Coated milling insert and method of making it

The present application is a reissue of U.S. Pat. No. 6 , 177 , 178 B 1 , which is a national stage application of PCT/SE 96 / 01577 file Nov. 29 , 1996 , and which claims the benefit of priority to Swedish Application No. 9504304 - 8 filed Nov. 30 , 1995 .

The present invention relates to a coated cutting tool (cemented carbide insert) particularly useful for wet and dry milling of low and medium alloyed steels, with raw surfaces such as cast skin, forged skin, hot or cold rolled skin or pre-machined surfaces.

When milling low and medium alloyed steels with cemented carbide tools, the cutting edge is worn according to different wear mechanisms, such as chemical wear, abrasive wear, adhesive wear and by edge chipping caused by cracks formed along the cutting edge, the comb cracks.

The comb crack formation is particularly severe when wet milling is employed (using coolant). Coolant and work piece material may penetrate and widen the comb cracks and the edge will start to chip. A chipped edge will generate a bad surface finish of the machined component.

Different cutting conditions require different properties of the cutting insert. For example, when cutting in steels with raw surface zones, a coated cemented carbide insert must consist of a tough carbide and have very good coating adhesion. When milling in low alloyed steels the adhesive wear is generally the dominating wear type. Here preferably thin (1-3 μm) CVD- or PVD-coatings have to be used.

Measures can be taken to improve the cutting performance with respect to a specific wear type. However, very often such action will have a negative effect on other wear properties.

The influence of some possible measures is given below:

1.) Comb crack formation can be reduced by lowering the binder phase content. However, such action will lower the toughness properties of the cutting inserts which is not desirable. 2.) Improved abrasive wear can be obtained by increasing the coating thickness. However, thick coatings increase the risk for flaking and will lower the resistance to adhesive wear. 3.) Milling at high cutting speeds and at high cutting edge temperatures requires a cemented carbide with a rather high amount of cubic carbides (solid solution of WC-TiC-TaC-NbC). Such carbides will more easily develop comb cracks.

So far it has been very difficult to improve all tool properties simultaneously. Commercial cemented carbide grades have therefore been optimized with respect to one or few of these wear types and hence to specific application areas.

Swedish patent application 9501286-0 which corresponds to U.S. Ser. No. 08/616,012, herein incorporated by reference discloses a coated cutting insert particularly useful for dry milling of grey cast iron. The insert is characterized by a straight WC-Co cemented carbide grade and a coating including a layer of TiC x N y O z with columnar grains and a top layer of fine grained textured α-Al 2 O 3 .

Swedish patent application 9502640-7 which corresponds to U.S. Ser. No. 08/675,034, herein incorporated by reference, discloses a coated turning insert particularly useful for intermittent turning in low alloyed steel. The insert is characterized by a WC-Co cemented carbide body having a highly W-alloyed Co-binder phase and a coating including a layer of TiC x N y O z with columnar grains and a top layer of a fine grained, textured α-Al 2 O 3 .

Swedish patent application 9503056-5 which corresponds to U.S. Ser. No. 08/703,965, herein incorporated by reference, discloses a coated turning cutting tool particularly useful for cutting in hot and cold forged low alloyed steel. The insert is characterized by a WC-Co cemented carbide body having a highly W-alloyed Co-binder phase and a coating including a layer of TiC x N y O z with columnar grains and a top layer of a fine grained, α-Al 2 O 3 .

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 coated cutting tool particularly useful for wet and dry milling of low and medium alloyed steels.

In one aspect of the invention there is provided a cutting tool insert for milling low and medium alloyed steels with or without raw surfaces during wet or dry conditions comprising a cemented carbide body and a coating wherein said cemented carbide body comprises WC, 8.6-9.5 wt-% Co and 0.2-1.8 wt-% cubic carbides of Ta, Ti and Nb, with Ti present on a level corresponding to a technical impurity, and a highly W-alloyed binder phase with a CW-ratio of 0.78-0.93 and said coating comprises

a first (innermost) layer of TiC x N y O z with x+y+z=1, with a thickness of 0.1-1.5 μm, and with equiaxed grains with size <0.5 μm a second layer of TiC x N y O z with x+y+z=1, with a thickness of 1-6 μm with columnar grains with diameter of <5 μm and a layer of a smooth, fine-grained (0.5-2 μm) κ-Al 2 O 3 with a thickness of 0.5-5 μm.

In another aspect of the invention, there is provided a method of making a milling insert comprising a cemented carbide body and a coating comprising a WC-Co-based cemented carbide body with a highly W-alloyed binder phase with a CW-ratio of 0.78-0.93 with

a first (innermost) layer of TiC x N y O z with x+y+z=1, with a thickness of 0.1-1.5 μm, with equiaxed grains with size <0.5 μm using known CVD-methods a second layer of TiC x N y O z with x+y+z=1, with a thickness of 1-6 μm with columnar grains with a diameter of about <5 μm deposited by MTCVD-technique, using acetonitrile as the carbon and nitrogen source for forming the layer in a preferred temperature range of 850-900° C. and a layer of a smooth κ-Al 2 O 3 with a thickness of 0.5-5 μm.

The FIGURE is a micrograph in 10,000× magnification of a coated insert according to the present invention in which

A—cemented carbide body B—TiC x N y O z -layer with equiaxed grains C—TiC x N y O z -layer with columnar grains D—κ-Al 2 O 3 -layer with columnar like grains E—TiN-layer preferred, could be an option.

