Oxide coated cutting tool

Abstract: The present invention provides a body coated with refrac tory single- or multilayers one of which consists of single-phase κ-Al 2 O 3 characterized by controlled microstructure with crystal planes preferably grown in the (210)-direction with respect to the surface of the coated body. The coated tool according to the invention exhibits increased wear properties when machining ball bearing steel.

Description: The present invention relates to an oxide coated cutting tool for chipforming machining. Chemical vapour deposition of alumina on cutting tools is a well established technology. The wear properties of Al 2 O 3 as well as of other refractory materials have been discussed extensively in the literature. The CVD-technique has also been used to produce coatings of other metal oxides, carbides and nitrides, the metal being selected from transition metals of the IVB, VB and VIB groups of the Periodic Table of the Elements. Many of these compounds have found practical applications as wear resistant or protective coatings, but few have received as much attention as TiC, TiN and Al 2 O 3 . Al 2 O 3 crystallizes in several different phases: α, κ, γ, β,  etc. The two most frequently occurring phases in CVD of wear resistant Al 2 O 3 -coatings are the thermodynamically stable, hexagonal α-phase and the metastable κ-phase. Generally, the κ-phase is fine-grained with a grain size in the range 0.5-3.5 µm often exhibiting a columnar coating morphology. Furthermore, κ-Al 2 O 3 coatings are free from crystallographic defects and free from micropores or voids. The crystallographic structure of κ-Al 2 O 3 is basically orthorhombic and the unit cell can be expressed with orthogonal indices which might be transformed to a hexagonal unit cell with hexagonal indices. The α-Al 2 O 3 grains in mixed α+κ-Al 2 O 3 coatings are usually coarser with a grain size of 1-6 µm depending upon the deposition conditions. Porosity and crystallographic defects are in this case frequently occurring. On commercial cutting tools, Al 2 O 3 is always applied on TiC x N y O z coated carbide or ceramic substrates (see, e.g. U.S. Pat. No. 3,837,896, now Reissue U.S. Pat. No. 29,420 and U.S Pat. No. 5,071,696) and the interfacial chemical reactions between the TiCxNyOz-surface and the alumina coating are of particular importance. The practice of coating cemented carbide cutting tools with oxides to further increase their wear resistance is in itself well known as is evidenced in e.g. U.S. Pat. Reissue No. 29,420 and U.S. Pat. Nos. 4,399,168, 4,018,631, 4,490,191 and 4,463,033. These patents disclose oxide coated bodies and how different pretreatments e.g. of TiC-coated cemented carbide, enhance the adherence of the subsequently deposited oxide layer. Alumina coated bodies are further disclosed in U.S. Pat. No. 3,736,107, 5,071,696 and 5,137,774 wherein the Al 2 O 3 -layers comprise α, κ resp α+κ-combinations. Smith US 4,619,866 describes a method for producing fast growing Al 2 O 3 -layers by utilizing a hydrolysis reaction of a metal halide under the influence of a dopant e.g. hydrogen sulphide (H 2 S). The resulting coating consists of a mixture of the smaller κ-grains and the larger α-grains. The process yields coatings with an even layer thickness distribution around the coated body. U.S. Pat No 5,071,696 discloses a body coated with single-phase κ-Al 2 O 3 deposited epitaxially onto an MX-layer where MX is a carbide, carbonitride or oxycarbonitride of a metal from the groups IVB, VB or VIB of the periodic table. EP-A-523021 discloses a method of growing a fine-grained κ-alumina coating. Single-phase α-Al 2 O 3 -layer with preferred crystal growth orientation in the (012)-direction is disclosed in EP-A-603144, in the (110)-direction in and in the (104) - EP-A-659903 direction in EP-A-738336. The object of the present invention is, thus, to provide onto a cemented carbide substrate or preferably onto the aforementioned TiC x N y O z coating at least one essentially single-phase Al 2 O 3 -layer of the polymorph κ with a desired microstructure and crystallographic texture using suitable nucleation and growth