a very crater wear resistant α-Al2O3 layer. These two layers are the layers that contributes most to the wear resistance of the coating of the cutting tool. The coating can comprise further layers to for example improve the adhesion of layers and/or improve the visual appearance of the coated cutting tool. Such additional layers can for example be TiN, TiCN, TiAlN, TiCO, TiCNO, AlTiCNO, AlTiCO etc.
The intermediate layer of TiCN is relatively thin, only 0.05-1 μm. The aim of this TiCN layer is to provide a good adhesion and a suitable starting layer for the subsequent wear resistant α-Al2O3 layer. In one embodiment of the present invention the thickness of the intermediate layer of TiCN is 0.05-0.3 μm. The TiCN layer is typically very thin in relation to the α-Al2O3 layer and/or to the T1-xAlxN layer.
In one embodiment of the present invention the TC(111) of the intermediate layer of TiCN is >3, wherein the texture coefficient TC (111) is defined as follows,
wherein I(hkl) are the intensities of the diffraction reflections measured by X-ray diffraction, I0(hkl) are the standard intensities of the diffraction reflections according to the pdf card 00-042-1489, n is the number of reflections used in the calculation, and for the calculation of TC(111) the reflections (111), (200), (220) and (311) are used.
The intermediate TiCN layer is preferably in epitaxial relation to the T1-xAlxN layer, i.e. crystal grains continue to grow with the same orientation through these layers instead of renucleations at the interface. This is preferred both due to a high adhesion but also since a high degree of orientation can be perceived. A high degree of orientation, i.e. high TC values, are advantageous in that it provides high wear resistance.
In one embodiment of the present invention the Σ3 grain boundary length to the total grain boundary length in the α-Al2O3 layer is >30%. The grain boundary length is measured with EBSD on a polished surface of the α-Al2O3 layer. The polished surface is parallel to the surface of the substrate. The Σ3 grain boundaries are considered to contribute to high wear resistance of the α-Al2O3 layer. In one embodiment the EBSD measurement is performed at a remaining layer thickness of 30% to 70% of the thickness of the α-Al2O3 layer, preferably in about the middle of the α-Al2O3 layer thickness.
In one embodiment of the present invention the T1-xAlxN layer has at least 90 vol-%, preferably at least 95 vol-%, particularly preferably about 98 vol-% face-centered cubic (fcc) crystal structure.
In one embodiment of the present invention the T1-xAlxN layer has a columnar microstructure.
In one embodiment of the present invention precipitations of Ti1-yAlyN are present at grain boundaries of the T1-xAlxN crystallites, said precipitations having a higher Al content than the inside crystallites and comprise AlN with hexagonal crystal structure (hcp) wherein y>x.
In one embodiment of the present invention the T1-xAlxN layer has stoichiometric coefficients of 0.60≤x≤0.90.
In one embodiment of the present invention the T1-xAlxN layer has a preferred orientation of the crystal growth with respect to the crystallographic {111} plane, characterized by a texture coefficient TC (111)>3, preferably >3.5, wherein the texture coefficient TC (111) is defined as follows:
wherein
In one embodiment of the present invention the thickness of the TiCN layer is 0.1-0.3 μm, preferably 0.1-0.2 μm.
In one embodiment of the present invention the average aspect ratio of the TiCN grains of the TiCN layer is, wherein the aspect ratio is defined as the height (i.e. layer thickness) to the width ratio.
In one embodiment of the present invention the thickness of the T1-xAlxN layer, t(Ti1-x AlxN), in relation to the thickness of the α-Al2O3 layer, t(α), is t(T1-xAlxN):t(α) from 2:1 to 3:1. These thickness relations have shown advantageous in increased wear resistance.
In one embodiment of the present invention the coating comprises an innermost layer of TiN, preferably with a thickness of 0.1-2 μm, preferably 0.2-1 μm or 0.2-0.5 μm. This innermost layer is deposited directly on the substrate. This innermost layer is preferably in direct contact with the T1-xAlxN layer.
