Al2O3-COATED CUTTING TOOL PREFERABLY FOR NEAR NET SHAPE MACHINING

Abstract: A body is disclosed with a coating comprising one or more refractory layers of which one layer is an outermost smooth, shiny 110-textured alpha -Al2O3 layer. Said Al2O3 layer has a surface appearance almost like a polished Al2O3 layer. The alpha -Al2O3 layer is applied by a CVD method. The oxidation potential of the CVD reactor atmosphere prior to the nucleation of Al2O3 is kept at a low level. The nucleation of Al2O3 is started by a controlled sequencing of the reactant gases. Two different dopants (H2S and SF6) are used providing different growth conditions. By changing the growth condition after a certain scheme, it is possible to grow the desired alpha -Al2O3 layer.

Description: Al 7 O 7 -COATED CUTTING TOOL PREFERABLY FOR NEAR NET SHAPE MACHINING BACKGROUND OF THE INVENTION The present invention relates to an Al 2 O 3 coated cutting tool for chip forming machining and in particular for near net shape machining. Cemented carbide cutting tools coated with various t pes of Al 2 O 3 layers, e.g., pure κ-Al 2 O 3 , mixtures of K- and α-Al 2 O 3 and very coarse-grained a- Al 2 O 3 have been commercially available for many years. Al 2 O 3 crystallizes in several different phases: , K, y, β, θ, etc. The two most frequently occurring phases formed by the CVD of wear resistant Al 2 O 3 layers 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 0.5-2.0 μm, often exhibiting a columnar coating morphology. Furthermore, κ-Al 2 O 3 layers are free from crystallographic defects and free from micropores or voids. The α-Al 2 O 3 grains are usually coarser with a grain size of 1-6 μm depending upon the deposition conditions. Porosity and crystallographic defects are in this case more common. Often, both a- and κ-phase are present in an Al 2 O 3 CVD layer deposited onto a cutting tool. In commercial cutting tools, AI 2 O 3 is always applied on TiC coated carbide or ceramic substrates (se, e.g., U.S. Patent 3,837,896, now Reissue U.S. Patent No. 29,420) and therefore the interfacial chemical reactions between the TiC surface and the Al 2 O 3 layer are of particular importance. In this context, the TiC layer should also be understood to include layers having the formula TiC„N,O r in which the carbon in TiC is completely or partly substituted by oxygen and/or nitrogen. U.S. Reissue Patent No. 29,420 and U.S. Patent Nos. 4,399,168, 4,018,631, 4,490,191 and 4,463,033 disclose oxide coated bodies and how different pretreatments, e.g., of TiC-coated cemented carbide, enhance the adherence of the subsequently deposited oxide layer. Al 2 O 3 coated bodies are further disclosed in U.S. Patent Nos. 3,736,107, 5,071,696 and 5,137,774 wherein the Al 2 O 3 layers comprise a, K and a+κ combinations, respectively. U.S. Patent No. 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 selected from the groups consisting of sulphur, selenium, tellurium, phosphorous arsenic, antimony, bismuth and mixtures thereof. Under these process conditions, essentially two phases of Al 2 O 3 , the α- and the κ-phases, are produced. The resulting layer consists of a mixture of the smaller κ-grains and the larger -grains. The process yields layers with an even layer thickness distribution around the coated body. In U.S. serial nos. 08/159,217, 08/348,084 and 08/366,107, methods are disclosed how to deposit fine-grained textured α-Al 2 O 3 layers. In U.S. serial no. 08/348,084, the Al 2 O 3 layer is deposited under influence of a sulphur-fluorine dopant. The resulting Al 2 O 3 layer generally has platelet-shaped grains with a strong 110-texture. The Al 2 O 3 layer is almost free from cooling cracks. Nowadays, many components in industry are forged or pressed close to their final dimensions. Thus, less machining is needed to finalize the components. Such so-called "near net shape machining" requires tools (e.g., indexable inserts) with smooth clean cutting edges, that is, a cutting edge free from smearings of work piece material, free from flaking of layers and with a very little developed flank and crater wear in order to ensure a good machined surface finish on the final component. Using cutting edges with very little developed wear makes it difficult for the machine operator