Oxide coated cutting tool

Abstract: According to the present invention there is provided a body coated with refractory single- or multilayers, wherein specific layers are characterized by a controlled microstructure and phase composition with crystal planes preferably grown in a preferential direction with respect to the surface of the coated body. Said coating comprises one or several refractory layers of which at least one layer is a dense, fine-grained layer of α- Al₂O₃ preferably textured in the (012) direction. The coated tool according to the invention exhibits excellent surface finish and shows much improved wear and toughness properties compared to prior art objects when used for machining steel, cast iron and, particularly, when machining nodular cast iron.

Description: The present invention relates to a coated cutting tool for chipforming machining. The Chemical Vapour Deposition (CVD) of alumina on cutting tools has been an industrial practice for more than 15 years. 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. 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 . Cemented carbide cutting tools coated with various types Al 2 O 3 -coatings, e.g., pure κ-Al 2 O 3 , mixtures of κ- and α-Al 2 O 3 and very coarse-grained α-Al 2 O 3 have been commercially available for many years. None of these oxide coated products have shown desirable cutting properties when used for machining nodular cast iron. Nodular cast iron is a work piece material difficult to machine since it adheres onto the cutting edge of the tool resulting in a successive and fast removal of the coating from the cutting edge and, hence, a shortened tool life of the cutting insert. 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 0.5-2.0 µm and often exhibits a columnar coating morphology. Furthermore, κ-Al 2 O 3 coatings 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 α- and κ-phase are present in a CVD alumina coating deposited onto a cutting tool. In commercial cutting tools, Al 2 O 3 is always applied on TiC coated carbide or ceramic substrates (see, e.g. U.S. Pat. No. 3,837,896, now Reissue U.S. Pat. No. 29,420) and therefore the interfacial chemical reactions between the TiC-surface and the alumina coating are of particular importance. In this context the TiC layer should also be understood to include layers having the formula TiC x N y O z in which the carbon in TiC is completely or partly substituted by oxygen and/or nitrogen. 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. Although the disclosed methods result in alumina layers tightly and adherently bonded to the cemented carbide body or to a refractory layer of e.g. TiC adjacent to the cemented carbide, they do not result in the particular α-polymorph of Al 2 O 3 as disclosed in the present invention. Alumina coated bodies are further disclosed in U.S. Pat. No. 3,736,107 and EPO Nos. 0 403 461 and 0 408 535 wherein the Al 2 O 3 layers comprise α, κ resp α/κ combinations. However, these patents do not disclose the desired microstructure and crystallographic texture of the α-polymorph which is the object of the present invention. The object of the present invention is, thus, to provide onto a hard substrate or preferably onto aforementioned TiC x N y O z coating at least one single phase Al 2 O 3 layer of the polymorph α 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 in steel, stainless steel, cast iron and, in particular, in nodular cast iron. Fig 1 shows a Scanning Electron Microscope (SEM) top-view micrograph at 2,000X magnification of a typical Al 2 O 3 -coating according to the invention. According to the invention there is provided a cutting tool comprising a body of a hard alloy onto which a wear resistant coating has been deposited. The coating comprises one or several refractory layers of which at least one layer is a dense, fine-grained and preferably textured Al 2 O 3 -layer of the polymorph α. A coated cutting tool according to the present invention exhibits improved wear and toughness properties compared to prior art tools when used for machining steel or cast iron, particularly if its surface has been further smoothened by wet blasting. 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, 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, preferentially textured layer of single phase α-Al 2 O 3 having a thickness of d = 0.5-25 µm with a grain size (s) of 0.5 µm < s < 1 µm for 0.5 µm < d < 2.5 µm and 0.5 µm < s < 3 µm for 2.5 µm < d < 25 µm The fine-grained microstructure comprises a narrow grain size distribution. Most often 80 % of the Al 2 O 3 grains have a grain size of ± 50 % of the average grain-size. The grain-size of the Al 2 O 3 -coating is determined from a SEM top view micrograph at 5,000X magnification. Drawing three straight lines in random directions, the average distances between grain boundaries along the lines, are taken as a measure of the grain-size. The Al 2 O 3 -layer