Patent Grant
8507082
The present invention relates to cutting tools having coatings applied by chemical vapor deposition (CVD) and, in particular, to CVD coated polycrystalline cubic boron nitride (PcBN) cutting tools.
Cutting tools have been used in both coated and uncoated conditions for machining various metals and alloys. In order to increase cutting tool wear resistance and lifetime, one or more layers of refractory materials have been applied to cutting tool surfaces. TiC, TiCN, TiOCN, TiN and Al2O3, for example, have been applied to cemented carbide substrates by CVD.
Al2O3 or alumina has been of particular interest as a coating for cutting tools. Alumina demonstrates various crystalline phases including α, κ, γ, β AND θ with the α and κ phases occurring most frequently on CVD coated cemented carbide cutting tools. α-alumina has proven to be a desirable coating given its thermodynamic stability and general chemical inertness at various temperatures encountered in cutting applications. However, deposition of α-alumina is increasingly difficult and often sensitive to deposition conditions and the chemical identity of the cutting tool substrate. Prior literature, for example, has demonstrated the requirement to sufficiently oxidize titanium carbide surfaces prior to alumina deposition in order to induce formation of the α-phase. Insufficient oxidation of TiC surfaces results in the production of κ-alumina or a mixture of κ and α phases (see e.g., Vourinen, S., Thin Solid Films, 193/194 (1990) 536-546 and Layyous et al., Surface and Coatings Technology, 56 (1992) 89-95).
Moreover, α-alumina coatings on cemented carbide substrates have displayed significant adhesion problems leading to premature coating failure by delamination and other degradative pathways. Adhesion problems in α-alumina coatings on cemented carbides has been attributed to significant interfacial porosity developed between the coating and substrate during α-alumina deposition (see e.g., Chatfield et al., Journal de Physique, Colioque C5, supplement au n° 5, Tome 50, mai 1989).
In view of these findings, α-alumina bonding layers have been extensively researched and developed. The bonding layers are provided on surfaces of cemented carbide substrates to ensure the nucleation and growth of α-alumina and to mitigate or eliminate the development of interfacial porosity (see e.g., Halvarsson et al., Surface and Coatings Technology, 68/69 (1994) 266-273 and Halvarsson et al., Surface and Coatings
Technology 76/77 (1995) 287-296).
Cutting tools based on polycrystalline cubic boron nitride (PcBN) are becoming more popular given the high hardness and high thermal stability (up to about 980° C.) of cBN. PcBN cutting tools, for example, find application in machining case-hardened and through-hardened steels, superalloys, chilled cast iron and gray cast iron. Additionally, PcBN based cutting tools are operable to run dry for clean machining processes thereby saving coolant, maintenance and disposal costs.
Similar to cemented carbides, cutting tools based on PcBN substrates can also benefit from the application of various refractory coatings. PcBN cutting tool substrates, for example, have been provided with TiCN, TiOCN, TiN and Al2O3 coatings. Nevertheless, as with cemented carbides, the deposition of α-alumina on PcBN cutting tool substrates occurs through the use of one or more intervening layers over the substrate, including bonding or modification layers. U.S. Pat. No. 7,455,918 to Gates et al. discloses PcBN cutting tools wherein α-alumina is deposited on modification layers residing between the PcBN substrate and the α-alumina layer.
In view of the foregoing, the present invention, in one aspect, provides coated cutting tools comprising a PcBN substrate wherein a layer of single phase α-alumina is deposited by chemical vapor deposition directly on one or more surfaces of the substrate. In some embodiments, a coated cutting tool described herein comprises a substrate comprising greater than 80 weight percent PcBN and a coating adhered to the substrate, the coating comprising a layer of single phase α-Al2O3 deposited by chemical vapor deposition directly on a surface of the substrate. In some embodiments, the layer of single phase α-Al2O3 deposited directly on a surface of the substrate comprising greater than 80 weight percent PcBN has a critical load (Lc) of greater than 70 N.
Moreover, in some embodiments, a coating of a cutting tool described herein further comprises one or more layers of MOxOnNz deposited over the single phase α-Al2O3 layer, wherein M is a metal selected from the group consisting of metallic elements of Groups IVB, VB and VIB of the Periodic Table and x+y+z=1. In some embodiments, one or more layers of MCxOyNz are deposited over the single phase α-Al2O3 layer by CVD or physical vapor deposition (PVD).