In one embodiment of the present invention the coating comprises an intermediate layer of TiN between the T1-xAlxN and the TiCN. The thickness of this intermediate TiN layer is preferably 0.05-0.1 μm. This intermediate TiN layer is preferably in direct contact with the Ti1-xAlxN layer. This intermediate TiN layer is preferably in direct contact with the TiCN layer.
The substrate can be made of cemented carbide, cermet, steel, ceramic, cubic boron nitride or high-speed steel. In one embodiment of the present invention the substrate is of cemented carbide. The cemented carbide preferably has a binder phase content of 4-9 wt %. The cemented carbide preferably comprises 80-90 wt % WC. The cemented carbide preferably comprises Co in the binder phase.
In the present examples substrates of cemented carbide with the cutting inserts geometry CNMA120408 were used. The cemented carbide composition was 86.1 wt % WC, 5.5 wt % Co, 8.0 wt % (NbC, TaC and TiC) and 0.4 wt % other carbides. The substrates have a binder phase enriched surface zone of about 20 μm.
The substrates were CVD coated in a CVD coating chamber of type Bernex BPX325S with a reactor height of 1250 mm, a reactor diameter of 325 mm and a volume of charge of 40 litres.
The example coatings according to the invention and the reference have been obtained using the herein described equipment and the process conditions as given in the following tables 1a, 1b, 2a and 2b. However, it is well known in the art that the process conditions to produce CVD coatings may to a certain degree vary depending on the equipment used. It is therefore within the purview of the person skilled in the art to modify the deposition conditions and/or the equipment used to achieve the coating properties of the present invention.
The substrates were deposited with a coating of the following layers starting from the surface of the substrate: 0.25 μm TiN, 9.0 μm T1-xAlxN, 0.075 μm TiN, 0.3 μm TiCN, 3.2 μm α-Al2O3. The deposition conditions are shown in Table 1a1 and 1b1.
The basic TiN layer was deposited at a temperature of 850° C. on the substrate. The reaction gases comprise TiCl4, N2, H2.
The T1-xAlxN layer was deposited at a temperature of 725° C. The reaction gases comprise TiCl4, AlCl3, NH3, H2.
The intermediated TiN layer is then deposited directly on top of the T1-xAlxN layer at a temperature of 725° C. The reaction gases comprise TiCl4, NH3, H2.
The TiCN layer is then deposited directly on top of the intermediate TiN layer at a temperature of 850° C. The reaction gases comprise TiCl4, CH3CN, N2, H2.
As a bonding layer the TiCN layer was oxidized in an oxidation step using CO, CO2 and H2.
The α-Al2O3 layer is then deposited on top of the bonding layer at a temperature of 850° C. The reaction gases comprise AlCl3, CO2, H2, HCl, H2S, CO. The deposition of the α-Al2O3 layer was carried out in two deposition steps, wherein in the first step a nucleation layer is grown, and in the second step the α-Al2O3 layer is grown to the desired thickness.
The substrates were deposited with a coating of the following layers starting from the surface of the substrate: 0.5 μm TiN, 4.7 μm T1-xAlxN, 0.25 μm TiN, 0.6 μm TiCN, 3.0 μm α-Al2O3. The deposition conditions are shown in Table 1a2 and 1b2.
The basic TiN layer was deposited at a temperature of 850° C. on the substrate. The reaction gases comprise TiCl4, N2, H2.
The T1-xAlxN layer was deposited at a temperature of 700° C. The reaction gases comprise TiCl4, AlCl3, NH3, H2.
The intermediated TiN layer is then deposited directly on top of the T1-xAlxN layer at a temperature of 700° C. The reaction gases comprise TiCl4, NH3, H2.
The TiCN layer is then deposited directly on top of the intermediate TiN layer at a temperature of 850° C. The reaction gases comprise TiCl4, CH3CN, N2, H2.