according to the invention has a preferred crystal growth orientation in the (012) direction which is determined by X-ray Diffraction (XRD) measurements. A Texture Coefficient, TC, can be defined as: where I(hkl) = measured intensity of the (hkl) reflection I(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 invention TC for the set of (012) crystal planes is larger than 1.3, preferably larger than 1.5. The coated body according to the invention is further characterized by a surface roughness (R a ) of the refractory coating of less than 0.3 µm over a measured length of 0.25 mm. Preferably, the Al 2 O 3 -layer is the outermost layer. The textured Al 2 O 3 -coating according to the invention is obtained by careful control of the water vapour concentration in the hydrogen carrier gas, being below 20 ppm, preferably below 5 ppm, of H 2 O, prior to the nucleation of Al 2 O 3 . The nucleation of Al 2 O 3 is started up by sequencing the reactant gases in the following order: CO 2 , CO and AlCl 3 . The temperature shall preferably be about 1000°C during the nucleation. 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 has been obtained and to modify the deposition conditions in accordance with the present specification, if desired, to effect the amount of texture. The α-Al 2 O 3 coatings according to the invention are dense and free of microporosity and crystallographic defects. This is in contrast to previous reports on α-Al 2 O 3 coatings. EXAMPLE 1 A) Cemented carbide cutting inserts with the composition 5.5 % 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 fine grained (1-2 µm), 7 µm thick layer of α-Al 2 O 3 was deposited. The oxidation potential of the hydrogen carrier gas, i.e. the water vapour concentration, was explicitly set forth to a relatively low level, 10 ppm, prior to and during the Al 2 O 3 -nucleation (See also U.S. Pat. No. 5,071,696, corresponding to EP-A-0 403 461). A reaction gas mixture comprising CO 2 , CO, and AlCl 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: 1. 2. (not in accordance with the invention) CO 2 : 4% CO 2 : 4% AlCl 3 : 4% AlCl 3 : 4% CO: 2% H 2 S: 0.2% H 2 : balance H 2 : balance Process Process pressure: 6500 Pa (65 mbar) pressure: 6500 Pa (65 mbar) Temperature: 1000°C Temperature: 1030°C Duration: 1 hr Duration: 5.5 hr XRD-analysis showed a texture coefficient, TC(012), of 2.1 of the (012) planes in the single α-phase of the Al 2 O 3 -coating. The Al 2 O 3 -coating had a surface roughness of 0.2 µm over a 0.25 mm length. B) The carbide substrate of A) was coated with TiCN (5 µm) and Al 2 O 3 (7 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 α- and fine κ-Al 2 O 3 grains in the coating. C) Tool inserts of the same substrate and coating composition and coating thickness as of A) except for that the Al 2 O 3 -coating comprises the single phase κ-polymorph according to prior art technique. Coated tool inserts from A), B) and C) were all wet blasted with 150 mesh Al 2 O 3 -powder in order to smoothen the coating surface. The cutting inserts were then tested with respect to edge line and rake face flaking in a facing operation in nodular cast iron (AISI 60-40-18, DIN GGG40). The shape of the machined work piece was such that the cutting edge is intermitted twice during each revolution. Cutting data: Speed = 150 m/min, Cutting Depth = 2.0 mm and Feed = 0.1 mm/rev. The inserts were run one cut over the face of the work piece. The results are expressed in the table below as percentage of the edge line in cut that obtained flaking as well as the rake face area subjected to flaking in relation to total contact area between the rake face and the work piece chip. Flaking (%) Edge line Rake face A) single phase/textured α-Al 2 O 3 (acc. to the inv.) 0 0 B) α/κ Al 2 O 3 40 5 C) κ-Al 2 O 3 15 45 EXAMPLE 2 Coated inserts from A) in EXAMPLE 1 were tested in a machining operation comprising external roughing with interrupted cuts. The test was carried out at an end user of cutting tools and the machined component was a differential hub made in nodular cast iron (AISI 60-40-18, DIN GGG 40). Cutting data: Speed = 270-290 m/min, Cutting Depth = 2 mm and Feed = 0.4-0.55 mm/rev. A commercial cemented carbide cutting tool with identical carbide composition as A) in Example 1 and, further, comprising a coating of 2 µm TiC and 8 µm Al 2 O 3 , was used as a reference in the cutting test. The Al 2 O 3 layer was deposited according to prior art technique resulting in a mixture of coarse α- and fine κ-Al 2 O 3 grains in the coating. Said commercial tool insert is frequently used in the machining of nodular cast iron. All inserts used in the above machining test of a differential hob were wet blasted with 150 mesh Al 2 O 3 powder. After machining 20 components, the commercial tool insert with α/κ coating showed excessive flaking with loss of the coating on more than 70% of the edge line in cut. The coated inserts from A) in EXAMPLE 1, according