by naked eye inspection to differentiate between such an edge and an unused cutting edge ("edge identification"). This is particularly difficult if the top layer is AI 2 O 3 which color is dark grey or black. By mistake, the use of a used tool edge, e.g., during an unmanned night shift run, may cause component rejection and unwanted production stops. Edge identification can more easily be done if the insert has a top layer of TiC„N y O 2 or in particular, if the top layer is a goldish TiN layer. Generally, with thin top layers of, e.g., TiN, on Al O 3 , the smoothness and shininess of the insert surface and hence the cutting performance is influenced by the morphology of the AJ : O : . layer. Although the α-Al 2 O 3 layers disclosed in U.S. serial nos. 08/159,217, 08/348,084 and 08/366,107 mentioned above exhibit excellent wear and flaking properties, the coating surface topography is not always optimal for near net shape machining unless these coatings are mechanically smoothened, e.g., by brushing, polishing or blasting methods. For example, in U.S. Patent No. 4,966,501 a method for obtaining a smooth cutting edge by diamond polishing is disclosed. However, post treatment of coated tools increase production costs. By smooth coatings (not mechanically treated) in this context is meant coatings with grains facets essentially parallel or almost parallel to the coating surface and with only small ditches between the grains. Such surfaces generally appear very shiny and are less prone to have work piece material adhere onto the edge. Coating surface topography is influenced by grain size, grain shape and grain orientation which in turn is determined by process conditions used during the nucleation and growth steps. A smooth coating surface of a thick, >4 μm, Al 2 O 3 layer structure can, to a certain extent, be obtained by interrupting the Al 2 O 3 layer with a number of very thin layers (0.1-1.0 μm) of TiC x N y O z . However, such multilayer CVD processes are very complicated. There is always a great risk for flaking of the individual layers. With this technique, it is not possible to grow an outermost layer of α-Al 2 O 3 thicker than about 2 μm if the smoothness of the layer has to be maintained. OBJECTS AND SUMMARY OF THE INVENTION It is an object of this invention to avoid or alleviate the problems of the prior art. It is further an object of this invention to provide a smooth and shiny Al 2 O 3 layer suitable for near net shape machining. It is still further an object of this invention to find process conditions in order to deposit α-Al 2 O 3 layers with smooth, shiny surface and thereby avoid costly post treatment production processes of the coated tools. In one aspect of the invention there is provided a body with a <20 μm thick coating including an outermost layer of α-Al 2 O 3 with a thickness of 2.5- 12 μm 3-8 μm, wherein said Al 2 O 3 layer as coated, has a smooth, shiny appearance like it has been polished. In another aspect of the invention there is provided a method of coating a body with an α-Al 2 O 3 layer by CVD by which the body is brought in contact with a hydrogen carrier gas containing one or more halides of aluminum and a hydrolyzing and/or oxidizing agent at a high temperature wherein the oxidation potential of the CVD reactor atmosphere prior to the nucleation of Al 2 O 3 is kept at a low level using a total concentration level of H 2 O or other oxidizing species such as CO 2 , O 2 , etc., below 5 ppm, the nucleation of Al 2 O 3 is started by a controlled sequencing of the reactant gases in the following order: CO 2 , CO and A1C1 3 , that the temperature is about 1000°C during the nucleation and that during the growth of the Al 2 O 3 layer, two different dopants are used providing different growth conditions. BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a SEM photo in lOOOX of the smooth α-Al 2 O 3 layer surface along the edge line of a cutting insert coated according to the presently claimed invention. FIG. 2 is an α-Al 2 O 3 layer according to U.S. serial no. 08/348,084. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS OF THE INVENTION Surprisingly, a CVD method has been found to grow α-Al 2 O 3 layers with a desired microstructure and surface topography. Furthermore, such α.