As a bonding layer the TiCN layer was oxidized in an oxidation step using CO, CO2 and H2.
The α-Al2O3 layer is then deposited on top of the bonding layer at a temperature of 850° C. The reaction gases comprise AlCl3, CO2, H2, HCl, H2S, CO. The deposition of the α-Al2O3 layer was carried out in two deposition steps, wherein in the first step a nucleation layer is grown, and in the second step the α-Al2O3 layer is grown to the desired thickness.
Cemented carbide substrates were deposited with coating of the following layers starting from the surface of the substrate: 0.4 μm TiN, 7.8 μm TiCN, 1.3 μm TiAlCNO, 3.4 μm α-Al2O3. Both the deposition of the TiCN and the α-Al2O3 layer was carried out in two deposition steps, wherein in the first step a nucleation layer is grown, and in the second step the layer is grown to the desired thickness. The deposition conditions are shown in Table 2a1 and 2b1.
Cemented carbide substrates were deposited with coating of the following layers starting from the surface of the substrate: 0.3 μm TiN, 4.6 μm TiCN, <0.1 μm TiAlCNO, 2.4 μm α-Al2O3. The deposition conditions are shown in Table 2a2 and 2b2.
Cross-section SEM microphotographs were prepared from the coatings and cross sections of Sample A1 are shown in
The coatings were analyzed in X-ray diffraction measurements.
X-ray diffraction measurements were performed in a XRD3003 PTS diffractometer of GE Sensing and Inspection Technologies using CuKα-radiation. The X-ray tube was run in point focus at 40 kV and 40 mA. A parallel beam optic using a polycapillary collimating lens with a measuring aperture of fixed size was used on the primary side whereby the irradiated area of the sample was defined in such manner that a spill over of the X-ray beam over the coated face of the sample was avoided. On the secondary side a Soller slit with a divergence of 0.4° and a 25 μm thick Ni Kβ filter was used. Thin film correction and absorption correction were made and the linear absorption coefficient used was μα-Al2O3=0.01258 μm−1 and μTiCN=0.08048 μm−1 and μTiAlN=0.02979 μm−1. Absorption of the overlaying layers was considered and corrected for.
Furthermore, texture and grain boundary orientation of the coatings were analyzed by electron backscatter diffraction (EBSD). For this purpose the coating surfaces (samples) were first polished subsequently using slurries of diamond having average grain sizes of 6 μm, 3 μm and 1 μm, respectively. Then, the samples were polished using colloidal silica having an average grain size of 0.04 μm. The last polishing step was done manually, and polishing time was increased stepwise until the sample quality was good enough to perform the EBSD maps, i.e. indexing of EBSD patterns would be accomplished with an average confidence index (CI)>0.2 at typical scan rates of 15-35 frames per second. The precise preparation conditions will depend on the individual sample and equipment, and can easily be determined by a person skilled in the art. Care was taken to ensure that the polished surfaces were smooth and parallel to the original coating surface. Finally, the samples were ultrasonically cleaned before EBSD examination.
