Method of coating a cutting tool

FIELD OF THE INVENTION

The present invention relates to a method of coating a cutting tool, aimed for machining by chip removal, with a hard and wear resistant nitride layer with low compressive stress. The method for deposition is characterised by the use of reactive magnetron sputtering using a substrate holder, whose projected area is small compared to the target area and by a high electron density current through the substrate, obtained by applying a positive substrate bias.

BACKGROUND OF THE INVENTION

The deposition of wear resistant PVD layers on a cutting tool always implies the use of substrate rotation in order to obtain the best possible coating thickness uniformity around the tool. However, this method is, at closer examination, to be characterised as repeated periods of high deposition rate followed by longer periods without deposition or with low deposition rate, coating-off periods. This periodic deposition rate will affect the coating properties in different ways. First, the average deposition rate will be decreased, which could act as a boost of the in-situ annealing for some coating material systems and therefore reduce the intrinsic residual stress. Secondly, if the deposition rate is decreased too much, and no ultra high vacuum deposition system is used, the surface will be contaminated during the coating-off period due to adsorption, which in turn enhance the renucleation tendency. This means that commercial single layers are not true single layers but mostly multi-layer in the nanometer regime. This renucleation affects the coating properties in different ways, but will mostly increase the compressive residual stresses as well as the amount of inhomogeneous stresses.

Industrial use of thicker PVD MeN- and/or Me₂N-layers on cutting tools has so far been strongly limited due to the compressive stresses normally possessed by such layers. The high biaxial compressive residual stress state will at the cutting edge result in shear and normal stresses which will act as a pre-load of the coating. This pre-load, at a compressive biaxial stress state, will decrease the effective adhesion of the coating to the substrate. When increasing the coating thickness the shear and normal stress at the interface will increase. This effect is the limiting factor for the coating thickness of functional PVD-coatings. Therefore, large efforts during the years have been made to develop PVD processes for deposition of thicker layers with a low compressive residual stress state. Different methods have been applied such as use of low negative substrate bias (between -10 and -50 V), high substrate bias (-400V to -1000V), pulsed bias (unipolar and bipolar) as well as high pressure (above 5 Pa). However, none of these techniques is able to deposit a layer with low intrinsic compressive residual stress state with a maintained dense microstructure without induced defects caused by the rotation of the substrates.

Another approach to reduce the residual Stress State, utilising in-situ annealing during deposition e.g. low deposition rate and/or high deposition temperature, has been tested without success.

US 5,952,085 discloses a multiple layer erosion resistant coating on a substrate comprises alternate layers of tungsten and titanium diboride for gas turbine engines. All of the layers have the same thickness and preferably have thickness of between 0.3 and 1 micrometer to give improved erosion resistance. Magnetron sputtering using a positive bias is used to deposition method of the layers.

EP-A-1245693 discloses low intrinsic residual stress coatings of TiB₂ grown by magnetron sputtering from a TiB₂ target.

SUMMARY OF THE INVENTION

It is an object of the present invention to provide a method to grow wear resistant nitride layers with reduced compressive residual stress, preferably based on Al and/or Si and/or Cr, onto cutting tools for machining by chip removal.

It is a further object of the present invention to provide a method to grow the layers as microstructurally true single layers with a good coating thickness distribution.

BRIEF DESCRIPTION OF THE DRAWINGS

<ul id="ul0001" list-style="none" compact="compact"><li>Figure 1 is a schematic description of the deposition system according to present invention, in which <ul id="ul0002" list-style="none" compact="compact"><li>S is substrate holder,</li><li>M is magnetron including target,</li><li>P is vacuum pump,</li><li>V_t target potential,</li><li>V_s substrate bias (potential),</li><li>I_s substrate current and</li><li>I_t target current.</li></ul></li><li>Figure 2 shows schematically the definitions of target area, At, and substrate holder area, A_s.</li></ul>