to the invention, machined 40 components with less than 10% of the edge line in cut showing flaking. EXAMPLE 3 D) Cemented carbide inserts with a composition 6.5 % Co, 8.8 % cubic carbides and balance WC were coated as set forth under A) in EXAMPLE 1. A fine-grained, dense α-Al 2 O 3 coating textured in the (012) direction was obtained. E) The carbide substrate of D) was coated as set forth under B) in EXAMPLE 1. An alumina coating comprising a mixture of coarse α and fine κ-Al 2 O 3 grains was obtained. Coated tool inserts from D) and E) were all wet blasted with 150 mesh Al 2 O 3 powder in order to smooth the coating surface. The cutting inserts were then 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 is 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 edgeline in cut that obtained flaking. Flaking (%) Edge line D) single phase/textured α-Al 2 O 3 (according to the invention) 0 E) α/κ Al 2 O 3 40 EXAMPLE 4 F) Cemented carbide inserts with a composition 6..5 % Co, 8.5 % of cubic carbides and balance WC were coated as set forth under A) in EXAMPLE 1. A 6 µm thick, fine-grained, dense α -Al 2 O 3 coating textured in the (012) direction was obtained. G) The carbide substrate of F) was coated as set forth under B) in EXAMPLE 1. An alumina coating comprising a mixture of coarse α and fine κ-Al 2 O 3 grains was obtained. Coated tool inserts from F) and G) were all wet blasted with 150 mesh Al 2 O 3 powder in order to smooth the coating surface. The cutting inserts were then tested with respect to rake face flaking in a facing operation in austenitic stainless steel (AISI 304L, W-no. 1,4306). The shape of the machined work piece was tubular and the inserts were run two cuts over the face of the work piece. Cutting data: Speed = 140 m/min, Cutting Depth = 0-3 mm and Feed = 0.36 mm/rev. The result below is expressed as percentage of the area on the rake face subjected to flaking in relation to the total contact area between the chip and the rake face of the insert. Flaking (%) Rake face F) single phase/textured α-Al 2 O 3 (according to the invention) 25 G) α/κ Al 2 O 3 65 EXAMPLE 5 H) Cemented carbide inserts with a composition 6.5 % Co, 8.5 % of cubic carbides and balance WC were coated as set forth under F) in EXAMPLE 4. A 6 µm thick, fine-grained, dense α-Al 2 O 3 coating textured in the (012) direction was obtained. K) The carbide substrate of H) was coated as set forth under G) in EXAMPLE 4. An alumina coating comprising a mixture of coarse α- and fine κ-Al 2 O 3 grains was obtained. Coated tool inserts from H) and K) were all wet blasted with 150 mesh Al 2 O 3 powder in order to smooth the coating surface. The cutting inserts were then tested with respect to edge line flaking in a facing operation in a cold forged steel (AISI 5015, W-no. 1,7015). The machined work piece was a gear wheel and the inserts were run 16 cuts over the face of the work piece. Cutting data: Speed = 180 m/min, Cutting Depth = 1.5 mm and Feed = 0.25 mm/rev. The result below is expressed as percentage of the edgeline in cut that obtained flaking in accordance with previous examples. Flaking (%) Edge line H) single phase/textured α-Al 2 O 3 (according to the invention) 0 K) α/κ Al 2 O 3 55

Claims: Body at least partially coated with one or more refractory layers of which at least one layer is alumina, said alumina layer having a thickness of d = 0.5-25 µm and consisting of single phase α-structure having a grain size (s): 0.5 µm < s < 1 µm for 0.5 µm < d < 2.5 µm and 0.5 µm < s < 3 µm for 2.5 µm < d < 25 pin characterized in that said alumina layer exhibits a texture coefficient (TC) larger than 1.3, preferably larger than 1.5, for the (012) growth direction of the equivalent crystallographic planes defined as: 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: (012), (104), (110), (113), (024), (116). Body according to claim 1 characterized in that the surface roughness (R a ) of the refractory coating is less than 0.3 µm over a measured length of 0.25 mm. Body according to any of the preceding claims 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 4 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 said body is a cutting tool insert of cemented carbide, titanium based carbonitride or ceramics. Method of coating a body with an alpha-alumina (Al 2 O 3 ) layer according to claim 1 or 2 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 water vapour concentration in the hydrogen carrier gas is below 20 ppm prior to the nucleation of Al 2 O 3 and that the nucleation of Al 2 O 3 is started up by sequencing the reactant gases in the following order: Co 2 , CO and AlCl 3 and that the temperature is about 1000°C during the nucleation.

Inventors: LENANDER ANDERS, LJUNGBERG BJOERN, LENANDER, ANDERS, LJUNGBERG, BJOERN, Ljungberg, Björn
Applicants: SANDVIK AB, SANDVIK AKTIEBOLAG
Application year: 1993
Main classification: C23C16
IPC codes: C23C16, B23B27, B32B9, C23C14, B23P15, B32B18