Planar surfaces on the rake face were used for the polishing, and the EBSD measurements were performed at distances <250 μm from the cutting edge of the insert. Due to the roughness of the cemented carbide substrate, areas of the lower TiCN or T1-xAlxN layers of the coatings according to the examples above were exposed as well. EBSD maps were acquired with an EDAX system (Digiview IV camera) using 8×8 or lower binning and typical scan rates of 15-35 frames per second on a Zeiss Supra 40 VP field emission scanning electron microscope using a 60 μm aperture, 15 kV acceleration voltage, high current mode and working distances between 6 mm and 15 mm. Areas for EBSD measurement of the upper α-Al2O3 layers, TiCN layers or T1-xAlxN layers were chosen by inspection of the surface in the SEM according to atomic number contrast. The maps had sizes of at least 10×10 μm, and step size ≤0.04 μm. Measurement of the upper α-Al2O3 layers was thus performed at a remaining layer thickness of 30% to 70% of the grown thickness. This was checked after polishing and EBSD measurement by preparing a cross section through the area where EBSD map had been acquired using a focused ion beam (FIB), and taking an average of >5 thickness measurements evenly distributed over the width of the EBSD map. The information depth of the electron diffraction patterns is small (on the order of a few tens of nanometers) compared to the layer thicknesses. The measurement depth of the TiCN layers in samples B1 and B2 was 0.5-1 μm below the interface between TiCN and α-Al2O3. For sample A2, EBSD maps of the 0.6 μm thick TiCN layer could be acquired and processed. The texture information thus obtained represents an approximate average over the TiCN layer thickness. Since the texture of the TiCN layer in sample A2 is given by epitaxy to the underlying T1-xAlxN layer, there is no significant texture gradient in the TiCN layer. The texture and epitaxial relations were checked by EBDS analysis in cross section. For sample A1, no EBSD map of the TiCN layer could be acquired due to too low thickness. Also in this case, texture and grain boundary orientation of the TiCN layer are defined by the underlying T1-xAlxN layer, as indicated by EBSD cross sectional analysis and by the XRD results given in table 3-1.
For data acquisition and analysis, the software packages OIM Data Collection 7.3.1 and OIM Analysis 7.3.1 from EDAX were used, respectively. From the data orientation distribution functions were calculated and plotted as 001 inverse pole figures to evaluate the preferential crystallographic orientation. The α-Al2O3 layers of samples A1, A2 and B2 had strong {0001} fiber textures, whereas sample B1 had a weak bimodal texture showing intensity maxima around {0001} and {01-12} in the inverse pole figure. TiCN layers of the coatings according to the invention had strong {111} texture, whereas TiCN-layers of the comparative samples had {211} texture. The strength and sharpness of the fiber texture is characterized by the maximum intensity in the 001 inverse pole figure appearing at the direction of preferential crystallographic orientation.
For the evaluation of grain boundary orientation, ΣN grain boundaries were identified. The Brandon criterion (ΔΘ<Θ0 (Σ)−0.5, where Θ0=15°) was used to account for the allowed deviations ΔΘ of experimental values from the theoretical values (D. Brandon, Acta metall. 14 (1966) 1479-1484.). The amount of Σ3 grain boundaries in the layers was calculated as fraction of Σ3/ΣN (N≤9) for α-Al2O3 layers. The ΣN (N≤49) boundaries used in the calculation for α-Al2O3 correspond to the common lattice rotations in rhombohedral lattice materials given in H. Grimmer, Acta Crystallographica A (1989), A45, 505-523. In addition, the amount of Σ3 grain boundaries was calculated as the fraction of Σ3 grain boundary length to the total grain boundary length.
For the present invention and the definitions herein, the ODF calculation and texture calculation, as well as Σ-values for the calculation of Σ-type grain boundaries are based on EBSD data without noise reduction or other cleanup procedures which alter the indexing and orientation data. Care should be taken that specimen preparation is carried out as described here with sufficient smoothness.
The results of EBSD measurements are given in table 4. It is notable that in the coatings according to the invention, the α-Al2O3 layers have a much higher fraction of Σ3 grain boundaries with respect to the total grain boundary length.
Cemented carbide inserts of the geometry CNMA120408 were coated as disclosed above. The inserts were tested in a turning test against 56NiCrMo steel without coolant. The following cutting parameters were used:
Cutting speed, vc: 150 m/min
Feed, f: 0.32 mm
Depth of cut, ap: 2.5 mm
The samples A1 and B1 were tested in longitudinal turning. One and the same cutting edge was run for 3 minutes, removed and analyzed in a LOM, remounted and run again for 3 minutes. This was repeated 4 times such that a total cutting time of 12 minutes was reached. The flank wear of the cutting edges (VBmax) as an average of two repeats are shown in table 5.
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 |
|---|---|---|---|
| 17153338.3 | Jan 2017 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2018/051950 | 1/26/2018 | WO | 00 |