In another aspect, methods of producing coated cutting tools are described herein. In some embodiments, a method of producing a coated cutting tool comprises providing a cutting tool substrate comprising greater than 80 weight percent PcBN and depositing directly on a surface of the substrate by chemical vapor deposition a layer of single phase α-Al2O3. In some embodiments, a method of producing a coated cutting tool further comprises depositing a one or more layers of MOxOnNz over the single phase α-Al2O3 layer, wherein M is a metal selected from the group consisting of metallic elements of Groups IVB, VB and VIB of the Periodic Table and x+y+z=1. In some embodiments, one or more layers of MOxCyNz are deposited by CVD or PVD.
In another aspect, methods of cutting metal are described herein. In some embodiments, a method of cutting metal comprises providing a metal work piece and cutting the metal work piece with a coated cutting tool, the coated cutting tool comprising a substrate comprising greater than 80 weight percent PcBN and a coating adhered to the substrate, the coating comprising a layer of single phase α-Al2O3 deposited by chemical vapor deposition directly on a surface of the substrate. In some embodiments, the coating of the cutting tool further comprises one or more layers of MOxCyNz deposited over the single phase α-Al2O3 layer as described herein.
These and other embodiments are described in greater detail in the detailed description which follows.
Embodiments described herein can be understood more readily by reference to the following detailed description and examples and their previous and following descriptions. Elements, apparatus and methods described herein, however, are not limited to the specific embodiments presented in the detailed description and examples. It should be recognized that these embodiments are merely illustrative of the principles of the present invention. Numerous modifications and adaptations will be readily apparent to those of skill in the art without departing from the spirit and scope of the invention.
In one aspect, the present invention provides coated cutting tools comprising a PcBN substrate wherein a layer of single phase α-alumina is deposited by chemical vapor deposition directly on one or more surfaces of the substrate. In some embodiments, a coated cutting tool described herein comprises a substrate comprising greater than 80 weight percent PcBN and a coating adhered to the substrate, the coating comprising a layer of single phase α-Al2O3 deposited by chemical vapor deposition directly on a surface of the substrate.
Turning now to components of a coated cutting tool described herein, a coated cutting tool described herein comprises a PcBN substrate. PcBN substrates of coated cutting tools described herein comprise greater than 80 weight percent PcBN. In some embodiments, for example, a substrate of a coated cutting tool comprises at least about 85 weight percent PcBN. A substrate of a coated cutting tool, in some embodiments, comprises at least about 90 weight percent PcBN. In some embodiments, a substrate comprises at least about 95 weight percent PcBN.
In some embodiments, a substrate of a coated cutting tool described herein comprises PcBN in an amount ranging from greater than 80 weight percent to about 97 weight percent. A substrate, in some embodiments, comprises PcBN in an amount ranging from about 85 weight percent to about 95 weight percent.
In some embodiments, a substrate comprises a ceramic or metallic binder in addition to the PcBN. Suitable ceramic binders for use in a substrate of a coated cutting tool described herein, in some embodiments, comprise nitrides, carbonitrides, carbides and/or borides of titanium, tungsten, cobalt or aluminum. In some embodiments, for example, a substrate comprises a binder of AlN, AlB2 or mixtures thereof. In some embodiments, a suitable metallic binder for PcBN substrates comprises cobalt. Moreover, in some embodiments, a substrate can comprise solid solutions of any of the foregoing ceramic or metallic binders.
Compositional determination of a PcBN substrate described herein can be conducted by X-ray diffraction (XRD). The cutting tool substrate rake face or flank face can be analyzed depending on cutting tool geometry. For compositional phase analysis of a PcBN substrate described herein, both a PANalytical Xpert MRD diffraction system fitted with a Eulerean cradle and microfocus optics for PcBN compacts and tips, or a PANalytical Xpert MPD fitted with programmable optics for analysis of a monolithic solid piece of PcBN can be used.
Both x-ray diffraction systems are configured with focusing beam optics and fitted with a copper x-ray tube and operating parameters of 45 KV and 40 MA. For analysis of the monolithic solid piece, the PANalytical MRD is fitted with programmable divergence slit and programmable antiscatter slit. The x-ray beam width is controlled by an appropriate mask size and x-ray beam length is fixed at 2 mm using the programmable optics. The PANalytical MPD is fitted with a linear strip solid state x-ray detector and nickel beta filter.