-Al 2 O 3 layers have a surprisingly smooth surface morphology very suitable for the application of thin (OJ-l μm) top coatings of TiC,N y O If in particular, a TiN layer, in order to make "edge identification" easier. The method employed is based on the principle of first carefully controlling the nucleation step in order to grow the α-Al 2 O 3 phase and then to alter the growth conditions a number of times, for instance, 3 to 10 times, during the entire Al 2 O 3 deposition step in order to obtain the desired coating moφhology. It has been found that the two dopants, H 2 S and SF 6 , give different α-Al 2 O 3 growth conditions and by employing this fact and changing the growth condition after a certain scheme, it is possible to grow the desired -Al 2 O 3 layers. According to the presently claimed invention, an α-Al 2 O 3 layer, 2.5-12 μm thickness, preferably 3-8 μm thickness, with an average grain size of 1-3 μm and an average surface smoothness of R π .^≤.0.4 μm over a length of 10 μm is provided which layer has by a naked eye observation, a shininess similar to a polished, brushed or wet-blasted Al 2 O 3 layer. However, the layer according to the presently claimed invention can easily be distinguished from a mechanically treated layer by SEM studies at magnification of about 3000X. In the mechanically treated layer, the grains are deformed. In the layer of the presently claimed invention, the grains are not deformed and are parallel or essentially parallel to the top surface. The body of the presently claimed invention comprises a substrate of a sintered cemented carbide, cermet or a ceramic body preferably of at least one metal carbide in a metal binder phase. The individual layers in the layer 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, B, Al and Si and/or mixtures thereof. At least one of said layers is in contact with the substrate. The outermost layer or the second outermost layer in the coating (in case of a thin top layer, see below) structure comprises a dense, single phase texture α-Al 2 O 3 layer with a smooth shiny surface. Preferably, said Al 2 O 3 layer is in contact with a TiC x N y O z layer which preferably is the innermost layer of the coating. The coated bodies are preferably used as a metal cutting tools, most preferably for use in near net shape machining. A thin, up to 1 μm thick, TiN layer on top of the Al 2 O 3 layer gives the tool a shiny goldish appearance which makes the so-called "used edge identification" easier. The improved cutting performance of such coated tool compared to a prior art tool is demonstrated in Example 3. In addition to the smooth shiny surface of the Al 2 O 3 layer according to the presently claimed invention, the Al 2 O 3 layer is also characterized by its preferred crystal growth orientation in the (110) direction. The Al 2 O 3 layer disclosed in U.S. serial no. 08/348,084 is also textured in the 110-direction. However, that layer does not exhibit the favorable smooth, shiny surface and grain shape as the Al 2 O 3 layer according to the presently claimed invention. The texture is determined by X-Ray Diffraction (XRD) measurements. A Texture Coefficient, TC, is defined as: where I(hkl) = measured intensity of the (hkl) reflection I 0 (hkl) = standard intensity of the ASTM standard powder pattern diffraction data n = number of reflections used in the calculation (hkl), reflections used are: (012), (104), (110), (113), (024), (116). According to the presently claimed invention, TC for the set of (110) crystal planes is larger than 1.5, preferably larger than 2.5. The smooth, shiny and 110-textured α-Al 2 O 3 layer according to the presently claimed invention is obtained by careful control of the oxidation potential of the CVD-reactor atmosphere prior to the nucleation of Al 2 O 3 . The total concentration level of H 2 O or other oxidizing species should preferably be below 5 ppm. However, the nucleation of Al 2 O 3 is initiated by a controlled sequencing of the reactant gases as follows: CO 2 , CO and A1C1 3 in a H 2 atmosphere. The temperature shall preferably be about 1000 β C, generally between 970 to 1030°C, during the nucleation. According to the presently claimed invention, during the Al 2 O 3 growth process two different dopants