DETAILED DESCRIPTION OF THE INVENTION

According to the present invention there is provided a method for coating cutting tools for machining by chip removal. The cutting tool comprises a body of a hard alloy of cemented carbide, cermet, ceramics, cubic boron nitride based material or high speed steel with a hard and wear resistant refractory coating. The wear resistant coating is composed of one or more layers of which at least one comprises a low compressive stressed metal nitride deposited by reactive magnetron sputtering i.e. MeN and/or Me₂N, where Me is one or more of the elements Sc, Y, Ti, Zr, Hf, V, Nb, Ta, Cr, Si, Al and B. The total amount of Al and/or Si and/or Cr, and/or B is preferably more than 40 at%, most preferably more than 60 at%. The B content should, however, be less than 10 at%. The rest of the layer(s), if any at all, are composed of metal nitrides and/or carbides and/or oxides with the elements chosen from Ti, Zr, Hf, V, Nb, Ta, Cr, W, Si and Al.

Characteristic for the method of the present invention is that the ratio between the area of the target, A_t, and the area of the substrate holder facing the target, A_s, defined as R=A_t/A_s is considerably larger than that commonly used in the process of depositing wear resistant coatings onto tools for machining by chip removal. According to the invention, R&gt;0.7 and preferably R&gt;1.0 most preferably R&gt;1.5. In addition, the distance from the target surface to the substrate surface, d_t, is small, compared to the extension of the target. The extension of the target can be approximated with the square root of the target area, then the distance is d_t&lt; (A_t)^0.5 and preferably d_t&lt; 0.7*(A_t)^0.5. In this way it is possible to deposit coatings with good uniformity all around the tool without the use of substrate rotation. This method minimises the amount of microstructural defects in the layers, which are induced during the coating-off periods, resulting in a coating with superior mechanical properties compared to coatings produced when rotating fixtures are used.

Since the area ratio, R, is large, a positive bias, V_s&gt;0, can be used, which is not possible in industrial deposition. If this condition is not fulfilled an extreme bias power supply is required and the plasma will be drained of electrons, which will stop the sputtering process. By applying a positive substrate bias, the deposition condition will change, so that there will be a net electron current from the plasma to the substrate holder. This is contradictory to the situation when a negative substrate bias is applied, which gives a net ion current from plasma to the substrate. The electron current density ϕ_s= I_s/ A_s is larger than 10 mA/cm² and preferably larger than 30 mA/cm². The high electron current density is a key factor in the present invention. The electron current increases the surface mobility of atoms and thereby decreases the generation rate of lattice defects, which are responsible for the compressive residual stress state in PVD coatings. By enhancing the surface mobility, layers with low compressive residual stresses can be deposited. Also the high electron current increases dissociation of the nitrogen molecules into atomic nitrogen. This effect eliminates the usual difficulties of achieving the correct stoichiometry of nitride coatings, normally associated to reactive magnetron sputtering. Using the present invention, nitrogen saturated nitride coatings are obtained in a wide range of nitrogen flow rates from 20 sccm up to more than 175 sccm (standard cubic centimetre per minute) at an Ar pressure of 0.25 Pa.

The use of a high ratio R in the present inventions should result in a very low productivity and therefore an unrealistic high production cost. However, by depositing the coatings (unconventionally) close to the target surface, a very high deposition rate is obtained. This extreme deposition rate will lower the production cost and make the method economically profitable. The deposition rate should be between 2 and 14 nm/s, preferably between 4 and 8 nm/s. If the deposition rate is to high, e.g. greater than 20 nm/s, the defect content of the layer will increase and this will be associated with an increased compressive residual stress state.

The average surface mobility of the elements should be adjusted in relation to the deposition rate of the process, i.e. at higher deposition rate, a higher surface mobility is required to keep the stresses at a low level. This could be adjusted by increasing the bulk temperature and/or by adjusting the composition of the sputtered flux. Of course, when optimising the composition, consideration shall also be made with respect to the mechanical properties of the final layer. In order to get a good surface atom mobility of the composition of the sputtered flux and consequently the sputtering target should comprise more than 40 at% Al and/or Si and/or Cr and/or B and preferably more than 60 at%. The B content should, however, be less than 10 at%.

In one embodiment thick MeN and/or Me₂N-layers are deposited directly onto a cutting tool substrate as mentioned above. The thickness of each individual layer then varies from 5 to 100 µm preferably from 5 to 50 µm, for metal machining when high wear resistance is desired.

