DIECHLE DOMINIC (DE)
| EP1914331A2 | 2008-04-23 | |||
| JP2010207915A | 2010-09-24 | |||
| US20090252973A1 | 2009-10-08 | |||
| DE102007030734A1 | 2009-01-08 |
| Claims 1 . Cutting tool having a base body and a coating applied thereto, characterized in that the coating comprises at least one oxide layer deposited in the PVD process, consisting of at least 10 alternating single coats of Al203 and (ΑΙχ,Μβι-χ)203 where 0 < x < 1 , wherein Me is selected from one or more of the group of Si, Ti, V, Zr, Mg, Fe, B, Gd, La and Cr. 2. Cutting tool according to claim 1 , characterized in that the single coats of (A\x,Me )2 3 of the oxide layer consisting of single coats are single phase. 3. Cutting tool according to any one of claims 1 or 2, characterized in that the single coats of Al203 of the oxide layer consisting of single coats have a γ crystal structure. 4. Cutting tool according to any one of the preceding claims, characterized in that the crystal structure of the single coats consisting of (A\x,Me )2 3 has the same crystal structure as the single coats of Al203. 5. Cutting tool according to any one of the preceding claims, characterized in that the single coats of Al203 of the oxide layer consisting of single coats have a γ crystal structure and the crystal structure of the single coats consisting of (Alx,Mei-x)203 has the same crystal structure as the single coats of Al203. 6. Cutting tool according to any one of the preceding claims, characterized in that the thickness of the single coats is 2 nm to 200 nm, preferably 3 nm to 50 nm, particularly preferably 4 nm to 10 nm. 7. Cutting tool according to any one of the preceding claims, characterized in that the oxide layer consists of 10 to 1000 single coats, preferably of 100 to 600 single coats, particularly preferably of 300 to 500 single coats. 8. Cutting tool according to any one of the preceding claims, characterized in that the overall layer thickness of the oxide layer consisting of the single coats is from 0.1 μιτι to 8 μιτι, preferably from 0.3 μιτι to 4 μιτι, particularly preferably from 0.4 μιτι to 2 μιτι. 9. Cutting tool according to any one of the preceding claims, characterized in that the fraction of Me in the oxide layer consisting of the single coats is in the range of from 0.3 at.% to 5.4 at.%, preferably in the range of from 1 .3 at.% to 2.0 at.% 10. Cutting tool according to any one of the preceding claims, characterized in that Me is selected among Si, Ti, V, Zr, Mg, Fe, Cr, and B and particularly preferably Me is Si. 1 1 . Cutting tool according to any one of the preceding claims, characterized in that the oxide layer consisting of the single coats is produced by means of sputtering, preferably dual magnetron sputtering or HIPIMS (high power impulse magnetron sputtering). 12. Cutting tool according to any one of the preceding claims, characterized in that for the manufacture of the oxide layer consisting of the single coats at least one Al target and at least one AIMe target were used. 13. Cutting tool according to any one of the preceding claims, characterized in that the AIMe target contains from 1 at.% Me to 16 at.% Me and from 99 at.% Al to 84 at.% Al, preferably 4 at.% Me to 6 at.% Me and from 96 at.% Al to 94 at.% Al. 14. Cutting tool according to any one of the preceding claims, characterized in that between the base body and the oxide layer consisting of the single coats at least one further layer is present, being or comprising a nitride, preferably TiN, TiCN, TiAIN, AICrN, TiSiN, TiAISiN, TiAICrN. 15. Cutting tool according to any one of the preceding claims, characterized in that the oxide layer consisting of the single coats has a Vickers hardness in the range of from 1800 HV to 4000 HV, preferably of from 2000 HV to 3500 HV, particularly preferably of from 2600 HV to 3000 HV. |
Introduction
The present invention relates to a cutting tool having a base body and a coating applied thereto. Cutting tools, including metal cutting tools, consist of a base body which is produced for example from hard metal, cermet, steel, high-speed steel or cubic boron nitride. Frequently a single-layer or multi-layer coating is applied to the substrate to improve the cutting characteristics as well as to increase the service lives. Such a single-layer or multi-layer coating includes for example metallic hard material layers, oxide layers, nitride layers and the like. The methods employed to apply the coating are the CVD process (chemical vapour deposition) and/or PVD process (physical vapour deposition). Multiple layers within a coating can be applied exclusively by means of CVD processes, exclusively by means of PVD processes or by a combination of those processes. CVD processes provide substantially stable phases of the desired compounds wheres PVD processes also make it possible to apply metastable phases of compounds.