The PANalytical Xpert MRD system is configured with a microfocus monocapillary optics of either 100μ or 500μ focal spot depending on size of PcBN compact. The PANalytical MRD is fitted with a linear strip solid state x-ray detector and nickel beta filter.
Analysis scan range, counting times, and scan rate are selected to provide optimal data for Rietveld analysis. A background profile is fitted and peak search is performed on the PcBN substrate diffraction data to identify all peak positions and peak intensities. The peak position and intensity data is used to identify the crystal phase composition of the PcBN substrate using any of the commercially available crystal phase databases.
Crystal structure data is input for each of the crystalline phases present in the substrate. Typical Rietveld refinement parameters settings are:
Any additional parameter to achieve an acceptable goodness of fit
PcBN substrates having compositional parameters described herein can be provided in various constructions. In some embodiments, for example, a coated cutting tool comprises a monolithic solid piece PcBN substrate. In some embodiments, a PcBN substrate is provided as a compact or insert attached to a support by brazing or other joining technique. In some embodiments, a PcBN substrate is a full top cutting insert on a support.
As described herein, a coating adhered to the PcBN substrate comprises a layer of single phase α-Al2O3 deposited by chemical vapor deposition directly on the surface of the PcBN substrate. In being deposited directly on one or more surfaces of the PcBN substrate, the layer of single phase α-Al2O3 does not reside on a modification layer, bonding layer or any other intervening layer.
In some embodiments, the layer of single phase α-Al2O3 has a thickness of at least about 2 μm. In some embodiments, the layer of single phase α-Al2O3 has a thickness of at least about 5 μm. The layer of single phase α-Al2O3, in some embodiments, has a thickness of at least about 10 μm or at least about 15 μm.
In some embodiments, a layer of single phase α-Al2O3 deposited directly on a surface of the PcBN substrate has a thickness ranging from about 2 μm to about 20 μm. In some embodiments, the layer of single phase α-Al2O3 has a thickness ranging from about 5 μm to about 15 μm. The layer of single phase α-Al2O3, in some embodiments, has a thickness ranging from about 3 μm to about 10 μm.
In some embodiments, the layer of single phase α-Al2O3 has an average grain size ranging from about 0.2 μm to about 5 μm. In some embodiments, the layer of single phase α-Al2O3 has an average grain size ranging from about 0.5 μm to about 2 μm. In some embodiments, the layer of single phase α-Al2O3 has an average grain size ranging from about 1 μm to about 3 μm. Grain size of a single phase α-Al2O3 layer described herein can be determined by taking a top down SEM image of the α-Al2O3 layer at a magnification of 5000×. A line is drawn on the SEM image in a random direction, and the grain size is calculated by the following formula:
Grain size=L/(N−1)
wherein L is the length of the line, and N is the number of grain boundaries intersected by the line. The foregoing measurement is repeated for five (5) SEM images of the α-Al2O3 layer, and the resulting grain size values are averaged to provide the average grain size.
In some embodiments, grains of the single phase α-Al2O3 layer display a columnar structure. Moreover, in some embodiments, grains at the surface of the single phase α-Al2O3 layer display a polyhedral morphology.
In some embodiments, grains at the surface of the single phase α-Al2O3 layer display a shape having an aspect ratio of at least 2 in a plane parallel to the surface of the α-Al2O3 layer. Aspect ratio, as used herein, refers to the length of the grain in a plane parallel to the surface of the α-Al2O3 layer divided by the width of the grain in a plane parallel to the surface of the α-Al2O3 layer. In some embodiments, grains at the surface of the α-Al2O3 layer have an aspect ratio of at least 5 or at least 10. In some embodiments, grains at the surface of the α-Al2O3 layer have an aspect ratio ranging from about 2 to about 20 or from about 5 to about 15. In some embodiments, grains at the surface of the α-Al2O3 layer have an aspect ratio ranging from about 2 to about 10.
In some embodiments, grain morphology at a surface of the single phase α-Al2O3 layer can be determined by taking a top down SEM of the surface at a magnification of 5000×.
In some embodiments, a coating of a cutting tool described herein further comprises one or more layers of MOxOnNz deposited over the single phase α-Al2O3 layer, wherein M is a metal selected from the group consisting of metallic elements of Groups IVB, VB and VIB of the Periodic Table and x+y+z=1. In some embodiments, M is selected from the group consisting of Ti, Zr and Hf. In some embodiments, for example, a layer of TiN is deposited over the single phase α-Al2O3 layer. In some embodiments, a layer of TiCN or TiOCN is deposited over the single phase α-Al2O3 layer. In some embodiments, one or more layers of MOxCyNz are deposited over the single phase α-Al2O3 layer by CVD or physical vapor deposition (PVD).