conditions such that said properties of the Al 2 O 3 -layer are stabilized. It is a further object of the invention to provide an alumina coated cutting tool insert with improved cutting performance when machining ball bearing steel. Fig 1 shows a Scanning Electron Microscope (SEM) top-view micrograph at 2000X magnification of a typical Al 2 O 3 -coating produced with the claimed process. According to the invention there is provided a cutting tool comprising a body of cemented carbide onto which a wear resistant coating has been deposited. The coating comprises one or more refractory layers of which at least one layer is a dense and textured Al 2 O 3 -layer of the κ polymorph. A cutting tool coated according to the present invention exhibits improved wear resistance compared to prior art tools when machining ball bearing steel with coolant. More specifically, the coated tool comprises a substrate of a sintered cemented carbide body, cermet or a ceramic body preferably of at least one metal carbide in a metal binder phase. The individual layers in the coating structure may be TiC or related carbide, nitride, carbonitride, oxycarbide and oxycarbonitride of a metal selected from the group consisting of metals in the Groups IVB, VB and VIB of the Periodic Table of the Elements, B, Al and Si and/or mixtures thereof. At least one of said layers is in contact with the substrate. However, at least one of the layers in the coating structure comprises a fine-grained, dense, essentially single-phase κ-Al 2 O 3 coating free of microporosity and crystallographic defects. This coating is preferentially textured with a thickness of d = 0.5-25 µm, preferably 1-10 µm and with a grain size of 0.5-6 µm, preferably 0.5-4 µm. The Al 2 O 3 -layer according to the invention has a preferred crystal growth orientation in the (210) direction which is determined by X-ray Diffraction (XRD) measurements. A Texture Coefficient, TC, can be defined as: TC(hkl) = I(hkl) I o (hkl) { 1 n Σ I(hkl) I o (hkl) } -1 where I(hkl) = measured intensity of the (hkl) reflection I o (hkl) = standard intensity of the ASTM standard powder pattern diffraction data n = number of reflections used in the calculation, (hkl) reflections used are: (002), (112), (013), (122), (113), (032), (210), (222), (050). According to the invention TC for the set of (210) crystal planes is larger than 1.5, preferably larger than 2.5 and most preferably larger than 3.0. In a preferred embodiment the alumina layer according to the present invention is preferably the outermost layer but there may also be deposited on top of it one or more further layers such as a thin up to 1 µm thick TiN-layer. In yet a preferred embodiment said alumina layer is in contact with a TiC x N y O z -layer which preferably is the innermost layer of the coating. The textured Al 2 O 3 -coating according to the invention is obtained by careful control of the process conditions during the nucleation of the Al 2 O 3 . It is furthermore of vital importance to set the oxidation potential of the process gases, i.e. the water vapour concentration, prior to the Al 2 O 3 -nucleation to less than 5 ppm. The nucleation of Al 2 O 3 is initiated by a controlled sequencing of the reactant gases as follows: H 2 and HCl are first allowed into the reactor in above mentioned order followed by AlCl 3 and at last CO 2 . The amount of HCl added should be controlled to be between 2.5 and 10 vol-%, preferably between 3.0 and 6.0 vol-%, most preferably between 3.5 and 5.0 vol-% during the nucleation. The temperature shall preferably be between 950 and 1000°C during the nucleation. The growth step in the alumina deposition process may be performed at the same temperature as the nucleation step but a dopant, a sulphur containing gas, preferably H 2 S, is added in order to enhance the deposition rate. However, the exact conditions depend to a certain extent on the design of the equipment used. It is within the purview of the skilled artisan to determine whether the requisite texture and coating morphology have been obtained and to modify the nucleation and the deposition conditions in accordance with the present specification, if