are employed, one sulphur-based dopant containing no fluorine, preferably H 2 S in a concentration OJ-1 % by volume of the total atmosphere, while the other is a sulphur-fluorine-based dopant, preferably SF 6 0J-1 %. In one embodiment, the change in growth conditions is obtained by switching between the two dopants a number of times during the Al 2 O 3 process, e.g., at least every hour, preferably in shorter periods, e.g., every 20 minutes. In an alternative embodiment, mixtures of two types of dopants mentioned above are used. As an example, a concentration of 0J % H 2 S is kept throughout the entire Al 2 O 3 process while SF 6 is introduced in intervals of 10 min to 1.5 h with a concentration of 0.3-1 % by volume of the total atmosphere. HC1 can optionally be added to the process gas mixture (see patent examples) in order to control the growth rate. Different grain size and grain shape can be obtained by using different dopant concentrations and different intervals of treatment in accordance with the present invention and using the skill of the artisan. It is smprising how grain shape, grain size and crystallographic texture can be changed and controlled by employing the two types of dopants mentioned above. Other growth conditions can be used provided that they provide sufficient change in growth conditions. The exact process conditions, however, 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 desired coating moφhology has been obtained and to modify the nucleation and the deposition conditions in accordance the present specification, if desired, to effect the surface appearance and smoothness of the layer. Inserts coated according to the presently claimed invention can be used for all kinds of machining. However, they are particularly useful for near net shape machining where clean cutting edges are required. The invention is additionally illustrated in connection with the following Examples which are to be considered as illustrative of the present invention. It should be understood, however, that the invention is not limited to the specific details of the Examples. Example 1 A) Cemented carbide cutting inserts with the composition 6.5% Co, 8.5% cubic carbides and balance WC were coated with a 6 μm thick layer of TiCN. In subsequent process steps during the same coating cycle, a 5 μm thick layer of α-Al 2 O 3 was deposited. Prior to the nucleation, the oxidation potential of the hydrogen carrier gas, i.e., the water vapor concentration, was explicitly set forth to a low level, less than 5 ppm. A reaction gas mixture comprising CO 2 , CO and A1C1 3 was sequentially added to the hydrogen carrier gas in given order. The gas mixtures and other process conditions during the Al 2 O 3 deposition steps 1-5 comprised: Step 1 2 3 4 5 CO 2 4% 4% 4% 4% 4% A1C1 3 4% 4% 4% 4% 4% CO 2% — — — — SF 6 — 0.3% — 0.3% — H 2 S ~ — 0.3% ~ 0.3% HC1 1.5% 4% 4% 4% 4% H 2 balance balance balance balance balance Pressure 60 mbar 60 mbar 60 mbar 60 mbar 60 mbar Temperature 1000°C 1030°C 1030°C 1030°C 1030°C Duration l h 1.5 h 1.5 h 1.5 h 1.5 h The resulting Al 2 O 3 layer appeared very smooth and shiny. A cooling crack network could be observed in SEM. XRD analysis showed a texture coefficient, TC(llO), of 1.8 of the (110) planes in the single α-phase of the Al 2 O 3 layer. B) The cemented carbide substrate of A) was coated with TiCN (6 μm) and Al 2 O 3 (5 μm) as set forth in A) except for that the Al 2 O 3 process was carried out according to prior art technique resulting in a mixture of coarse a- and fine κ-Al 2 O 3 grains in the layer. C) The cemented carbide substrate of A) was coated with TiCN (6 μm) and Al 2 O 3 (5 μm) as set forth in A) except for that the Al 2 O 3 process was carried out according to U.S. serial no. 08/348,084 resulting in an α-Al 2 O 3 layer with elongated Al 2 O 3 grains and with a texture coefficient of 3.2. The cutting inserts from A), B) and C) were tested with respect to edge line flaking in a facing operation in an alloyed steel (AISI 1518, W-no. 1,0580). The shape of the machined work piece was such that the cutting edge was intermitted three times during each revolution. Cutting data: Speed = 130-220 m/min Cutting Depth = 2 mm and Feed = 0.2 mm/rev The inserts were run one cut over the