In some embodiments, one or more layers of MOxOnNz can have any thickness not inconsistent with the objectives of the present invention. In some embodiments, a layer of MOxCyNz has a thickness of at least about 0.5 μm. In some embodiments, a layer of MOxCyNz has a thickness ranging from about 0.5 μm to about 5 μm or from about 1 μm to about 3 μm.
In some embodiments wherein one or more layers of MOxOnNz are deposited over the single phase α-Al2O3 layer, the MOxCyNz layer(s) can be etched away to expose a surface of the single phase α-Al2O3 layer for SEM analysis of grain morphology.
A coating comprising a single phase α-Al2O3 layer in direct contact with a PcBN cutting tool substrate described herein and an optional MOxCyNz layer deposited over the α-Al2O3 layer, in some embodiments, demonstrates a critical load (Lc) greater than 60 N or greater than 65 N. In some embodiments, the coating has a critical load (Lc) greater than 70 N. Lc values for coatings recited herein were determined according to ASTM C1624-05—Standard Test for Adhesion Strength by Quantitative Single Point Scratch Testing wherein a progressive loading rate of 10 N/mm was used.
In some embodiments, a coating comprising a single phase α-Al2O3 layer in direct contact with a PcBN cutting tool substrate described herein and an optional MOxCyNz layer deposited over the α-Al2O3 layer has modulus (E) of at least about 390 GPa. In some embodiments, the coating has a modulus of at least about 400 GPa. In some embodiments, the coating has a modulus ranging from about 380 GPa to about 420 GPa.
In some embodiments, a coating comprising a single phase α-Al2O3 layer in direct contact with a PcBN cutting tool substrate described herein and an optional MOxCyNz layer deposited over the α-Al2O3 layer has a nanohardness of at least about 20 GPa. In some embodiments, the coating has a nanohardness of at least about 24 GPa. The coating, in some embodiments, has a nanohardness ranging from about 15 GPa to about 30 GPa or from about 20 GPa to about 25 GPa.
Coating modulus and nanohardness values recited herein were determined from nano-indentation testing conducted with a Fischerscope HM2000 in accordance with ISO standard 14577 using a Vickers indenter. Indentation depth was set to 0.25 μm.
In another aspect, methods of producing coated cutting tools are described herein. In some embodiments, a method of producing a coated cutting tool comprises providing a cutting tool substrate comprising greater than 80 weight percent PcBN and depositing directly on a surface of the substrate by chemical vapor deposition a layer of single phase α-Al2O3. In some embodiments, a method of producing a coated cutting tool further comprises depositing a one or more layers of MOxCyNz over the single phase α-Al2O3 layer, wherein M is a metal selected from the group consisting of metallic elements of Groups IVB, VB and VIB of the Periodic Table and x+y+z=1. In some embodiments, one or more layers of MOxCyNz are deposited by CVD or PVD.
In some embodiments of methods described herein, a cutting tool substrate can comprise any PcBN content recited herein for the substrate. Moreover, in some embodiments of methods described herein, the single phase α-Al2O3 layer can comprise any of the compositional, chemical and/or physical properties recited hereinabove for a single phase α-Al2O3 layer. Additionally, in some embodiments, one or more layers of MOxCyNz can comprise any of the compositional, chemical and/or physical properties recited hereinabove for a MOxCyNz layer.
In some embodiments, depositing a layer of single phase α-Al2O3 directly on a surface of the PcBN substrate comprises varying the rate at which the α-Al2O3 is deposited. In some embodiments, varying the rate at which the α-Al2O3 is deposited comprises transitioning from a lower rate of α-Al2O3 deposition to a higher rate of α-Al2O3 deposition. In some embodiments, a higher rate of α-Al2O3 deposition is 1.5× greater than a lower rate of α-Al2O3 deposition. In some embodiments, varying the rate at which the α-Al2O3 is deposited comprises transitioning from a higher rate of α-Al2O3 deposition to a lower rate of α-Al2O3 deposition.