In another embodiment, further layers of metal nitrides and/or carbides and/or oxides with the metal elements selected from Ti, Nb, Hf, V, Ta, Mo, Zr, Cr, W and Al are deposited together with the MeN and/or Me₂N-layer. The total coating thickness then varies from 5 to 100 µm, preferably from 5 to 50 µm, with the thickness of the non MeN and/or Me₂N, - layer(s) varying from 0.1 to 15 µm.

In yet another embodiment, thin layers (0.2 - 5 µm) with an increased effective adhesion can be deposited, using the invented method of deposition. Such layers can be used in applications where the demand on adhesion of the layer is particularly important. Examples of layers with increased effective adhesion includes layers having compositions comprising (Ti,Al)N, (Ti,Al,Cr)N, (Al,Cr)N, (Ti,Al,Si)N, (Ti,Al,Cr,Si)N, (Ti,Si)N, (Cr,Si)N.

According to the method of the present invention low compressive stress nitride layer, e.g. MeN and/or Me₂N layers are deposited by reactive magnetron sputtering using the following characteristics: <ul id="ul0003" list-style="none" compact="compact"><li>Magnetron power density: 3.1 W/cm² to 63 W/cm², preferably 9.4 W/cm² to 19 W/cm².</li></ul>

Substrate current density I_s/A_s: &gt;10 mA/cm², preferably 10 mA/cm² to 1500 mA/cm², most preferably 30 mA/cm² to 750 mA/cm². <ul id="ul0004" list-style="none" compact="compact"><li>Atmosphere: mixture of Ar and N₂ mixture or pure N₂</li><li>Total pressure: &lt;5 Pa</li><li>Bias voltage V_s: &gt;0 preferably &gt; +5 V but &lt; +60 V.</li><li>Geometrical arrangements: <ul id="ul0005" list-style="dash" compact="compact"><li>Target to substrate area; R= A_t / A_s: R&gt;0.7, preferably &gt;1.0, most preferably &gt;1.5</li><li>Target to substrate distance: d_t&lt; (A_t)^0.5, preferably d_t&lt; 0.7*(A_t)^0.5, most preferably d_t&lt; 0.7*(A_t)^0.5</li></ul></li></ul>    The sputtering target preferably contains more than 40 at% Al and/or Si and/or Cr and/or B, more preferably more than 60 at%. The B content should, however, be less than 10 at%.

Without limiting the invention to any particular theory, it is believed that the advantage of the present invention is due to a combination of several effects: <ul id="ul0006" list-style="dash" compact="compact"><li>The area relation between the target and the substrate holder, in combination with the close distance from the target to the substrate, gives an advantage of a high deposition rate with good coating thickness uniformity around the tool in absence of coating-off periods. This gives a coating with minimised amount of microstructural defects, interlayers and re-nucleation zones, caused by residual gases.</li><li>The area relation between the target and the substrate holder makes it possible to use a positive substrate bias. The positive substrate bias gives three-fold advantage due to the high electron current density: <ul id="ul0007" list-style="none" compact="compact"><li>Increased surface mobility of adatoms minimises the microstructural defects and thereby the compressive residual stress.</li></ul></li><li>Increased dissociation rate of nitrogen molecules into atomic nitrogen makes it easier to achieve desired stoichiometric composition of the layer.</li><li>Increased desorption rate of absorbed hydrogen and/or water molecules from the surface would decrease the formation rate of hydroxide based defect complex, which contribute to high compressive stresses in some coating material systems.</li><li>By using a target composition that is tailored for a high surface mobility of the adatoms, the associated risk of high compressive stress due to the high deposition rate is minimised.</li></ul>

The present invention has been described with reference to a reactive magnetron sputtering method for deposition of MeN and/or Me₂N layer(s). It is obvious that the method can also be applied to the deposition of other coating material based on metal carbonitrides and/or carbooxynitrides and/or oxynitrides with the metal elements chosen from Ti, Zr, Hf, V, Nb, Ta, Cr, W, Si and Al by adding carbon and/or oxygen containing gas.