face of the work piece. The result below is expressed as percentage of the edge line in cut that obtained flaking. Flaking. (%) Edge Line Cleanness of Edge A) single phase/ 10 Almost no smearings textured α-Al 2 O 3 according to the invention B) α+/ Al 2 O 3 72 Smearings C) 110-textured 43 Some smearings according to U.S. serial no. 08/348,084 Example 2 D) Cemented carbide cutting inserts with the composition 6.5% Co, 8.5% cubic carbides and balance WC were coated with a 7 μm thick layer of TiC. In subsequent process steps during the same coating cycle, a 6 μm thick layer of α-Al 2 O 3 was deposited. Prior to the nucleation, the oxidation potential of the hydrogen carrier gas, i.e. , the water vapor concentration, was explicitly set forth to a low level, less than 5 ppm. A reaction gas mixture comprising CO 2 , CO and A1C1 3 was sequentially added to the hydrogen carrier gas in given order. The gas mixtures and other process conditions during the Al 2 O 3 deposition steps comprised: Step 1 • 2 3 CO 2 4% 4% 4% A1C1 3 4% 4% 4% CO 2% — ~ SF 6 — 0.4% — H 2 S — — 0.4% HC1 1.5% 4% 4% H 2 balance balance balance Pressure 60 mbar 60 mbar 60 mbar Temperature 1000°C 1030°C 1030°C Duration l h 20 min 20 min Steps 2 and 3 were repeated 8 times. The resulting Al 2 O 3 layer appeared very smooth and shiny. XRD analysis showed a texture coefficient, TC(llO), of 2.9 of the (110) planes in the single α-phase of the Al 2 O 3 layer. E) The cemented carbide substrate of D) was coated with TiC (7 μm) and Al 2 O 3 (6 μm) as set forth in D) except for that the Al 2 O 3 process was carried out according to U.S. serial no. 08/348,084, resulting in a fine-grained α- Al 2 O 3 layer with a 012-texture and with a texture coefficient of 2J. The cutting inserts from D) and E) were tested with respect to edge line flaking as described above in Example 1 with the following results: Flaking (%) Edge Line Cleanness of Edge D) single phase/ 5 Clean Edge textured α-Al 2 O 3 according to the invention B) 012-textured 54 Smearings according to U.S. serial no. 08/348,084 Example 3 F) Cemented carbide cutting inserts with the composition 6.5% Co, 8.5% cubic carbides and balance WC were coated with a 5 μm thick layer of TiCN. In subsequent process steps during the same coating cycle, a 5 μm thick layer of α-Al 2 O 3 was deposited. Prior to the nucleation, the oxidation potential of the hydrogen carrier gas, i.e., the water vapor concentration, was explicitly set forth to a low level, less than 5 ppm. A reaction gas mixture comprising CO 2 , CO and A1C1 3 was sequentially added to the hydrogen carrier gas in given order. The gas mixtures and other process conditions during the Al 2 O 3 deposition steps as according to A) in Example 1. On top of the Al 2 O 3 layer, a 0.2. μm TiN layer was deposited according to prior art technique. The resulting coated insert appeared very smooth, shiny and with a goldish color. XRD analysis showed a texture coefficient, TC(llO), of 2.3 of the (110) planes in the single α phase of the Al 2 O 3 layer. G) The cemented carbide substrate of F) was coated with TiCN (5 μm) and Al 2 O 3 (5 μm) as set forth in F) except that the Al 2 O 3 process was carried out according to U.S. serial no. 08/348,084. On top, a 0.2 μm TiN layer was deposited under the same process conditions as in F). The resulting coated insert showed a dull yellow color. XRD analysis showed a texture coefficient, T(012j, of 2.2. The cutting inserts from F) and G) were tested with respect to edge line flaking as has been described above in Example 1 with the following results: Flaking (%) Edge Line Cleanness of Edge F) single phase/ 22 Very Little Smearing textured α-Al 2 O 3 according to the invention + TiN top layer G) 012-textured 68 Smearings according to U.S. serial no. 08/348,084 + TiN top layer The principles, preferred embodiments and modes of operation of the present invention have been described in the foregoing specification. The invention which is intended to be protected herein, however, is not to be construed as limited to the particular forms disclosed, since these are to be regarded as illustrative rather than restrictive. Variations and changes may be made by those skilled in the art without departing from the spirit of the invention.