In regard to PVD processes a distinction is drawn between various variants in such processes such as magnetron sputtering, arc vapour deposition (arc PVD), ion plating, electron beam vapour deposition and laser ablation. Of these PVD processes there are in turn different variations and modifications. Applying different variants of PVD processes as well as variations of the deposition parameters within one variant of a PVD process may render a layer deposited thereby different structural, morphological and/or physical properties even with an otherwise identical chemical composition of the layer.
DE 10 2007 030 734 describes a cutting tool with a base body and a single-layer or multi-layer coating applied thereto. The coating includes at least one two-phase or multi-phase layer, comprising at least two different phases of metal oxide, wherein the at least one two-phase or multiphase layer is electrically conductive.
Schmucker et al. (2001 ), "Constitution and crystallization behavior of ultrathin physical vapor deposited (PVD) Al 2 0 3 /Si0 2 laminates", Journal of the European Ceramic Society 21 (2001 ); 2503- 2507, describe the production of very thin Al 2 0 3 /Si0 2 multi layers by means of PVD using two targets and electron beam deflection of a single electron beam.
When applying oxide layers, in particular when using PVD processes, the problem arises that such layers have a high degree of hardness whereas they are brittle in general. For chip- removing manufacturing processes, in particular milling operations, it is however necessary that the cutting tools apart from the hardness, imparted by the oxide, also show a high degree of toughness which amongst others increases the service life of the tool.
Sputtered Al 2 0 3 /Si0 2 single-layer coatings with a nanocrystalline γ-structure as well as single (AICr) 2 0 3 layers deposited by means of arc PVD, having proportions of a and γ, however, having a high fraction of droplets, or (AICr) 2 0 3 single layers with proportions of a and/or γ, deposited by magnetron sputtering, have been suggested so far for solving this problem. Although these coatings provide an improvement with respect to fracture toughness to some extent, no satisfying solution could be provided, yet, with respect to the problem of the high brittleness, in particular for milling cutters.
The invention
In view of this prior art, the object of the present invention was that of providing a cutting tool, having both a hard coating that also exhibits fracture toughness.
This object according to the invention is attained by a cutting tool as set out at the beginning, wherein the coating comprises at least one oxide layer deposited in the PVD process, consisting of at least 10 alternating single coats of Al 2 0 3 and (Al x ,Mei- x ) 2 0 3 where 0 < x < 1 , wherein Me is selected from one or more of the group of Si, Ti, V, Zr, Mg, Fe, B, Gd, La and Cr.
Such a coating has been shown to have an increased toughness, in particular an increased fracture toughness, which also goes along with improved cutting properties and increased service life, in particular in comparison to pure aluminium oxide layers.
The reason for the increased fracture toughness of the coating according to the invention is not yet understood. It is however assumed to be associated with stress conditions within the layers, the grain sizes, phase transitions, grain boundary phases, defect sizes and defect densities, deformations of the crystal lattice caused by integrating Me atoms, layer boundaries as well as layer thicknesses.
In an embodiment, the coating comprises several oxide layers consisting of single coats according to the invention.
In an embodiment the thicknesses of the single coats in an oxide layer consisting of single coats are each identical. In an embodiment the thicknesses of the single coats in the oxide layer consisting of single coats are 2 nm to 200 nm, preferably 3 nm to 50 nm, particularly preferably 4 nm to 10 nm. Through these layer thicknesses the fracture toughness is particularly high.
In an embodiment the oxide layer consists of 10 to 1000 single coats, preferably of 100 to 600 single coats, particularly preferably of 300 to 500 single coats. In particular the fracture toughness is increased with such a number of single coats.
In an embodiment the overall layer thickness of the oxide layer consisting of the single coats is from 0.1 μιτι to 8 μιτι, preferably 0.3 μιτι to 4 μιτι, particularly preferably 0.4 μιτι to 2 μιτι. It has been shown that the wear properties are positively affected by such layer thicknesses while this is not the case with smaller layer thicknesses and whereas larger layer thicknesses cause high compressive stresses.
In an embodiment the fraction of Me in the oxide layer consisting of the single coats is in the range of from 0.3 at.% to 5.4 at.%, preferably in the range of from 1 .3 at.% to 2.0 at.%. Particularly within these ranges an increase in fracture toughness is observable without the formation of further Me oxide phases.
In an embodiment Me is selected among Si, Ti, V, Zr, Mg, Fe, Cr and B, particularly preferably Me is Si. It has been shown that within a layer of aluminium oxide integrating one of the aforementioned further metals may significantly increas the fracture toughness in comparison to a layer of pure aluminium oxide. This could be shown in particular for Si.