Example 1

(Ti,Al)N-layers were deposited in a deposition system equipped with a rectangular dc magnetron sputter source with a Ti + Al target (50 at% Ti + 50 at% Al) of 318 cm². The substrate table projected surface area was 20 cm² positioned at a distance of 5 cm from the target surface.

Mirror-polished cemented carbide substrates with composition 6 wt% Co and 94 wt% WC were used. The WC grain size was about 1 µm and the hardness was 1650 HV_10.

Before deposition, the substrates were cleaned in an ultrasonic bath of an alkali solution and in alcohol. The substrates were stationarily positioned above the magnetron and resistively heated by an electron beam for 40 min to about 400°C. Immediately after heating, the substrates were argon-ion etched (ion current density 5 mA/cm²) for 30 minutes using a substrate bias of -200V. The subsequent (Ti,Al)N deposition was carried out by reactive magnetron sputtering using a magnetron power of 5 kW, an Ar pressure of 0.3 Pa, a nitrogen flow rate of 100 sccm. The substrate bias voltages, V_s, were varied in three different deposition processes: -100V, -50V and +50V. The resulting thickness of the positively biased layers was ∼ 5 µm after 20 min of deposition corresponding to a deposition rate of 4,2 nm/s. The substrate temperature was measured with a thermocouple attached to the substrate holder. The temperatures were approximately 400°C (using negative bias) to 500°C (using positive bias) at the end of the reactive deposition period.

The substrate current I_s was +1.2 A for negative V_s, irrespective of voltage. When changing from negative to positive V_s the substrate current changed sign from positive to negative and become around -10 A corresponding to electron current of 500 mA/cm².

XRD analysis showed that all layers exhibited the cubic sodium chloride structure (Ti,Al)N with a lattice parameter of about 4.18 Å.

By applying a positive V_s, a layer with low compressive residual stress states, σ_tot ≈ +0.6 GPa, was obtained measured using the XRD sin²ϕ method. The thermal stresses, σ_thermal, can be calculated using<maths id="math0001" num=""><math display="block"><mrow><msub><mrow><mtext mathvariant="italic">σ</mtext></mrow><mrow><mtext mathvariant="italic">thermal</mtext></mrow></msub><mtext> = </mtext><mfrac><mrow><msub><mrow><mtext mathvariant="italic">E</mtext></mrow><mrow><mtext mathvariant="italic">f</mtext></mrow></msub><mtext></mtext></mrow><mrow><msub><mrow><mtext>(1-ν</mtext></mrow><mrow><mtext mathvariant="italic">f</mtext></mrow></msub><mtext>)</mtext></mrow></mfrac><mtext>·(</mtext><msub><mrow><mtext mathvariant="italic">α</mtext></mrow><mrow><mtext mathvariant="italic">f</mtext></mrow></msub><mtext mathvariant="italic"> -</mtext><msub><mrow><mtext> α</mtext></mrow><mrow><mtext mathvariant="italic">sub</mtext></mrow></msub><mtext>)·(</mtext><msub><mrow><mtext mathvariant="italic">T</mtext></mrow><mrow><mtext mathvariant="italic">dep</mtext></mrow></msub><msub><mrow><mtext mathvariant="italic"> - T</mtext></mrow><mrow><mtext mathvariant="italic">ana</mtext></mrow></msub><mtext>)</mtext></mrow></math><img file="EP1548146A1_D0001.tif" /></maths>    where E_f and ν_f are the Young's modulus and Poisson's ratio of the layer, respectively. α_f and α_sub the coefficient of thermal expansion of the layer and substrate material. T_dep and T_ana are the deposition temperature and analyse temperature in K. Using α_sub = 4.8*10^-6, α_(Ti,Al)N,a = 9.35*10^-6, E_f = 450 GPa, ν_f = 0.22, T_dep = 773 K, T_ana = 298 K in the equation above gives σ_thermal = +1.2 GPa. The intrinsic stress can then be obtained by applying the equation:<maths id="math0002" num=""><math display="block"><mrow><msub><mrow><mtext>σ</mtext></mrow><mrow><mtext>int</mtext></mrow></msub><msub><mrow><mtext> = σ</mtext></mrow><mrow><mtext>tot</mtext></mrow></msub><msub><mrow><mtext> - σ</mtext></mrow><mrow><mtext>thermal</mtext></mrow></msub></mrow></math><img file="EP1548146A1_D0002.tif" /></maths>

The intrinsic stress, σ_int, of coatings deposited with positive bias is therefore: σ_int = +0.6 - 1.2 = -0.6 GPa, i.e. those coatings are grown in a low compressive intrinsic stress mode.