Claims: WHAT IS CLAIMED IS: 1. A body with a <20 μm thick coating including an outermost layer or second outermost layer of α-Al 2 O 3 with a thickness of 2.5-12 μm wherein said Al 2 O 3 layer as coated, has a smooth, shiny appearance like it has been polished. 2. The body of claim 1 wherein said Al 2 O 3 layer has a 110- texture with a texture coefficient larger than 1.5, the texture coefficient being defined as: τc(hki) J ( JcI) "1 where I(hkl) = measured intensity of the (hkl) reflection I 0 (hkl) = standard intensity of the ASTM standard powder pattern diffraction data n = number of reflections used in the calculation (hkl), reflections used are: (012), (104), (110), (113), (024), (116). 3. The body of claim 1 wherein said Al 2 O 3 layer has an average surface smoothness of R π -^0.4 μm over a length of 10 μm. 4. The body of claim 1 wherein the body is a substrate of a cemented carbide, cermet or a ceramic. 5. The body of claim 1 wherein said coating comprises layers of said Al 2 O 3 layer and a TiC,.N y O z layer. 6. The body of claim 5 wherein said Al 2 O 3 layer is atop said TiC x N y O z layer. 7. The body of claim 6 wherein on top of said Al 2 O 3 layer is a thin, up to 1 μm thick, layer of TiN. 8. The body of claim 1 wherein the outermost layer of α-Al 2 O 3 has a thickness of 3-8μm. 9. The body of claim 2 wherein the texture coefficient is larger than 2.5. 10. The body of claim 4 wherein said the cermet of said body is a titanium-based carbonitride. 11. A method of coating a body with an α-Al 2 O 3 layer by CVD by which the body is brought in contact with a hydrogen carrier gas containing one or more halides of aluminum and a hydrolyzing and/or oxidizing agent at a high temperature wherein the oxidation potential of the CVD reactor atmosphere prior to the nucleation of Al 2 O 3 is kept at a low level using a total concentration level of H 2 O or other oxidizing species such as CO 2 or O 2 below 5 ppm, the nucleation of Al 2 O 3 is started by a controlled sequencing of the reactant gases in the following order: CO 2 , CO and A1C1 3 , that the temperature is about 1000°C during the nucleation and that during the growth of the Al 2 O 3 layer, two different dopants are used providing different growth conditions. 12. The method of claim 11 wherein one of said dopants is a sulphur-based dopant containing no fluorine and the other one is a sulphur- fluorine-based dopant 13. The method of claim 12 wherein said sulphur-based dopant containing no fluorine is H 2 S. 14. The method of claim 12 wherein said sulphur-based dopant containing fluorine is SF 6 . 15. The method of claim 12 wherein said dopants are used alternatingly for a period of time of about 20 minutes. 16. The method of claim 14 wherein the concentration of the sulphur-based dopant containing no fluorine is held constant and the concentration of the sulphur-based dopant containing fluorine is added to the reaction mixture in periods of 20 minutes to 1.5 h.

Inventors: LJUNGBERG BJOERN, LJUNGBERG, BJOERN
Applicants: SANDVIK AB
Application year: 1995
Main classification: C23C16
IPC codes: B23B27, C23C16, C23C30