In some embodiments, depositing a layer of single phase α-Al2O3 directly on a surface of the PcBN substrate comprises varying the deposition temperature of the α-Al2O3. Varying the deposition temperature, in some embodiments comprises transitioning from a higher α-Al2O3 deposition temperature to a lower α-Al2O3 deposition temperature. In some embodiments, the difference between the higher α-Al2O3 deposition temperature and the lower α-Al2O3 deposition temperature is at least 50° C. In some embodiments, the difference between the higher α-Al2O3 deposition temperature and the lower α-Al2O3 deposition temperature is at least 130° C. In some embodiments, the difference between the higher α-Al2O3 deposition temperature and the lower α-Al2O3 deposition temperature ranges from about 50° C. to about 150° C. In some embodiments, the difference between the higher α-Al2O3 deposition temperature and the lower α-Al2O3 deposition temperature ranges from about 50° C. to about 130° C. In some embodiments, transitioning from a higher α-Al2O3 deposition temperature to a lower α-Al2O3 deposition temperature comprises transitioning from high temperature (HT) α-Al2O3 deposition to medium temperature (MT) α-Al2O3 deposition.
Alternatively, in some embodiments, varying the deposition temperature comprises transitioning from a lower deposition temperature to a higher deposition temperature.
In some depositing a layer of single phase α-Al2O3 directly on a surface of the PcBN substrate comprises varying the deposition rate and deposition temperature of the α-Al2O3 as described hereinabove.
In another aspect, methods of cutting metal are described herein. In some embodiments, a method of cutting metal comprises providing a metal work piece and cutting the metal work piece with a coated cutting tool, the coated cutting tool comprising a substrate comprising greater than 80 weight percent PcBN and a coating adhered to the substrate, the coating comprising a layer of single phase α-Al2O3 deposited by chemical vapor deposition directly on a surface of the substrate. In some embodiments, the coating of the coated cutting tool further comprises one or more layers of MOxCyNz deposited over the single phase α-Al2O3 layer as described herein.
In some embodiments, metal cutting with a coated cutting tool described herein is conducted dry, in the absence of any liquids and/or lubricants. In some embodiments, a metal work piece is selected from the group consisting of gray cast iron, case-hardened and through-hardened steels, superalloys and chilled cast iron.
These and other embodiments are further illustrated by the following non-limiting examples.
A coated cutting tool described herein was produced by placing a monolithic solid piece substrate (ANSI Catalog No. SNM433S0820) comprising PcBN in an amount of 90 weight percent with the balance AlN/AlB2 binder in a CVD apparatus having an axial feed configuration. A layer of single phase α-Al2O3 was deposited directly on a surface of the PcBN substrate according to the process parameters provided in Table I.
The deposited single phase α-Al2O3 layer had a thickness of 7.2 μM. A TiN top layer of 1.5 μm was subsequently deposited over the single phase α-Al2O3 layer by standard CVD techniques.
Moreover,
A coated cutting tool described herein was produced by placing a monolithic solid piece substrate (ANSI Catalog No. SNM433S0820) comprising PcBN in an amount of 90 weight percent with the balance AlN/AlB2 binder in a CVD apparatus having an axial feed configuration. A layer of single phase α-Al2O3 was deposited directly on a surface of the PcBN substrate according to the process parameters provided in Table II.
The deposited single phase α-Al2O3 layer had a thickness of 9.9 μm. A TiN top layer of 0.6 μm was subsequently deposited over the single phase α-Al2O3 layer by standard CVD techniques.
Moreover,
Coated cutting tools described herein were subjected to cutting lifetime testing in comparison with prior art coated cutting tools. Non-limiting embodiments of coated cutting tools of the present invention A, B and C were produced in accordance with Example 1 above. Non-limiting embodiments of coated cutting tools of the present invention D and E were prepared in accordance with Example 2 above. Compositional parameters of coated cutting tools A-E and coated cutting tools of the prior art F, G and H are provided in Table III.
Coated cutting tools A and F were subjected to cutting lifetime testing as follows:
As provided in Table IV, cutting tools having an architecture described herein (A-E) demonstrated significant increases in lifetime at all cutting speeds in comparison with the prior art coated cutting tools (F-H). Coated cutting tool E of the present invention, for example, displayed a 177% increase in cutting lifetime at a cutting speed of 3500 sfm in comparison with prior art cutting tool H.
Various embodiments of the invention have been described in fulfillment of the various objects of the invention. It should be recognized that these embodiments are merely illustrative of the principles of the present invention. Numerous modifications and adaptations thereof will be readily apparent to those skilled in the art without departing from the spirit and scope of the invention.
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