Using negative V_s gave layers with total residual stresses in the range of approximately -2 GPa.

Adhesion testing by Rockwell indentation displayed that the adhesion was acceptable for all layers. There was no significant difference in adhesion between variant A and D, but since D, present invention, has almost three times thicker coating the results are extremely good. The indentation test demonstrates that the layer according to the present invention has strongly enhanced toughness properties compared to layers grown using negative bias and state of the art. <tables id="tabl0001" num="0001"><table frame="all"><title>Table 1.</title><tgroup cols="6" colsep="1" rowsep="1"><colspec colnum="1" colname="col1" colwidth="26.25mm" /><colspec colnum="2" colname="col2" colwidth="26.25mm" /><colspec colnum="3" colname="col3" colwidth="26.25mm" /><colspec colnum="4" colname="col4" colwidth="26.25mm" /><colspec colnum="5" colname="col5" colwidth="26.25mm" /><colspec colnum="6" colname="col6" colwidth="26.25mm" /><thead valign="top"><row rowsep="1"><entry namest="col1" nameend="col6" align="left">Properties of the (Ti,Al)N layers.</entry></row><row><entry namest="col1" nameend="col1" align="left">Variant</entry><entry namest="col2" nameend="col2" align="left">V_s [V]</entry><entry namest="col3" nameend="col3" align="left">Deposition rate (nm/s)</entry><entry namest="col4" nameend="col4" align="left">Coating Thickness [um]</entry><entry namest="col5" nameend="col5" align="left">HR_C</entry><entry namest="col6" nameend="col6" align="left">σ [GPa]</entry></row></thead><tbody valign="top"><row><entry namest="col1" nameend="col1" align="left">A</entry><entry namest="col2" nameend="col2" align="left">Prior art</entry><entry namest="col3" nameend="col3" align="char" char=".">0.8</entry><entry namest="col4" nameend="col4" align="char" char=".">2.4</entry><entry namest="col5" nameend="col5" align="left">Good</entry><entry namest="col6" nameend="col6" align="char" char=".">-3.8</entry></row><row><entry namest="col1" nameend="col1" align="left">B</entry><entry namest="col2" nameend="col2" align="left">-100V</entry><entry namest="col3" nameend="col3" align="char" char=".">4.3</entry><entry namest="col4" nameend="col4" align="char" char=".">5.1</entry><entry namest="col5" nameend="col5" align="left">Acceptable</entry><entry namest="col6" nameend="col6" align="char" char=".">-2.1</entry></row><row><entry namest="col1" nameend="col1" align="left">C</entry><entry namest="col2" nameend="col2" align="left">-50V</entry><entry namest="col3" nameend="col3" align="char" char=".">4.5</entry><entry namest="col4" nameend="col4" align="char" char=".">5.4</entry><entry namest="col5" nameend="col5" align="left">Acceptable</entry><entry namest="col6" nameend="col6" align="char" char=".">-1.7</entry></row><row rowsep="1"><entry namest="col1" nameend="col1" align="left">D Present invention</entry><entry namest="col2" nameend="col2" align="left">+50V</entry><entry namest="col3" nameend="col3" align="char" char=".">5.1</entry><entry namest="col4" nameend="col4" align="char" char=".">6.1</entry><entry namest="col5" nameend="col5" align="left">Good</entry><entry namest="col6" nameend="col6" align="char" char=".">+0.6</entry></row></tbody></tgroup></table></tables>