desired, to effect the amount of texture and coating morphology. It has also been found that a smooth coating surface will further improve the cutting performance of the tool insert. A smooth coating surface can be obtained by a gentle wet-blasting of the coating surface with fine grained 37-105 µm (400 - 150 mesh) alumina powder or by brushing the edges with brushes based on e.g. SiC as been disclosed in EP-A-693574. Example 1. A. Cemented carbide cutting inserts with the composition 5.5 wt-% Co, 8.6 wt-% cubic carbides and balance WC were coated in a chemical vapour deposition process with 4 µm of TiCN. In a subsequent process within the same coating cycle, a 6 µm thick κ-Al 2 O 3 -layer was applied. The Al 2 O 3 coating process was divided into two parts: a nucleation part and one growth part during which the process was catalysed using H 2 S as dopant. During the nucleation step of Al 2 O 3 the process parameters were controlled in order to promote the (210) texture of the Al 2 O 3 -layer. Prior to the Al 2 O 3 deposition process the oxidation potential of the gas passing through the reactor was kept at a minimum to ensure that the surface composition would promote κ-Al 2 O 3 deposition. The process conditions during the Al 2 O 3 deposition process were: Nucleation Growth CO 2 , vol-% 3.5 3.5 AlCl 3 , vol-% 2.3 2.3 HCl, vol-% 3.5 4.5 H 2 S, vol-% --- 0.4 H 2 balance balance Pressure, mbar 55 55 Temperature, °C 980 980 Duration, h 1 8.5 XRD-analysis showed that the coating consisted of single phase κ-Al 2 O 3 with a texture coefficient TC(210) of 3.3 of the (210) planes. SEM-studies showed a 6 µm thick Al 2 O 3 -layer. B. Cemented carbide cutting inserts of the same composition as in A above were subjected to a coating process and coated with 5 µm of TiCN and then 5.8 µm of κ-Al 2 O 3 . The κ-Al 2 O 3 deposition was performed according to prior art technique. XRD analysis of the coating showed that the Al 2 O 3 consisted of single-phase κ-Al 2 O 3, with a texture coefficient TC(013) of 3.1 of the (013) plane. C. Cemented carbide cutting inserts according to A were coated in a process with TiCN followed by an Al 2 O 3 process according to a prior art technique resulting in a mixture of coarse α-Al 2 O 3 grains and fine κ-Al 2 O 3 grains. On a polished cross-section the coating thicknesses were found to be 5,0 µm of TiCN and about 6.2 µm for the mixed-phase Al 2 O 3 . A XRD investigation showed that the ratio κ/α was about 0.4. The κ-Al 2 O 3 exhibited a texture coefficient TC (013) of 2.6 of the (013)-planes and the α-Al 2 O 3 showed no preferred orientation. D. Inserts from deposition A were subjected to a heat treatment for 8 hours in flowing H 2 -atmosphere. This resulted in a transformation of κ-Al 2 O 3 to 100 % α-Al 2 O 3 . According to XRD-analysis the α-Al 2 O 3 exhibited a texture coefficient TC of 1.5 of the (104) plane as well as of the (110)-plane. The inserts were then tested with respect to flank wear resistance in a longitudinal turning operation in ball bearing steel (similar to DIN 100 Cr Mo 6). Cutting data: Speed: 200 m/min Cutting depth: 2.0 mm Feed: 0.36 mm/rev Coolant was used The result is expressed in the table below as working time required to reach a predetermined flank wear of 0.3 mm on the cutting inserts. Time to reach 0.3 mm flank wear, min Test 1 Test 2 A κ-Al 2 O 3 (210) 22.5 22.5 (invention) B κ-Al 2 O 3 (013) 15 17.5 C α+κ-Al 2 O 3 15 15 D heat treated A 15 17.5 Example 2. A. Cemented carbide cutting inserts with the composition 5.5 wt-% Co, 8.6 wt-% cubic carbides and balance WC as in example 1 above were coated in a Chemical Vapour Deposition (CVD) process with 4 µm of TiCN followed by 5.8 µm of κ-Al 2 O 3 according to the invention. The process conditions during the Al 2 O 3 deposition process were: Nucleation Growth CO 2 , vol-% 3.5 3.5 AlCl 3 , vol-% 2.3 2.3 HCl, vol-% 5.0 3.5 H 2 S, vol-% --- 0.4 H 2 balance balance Pressure, mbar 55 55 Temperature, °C 980 980 Duration, h 1 8.5 XRD-analysis showed that the coating consisted of single phase κ-Al 2 O 3 with a texture coefficient TC(210) of 2.2 of the (210) planes. B. Cemented carbide cutting inserts of the same