It has now surprisingly been found that by combining many different features, a cutting tool for milling with excellent cutting performance in low and medium alloyed steel with or without raw surface zones both in wet and dry milling can be obtained. The cutting tool according to the invention shows improved properties with respect to many of the wear types earlier mentioned.

The milling cutting insert according to the invention is: a cemented carbide body with a highly W-alloyed binder phase and with a well-balanced chemical composition and grain size of the WC, a columnar TiC x N y O z -layer, a κ-Al 2 O 3 -layer, a TiN-layer and optionally followed by smoothening, the cutting edges by brushing the edges with, e.g., a SiC based brush.

According to the present invention, a milling tool insert is provided with a cemented carbide body with a composition of 8.6-9.5 wt % Co, preferably 8.7-9.5 wt % Co, most preferably 8.8-9.4 wt % Co, 0.2-1.8 wt % cubic carbides, preferably 0.4-1.8 wt % cubic carbides, most preferably 0.5-1.7 wt % cubic carbides of the metals Ta, Nb and Ti and balance WC. The cemented carbide may also contain other carbides from elements from group IVb, Vb or VIb of the periodic table. The content of Ti is preferably on a level corresponding to a technical impurity. The average grain size of the WC is in the range of about 1.5-2 μm, preferably about 1.7 μm.

The cobalt binder phase is highly alloyed with W. The content of W in the binder phase can be expressed as the CW-ratio=M s /(wt % Co 0.0161) CW- ratio=M s /( wt % Co× 0 . 0161 ), where M s is the measured saturation magnetization of the cemented carbide body in kA/m hAm 2 /kg and wt % Co is the weight percentage of Co in the cemented carbide. The CW-value is a function of the W content in the Co binder phase. A low CW-value corresponds to a high W-content in the binder phase.

It has now been found according to the present invention, that improved cutting performance is achieved if the cemented carbide body has a CW-ratio of 0.78-0.93, preferably 0.80-0.91, and most preferably 0.82-0.90. The cemented carbide may contain small amounts, <1 volume %, of η-phase (M 6 C), without any detrimental effect. From the CW-value, it follows that no free graphite is allowed in the cemented carbide body according to the present invention.

The cement carbide body may contain a thin (about 5-25 μm) surface zone depleted in cubic carbides and often enriched in binder phase according to prior art such as disclosed in U.S. Pat. No. 4,610,931. In this case, the cemented carbide may contain carbonitride or even nitride.

The coating comprises

a first (innermost) layer of TiC x N y O z with x+y+z=1, preferably z<0.5, with equiaxed grains with size <0.5 μm and a total thickness <1.5 μm and preferably >0.1 μm. a layer of TiC x N y O z with x+y+z=1, preferably with z=0 and x>0.3 and y>0.3, with a thickness of 1-6 μm, preferably 2-5 μm, with columnar grains and with an average diameter of about <5 μm, preferably 0.1-2 μm a layer of a smooth, fine-grained (grain size about 0.5-2 μm) Al 2 O 3 consisting essentially of the κ-phase. However, the layer may contain small amounts, 1-3 vol-%, of the θ- or the α-phases as determined by XRD-measurement. The Al 2 O 3 -layer has a thickness of 0.5-5 μm, preferably 0.5-2 μm, and most preferably 0.5-1.5 μm. Preferably, this Al 2 O 3 -layer is followed by a further layer (<1 μm, preferably 0.1-0.5 μm thick) of TiN, but the Al 2 O 3 layer can be the outermost layer. This outermost layer, Al 2 O 3 or TiN, has a surface roughness R max ≦0.4 μm over a length of 10 μm. The TiN-layer, if present, is preferably removed along the cutting edge.

According to the method of the invention, a WC-Co-based cemented carbide body is made with a highly W-alloyed binder phase with a CW-ratio according to above, and a content of cubic carbide according to above, and a WC grain size according to above, and preferably without a binder phase enriched surface zone, a first (innermost) layer of TiC x N y O z with x+y+z=1, preferably z<0.5, with a thickness of <1.5 μm, and with equiaxed grains with size <0.5 μm using known CVD-methods.

a layer of TiC x N y O z x+y+z=1, preferably with z=0 and x>0.3 and y>0.3, with a thickness of 1-6 μm, preferably 2-5 μm, with columnar grains and with an average diameter of about <5 μm, preferably <2 μm, using preferably MTCVD-technique (using acetonitrile as the carbon and nitrogen source for forming the layer in the temperature range of 700-900° C.). The exact conditions, however, depend to a certain extent on the design of the equipment used. a smooth Al 2 O 3 -layer essentially consisting of κ-Al 2 O 3 is deposited under conditions disclosed in e.g. EP-A-523 021 which corresponds to U.S. Pat. No. 5,674,564, herein incorporated by reference. The Al 2 O 3 layer has a thickness of 0.5-5 μm, preferably 0.5-2 μm, and most preferably 0.5-1.5 μm. Preferably, a further layer (<1 μm, preferably 0.1-0.5 μm thick) of TiN is deposited, but the Al 2 O 3 layer can be the outermost layer. This outermost layer, Al 2 O 3 or TiN, has a surface roughness R max ≦0.4 μm over a length of 10 μm. The smooth coating surface can be obtained by a gentle wet-blasting of the coating surface with fine-grained (400-150 mesh) alumina powder or by brushing (preferably used when TiN top coating is present) the edges with brushes based on, e.g.; SiC as disclosed, e.g.; in Swedish patent application 9402543-4 which corresponds to U.S. Ser. No. 08/497,934, herein incorporated by reference. The TiN-layer, if present, is preferably removed along the cutting edge.

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.