Example 2

In order to determine the correct N₂ flow rate to get a stoichiometric ratio between the metallic elements and nitrogen i.e. (Ti+Al)/N ∼ 1, a test was performed where the N₂ flow rate was varied between 10 and 175 sccm. All other deposition data was kept constant i.e. the magnetron power at 5 kW, the substrate bias at +50V, Ar pressure at 0.25 Pa. The deposition system set-up was the same as in example 1. The content of Al, Ti and N in the layers was measured using EDS. The results are reported in table 2 below and show that using the present invention a surprisingly high stability for the N₂ flow rate is achieved. In the whole range between 30 sccm and 175 sccm, a stoichiometric composition is obtained. This is an effect of the high substrate electron current, increasing the dissociation rate of the N₂ molecule. No Ar could be detected in any of the layers. <tables id="tabl0002" num="0002"><table frame="all"><title>Table 2.</title><tgroup cols="6" colsep="1" rowsep="1"><colspec colnum="1" colname="col1" colwidth="26.25mm" /><colspec colnum="2" colname="col2" colwidth="26.25mm" /><colspec colnum="3" colname="col3" colwidth="26.25mm" /><colspec colnum="4" colname="col4" colwidth="26.25mm" /><colspec colnum="5" colname="col5" colwidth="26.25mm" /><colspec colnum="6" colname="col6" colwidth="26.25mm" /><thead valign="top"><row rowsep="1"><entry namest="col1" nameend="col6" align="left">Dependence of N₂ flow rate on the stoichiometry ratio (Ti+Al)/N</entry></row><row><entry namest="col1" nameend="col1" align="left">Variant</entry><entry namest="col2" nameend="col2" align="left">N₂ flow rate [sccm]</entry><entry namest="col3" nameend="col3" align="left">Ti [at%]</entry><entry namest="col4" nameend="col4" align="left">Al [at%]</entry><entry namest="col5" nameend="col5" align="left">N [at%]</entry><entry namest="col6" nameend="col6" align="left">Stoichiometry ratio (Ti+Al)/N</entry></row></thead><tbody valign="top"><row><entry namest="col1" nameend="col1" align="left">E</entry><entry namest="col2" nameend="col2" align="left">10</entry><entry namest="col3" nameend="col3" align="left">41</entry><entry namest="col4" nameend="col4" align="left">40</entry><entry namest="col5" nameend="col5" align="left">19</entry><entry namest="col6" nameend="col6" align="char" char=".">4.40</entry></row><row><entry namest="col1" nameend="col1" align="left">F</entry><entry namest="col2" nameend="col2" align="left">20</entry><entry namest="col3" nameend="col3" align="left">33</entry><entry namest="col4" nameend="col4" align="left">32</entry><entry namest="col5" nameend="col5" align="left">35</entry><entry namest="col6" nameend="col6" align="char" char=".">1.85</entry></row><row><entry namest="col1" nameend="col1" align="left">G</entry><entry namest="col2" nameend="col2" align="left">30</entry><entry namest="col3" nameend="col3" align="left">24</entry><entry namest="col4" nameend="col4" align="left">27</entry><entry namest="col5" nameend="col5" align="left">50</entry><entry namest="col6" nameend="col6" align="char" char=".">1.02</entry></row><row><entry namest="col1" nameend="col1" align="left">H</entry><entry namest="col2" nameend="col2" align="left">40</entry><entry namest="col3" nameend="col3" align="left">24</entry><entry namest="col4" nameend="col4" align="left">26</entry><entry namest="col5" nameend="col5" align="left">49</entry><entry namest="col6" nameend="col6" align="char" char=".">1.03</entry></row><row><entry namest="col1" nameend="col1" align="left">I</entry><entry namest="col2" nameend="col2" align="left">50</entry><entry namest="col3" nameend="col3" align="left">24</entry><entry namest="col4" nameend="col4" align="left">28</entry><entry namest="col5" nameend="col5" align="left">48</entry><entry namest="col6" nameend="col6" align="char" char=".">1.09</entry></row><row><entry namest="col1" nameend="col1" align="left">J</entry><entry namest="col2" nameend="col2" align="left">75</entry><entry namest="col3" nameend="col3" align="left">26</entry><entry namest="col4" nameend="col4" align="left">26</entry><entry namest="col5" nameend="col5" align="left">48</entry><entry namest="col6" nameend="col6" align="char" char=".">1.08</entry></row><row><entry namest="col1" nameend="col1" align="left">K</entry><entry namest="col2" nameend="col2" align="left">100</entry><entry namest="col3" nameend="col3" align="left">25</entry><entry namest="col4" nameend="col4" align="left">27</entry><entry namest="col5" nameend="col5" align="left">47</entry><entry namest="col6" nameend="col6" align="char" char=".">1.11</entry></row><row><entry namest="col1" nameend="col1" align="left">L</entry><entry namest="col2" nameend="col2" align="left">125</entry><entry namest="col3" nameend="col3" align="left">23</entry><entry namest="col4" nameend="col4" align="left">26</entry><entry namest="col5" nameend="col5" align="left">50</entry><entry namest="col6" nameend="col6" align="char" char=".">0.98</entry></row><row><entry namest="col1" nameend="col1" align="left">M</entry><entry namest="col2" nameend="col2" align="left">150</entry><entry namest="col3" nameend="col3" align="left">23</entry><entry namest="col4" nameend="col4" align="left">26</entry><entry namest="col5" nameend="col5" align="left">51</entry><entry namest="col6" nameend="col6" align="char" char=".">0.95</entry></row><row rowsep="1"><entry namest="col1" nameend="col1" align="left">N</entry><entry namest="col2" nameend="col2" align="left">175</entry><entry namest="col3" nameend="col3" align="left">23</entry><entry namest="col4" nameend="col4" align="left">26</entry><entry namest="col5" nameend="col5" align="left">51</entry><entry namest="col6" nameend="col6" align="char" char=".">0.95</entry></row></tbody></tgroup></table></tables>