composition as in A above were subjected to a coating process and coated with 4 µm of TiCN and then 6.3 µm of κ-Al 2 O 3 . The κ-Al 2 O 3 deposition was performed according to prior art technique. XRD analysis of the coating showed that the Al 2 O 3 consisted of single-phase κ-Al 2 O 3 with crystal (013)-orientation, with a texture coefficient TC of 3.2 of the (013)-plane. SEM studies of the inserts showed that the alumina layer had an average grain size of 2.8 µm. C. Cemented carbide cutting inserts according to C in example 1 above. The inserts were then tested with respect to flank wear resistance in a longitudinal turning operation in ball bearing steel (similar to DIN 100 Cr Mo 6). Cutting data: Speed: 200 m/min Cutting depth: 2.0 mm Feed: 0.36 mm/rev Coolant was used The result is expressed in the table below as working time required to reach a predetermined flank wear of 0.3 mm on the cutting inserts. Time to reach 0.3 mm flank wear, mm Test 1 Test 2 A κ-Al 2 O 3 (210) 30 35 (invention) B κ-Al 2 O 3 (013) 22.5 22.5 C α+κ-Al 2 O 3 12.5 15 Example 3. Inserts from example 1 were subjected to wet blasting with 37 µm (150 mesh) Al 2 O 3 after the coating processes in order to smoothen the layer. They were then tested in a facing operation in SS2172-4. Edge line flaking is the critical wear mechanism in this turning operation Cutting data: Speed: 130 m/min Feed: 0.2 mm/rev Cutting depth: 2.0 mm The shape of the workpiece was such that the cut was interrupted three times during each revolution. Flaking (%) Edge line Inserts B Example 1 78 Inserts A Example 1 67 Inserts A Example 1, wet blasted 3

Claims: Body at least partially coated with one or more refractory layers of which at least one is alumina characterized in said alumina having a coating thickness of 0.5-25 µm and consisting of single-phase κ-Al 2 O 3 textured in the (210)-direction with a texture coefficient larger than 1.5, preferably larger than 2.5 and most preferably larger than 3.0, the texture coefficient being defined as below: TC(hkl) = I(hkl) I o (hkl) { 1 n Σ I(hkl) I o (hkl) } -1 where I(hkl) = measured intensity of the (hkl) reflection I o (hkl) = standard intensity of the ASTM standard powder pattern diffraction data n = number of reflections used in the calculation, (hkl)reflections used:(002), (112), (013), (122), (113), (032), (210), (222), (050). Body according to the preceding claim characterized in that said alumina layer is the outermost layer. Body according to any of the preceding claims characterized in that said alumina layer is in contact with a TiC x N y O z layer. Body according to claim 3 characterized in that said TiC x N y O z layer is the innermost layer of the coating. Body according to any of the preceding claims characterized in that on top of said alumina layer is a thin up to 1 µm thick TiN-layer. Body according to any of the preceding claims characterized in that said body is a cutting tool of cemented carbide, titanium based carbonitride or ceramics. Method of coating a body with a κ-alumina coating at which the body is brought in contact with a hydrogen carrier gas containing one or more halides of aluminium and a hydrolyzing and/or oxidizing agent at high temperature characterized in that the oxidation potential prior to the alumina coating is kept at a low level using a total concentration of H 2 O or other oxidizing species below 5 ppm, that the nucleation of alumina is started up by controlled sequencing of the reactant gases, that HCl and AlCl 3 are entering the reactor first in a H 2 atmosphere followed by CO 2 that the amount of HCl is controlled to be 2.5-10 vol-%, preferably 3.0-6 vol-%, most preferably 3.5-5 vol-% that the temperature is between 950-1000°C during the nucleation and that during the growth of the Al 2 O 3 a sulphur containing gas is added, preferably H 2 S. Method of coating a body with a κ-alumina coating according to claim 7 characterized in that the alumina is subjected to a post-treatment such as wet-blasting.

Inventors: KUTSCHER ASA, KUTSCHER, ASA
Applicants: SANDVIK AB, SANDVIK AKTIEBOLAG
Application year: 1996
Main classification: C23C16
IPC codes: B23B27, C23C30, C23C16