Example 3

Cemented carbide cutting tool inserts from example 1 (the same names of the variants are used) were used in a face milling cutting test, in solid and slotted work piece material, SS2541. The homogeneous cutting test (solid work piece) was made in a 60 mm wide plate and the interrupted cutting test was performed by using three 20 mm wide plates separated by 10 mm, mounted as a package. The cutting data were; v_c = 250 m/min (homogeneous) and 200 m/min (interrupted), f = 0.1 mm/rev and depth of cut = 2.5 mm. <tables id="tabl0003" num="0003"><table frame="all"><tgroup cols="4" colsep="1" rowsep="1"><colspec colnum="1" colname="col1" colwidth="39.37mm" /><colspec colnum="2" colname="col2" colwidth="39.37mm" /><colspec colnum="3" colname="col3" colwidth="39.37mm" /><colspec colnum="4" colname="col4" colwidth="39.37mm" /><thead valign="top"><row><entry namest="col1" nameend="col1" align="left">Variant</entry><entry namest="col2" nameend="col2" /><entry namest="col3" nameend="col3" align="left">Homogeneous cut Tool life, mm</entry><entry namest="col4" nameend="col4" align="left">Interrupted cut Tool life, mm</entry></row></thead><tbody valign="top"><row><entry namest="col1" nameend="col1" align="left">A</entry><entry namest="col2" nameend="col2" align="left">Prior art (Ti,Al)N</entry><entry namest="col3" nameend="col3" align="left">2200</entry><entry namest="col4" nameend="col4" align="left">1500</entry></row><row><entry namest="col1" nameend="col1" align="left">B</entry><entry namest="col2" nameend="col2" align="left">(Ti,Al)N (V_s = -100 V)</entry><entry namest="col3" nameend="col3" align="left">1700</entry><entry namest="col4" nameend="col4" align="left">900</entry></row><row rowsep="1"><entry namest="col1" nameend="col1" align="left">D</entry><entry namest="col2" nameend="col2" align="left">Present invention (Ti,Al)N (V_s = +50 V)</entry><entry namest="col3" nameend="col3" align="left">2800</entry><entry namest="col4" nameend="col4" align="left">2100</entry></row></tbody></tgroup></table></tables>

This test demonstrates that the variant D shows the best wear resistance, but also surprisingly the best toughness in spite of the thickest coating.