In an embodiment the oxide layer consisting of the single coats is produced by means of sputtering, preferably dual magnetron sputtering or HIPIMS (high power impulse magnetron sputtering). These processes are special PVD processes not resulting in a formation of droplets, in particular in comparison to the arc PVD process. This has been proven to be particularly advantageous for the production of the oxide layer consisting of the single layers. A particular good adjustability for a respective use is possible through the changed microstructure, a different crystal structure and/or different stress conditions of the surface, caused by these production methods.
In an embodiment for the manufacture of the oxide layer consisting of the single coats at least one Al target and at least one AIMe target are used. This also encompasses the use of so-called segmented targets wherein one half corresponds to the Al target and the other half corresponds to the AIMe target. When applying the single coats such a target is mounted such that the separating line between the two halves of the target is parallel to the rotational axis of the substrate table. In an embodiment the AIMe target consists of from 1 at.% Me to 16 at.% Me and from 99 at.% Al to 84 at.% Al, preferably 4 at.% Me to 6 at.% Me and from 96 at.% Al to 94 at.% Al. The particularly preferred single coats of (Al x ,Me 1 . x ) 2 0 3 in the oxide layers with a low fraction of Me may be produced thereby.
In an embodiment between the base body and the oxide layer consisting of the single coats at least one further layer is present, being or comprising a nitride, preferably TiN, TiCN, TiAIN, AICrN, TiSiN, TiAISiN, TiAICrN. This layer has a high degree of hardness as well as a high modulus of elasticity and in combination with an oxide layer consisting of alternating single coats and arranged directly on top of it contriubutes to the wear reducing properties of the overall coating.
In an embodiment, the layer that is a nitride or comprises a nitride has a thickness of from 1 μιτι to 15 μιτι, preferably from 3 μιτι to 7 μιτι. Such layer thicknesses in combination with the layer consisting of single coats result in a particular good wear resistance.
In an embodiment several oxide layers consisting of single coats as described above are arranged on top each other, each separated through a further layer which is a nitride or comprises a nitride, preferably TiN, TiCN, TiAIN, AICrN, TiSiN, TiAISiN, TiAICrN.
In an embodiment the coating comprises 1 to 7 oxide layers consisting of single coats and 1 to 8 layers consisting of a nitride or comprising a nitride, preferably TiN, TiCN, TiAIN, AICrN, TiSiN, TiAISiN, TiAICrN. In an embodiment below the lowermost oxide layer consisting of single coats and on top of the uppermost oxide layer consisting of single coats one coat being or comprising a nitride is present, preferably TiN, TiCN, TiAIN, AICrN, TiSiN, TiAISiN, TiAICrN.
In an embodiment the oxide layer consisting of the single coats has a Vickers hardness in the range of from 1800 HV to 4000 HV, preferably of from 2000 HV to 3500 HV, particularly preferably of from 2600 HV to 3000 HV. It has been shown that oxide layers having such Vickers hardnesses are particularly wear resistant.
In an embodiment the single coats of (Al x ,Me 1 . x ) 2 0 3 of the oxide layer consisting of single coats are single phase or multi-phase. Preferably, the single coats consisting of (Al x ,Mei- x ) 2 0 3 of the oxid layer consisting of single coats are single phase.
In an embodiment the crystal structure of the coats of (Al x ,Me 1 . x ) 2 0 3 of the oxide layer consisting of single coats is equal to that of the single coats of Al 2 0 3 . In an embodiment the single coats of Al 2 0 3 of the oxide layer consisting of single coats are coats of Y aluminium oxide. In specific embodiments the crystal structure of the single coats consisting of (ΑΙ χ ,Μβι ) 2 θ3 has the same or a different crystal structure. Thus, in an embodiment, the single coats of Al 2 0 3 and the single coats of (Al x ,Me 1 . x ) 2 0 3 of the oxide layer consisting of single coats are both single phase and have both a γ crystal structure.
Further advantages, features and embodiments of the present invention will be described on the basis of the following examples.
Examples
Example 1 : Coating of substrates
For investigating the production of the oxide layers having alternating single coats and in order to compare these with known single layers of Al 2 0 3 , different coatings were applied to base bodies.
In all examples the same base bodies were used. These are base bodies having a geometry of S-15 in accordance with ISO naming, having a mirror polished surface as well as a proportion of Co of 10 wt.-% and 90 wt.-% WC.
In order to eliminate effects from underlying layers, with respect to the determination of fracture toughness multi-coat layers have been applied directly to a base body (substrate) and no further layers have been arranged above or below.
Experiment A: [AI 2 Q 2 - (AISi) 2 Q 2 l oxide layer
Onto the above described base body the following oxide layer has been applied:
[Al 2 0 3 - (AISi) 2 0 3 ] oxide layer having 360 essentially alternating single coats
PVD process: Dual magnetron sputtering (dMS)
Targets: Target 1 : Al; target size: 800x200 mm
Target 2: AISi where AI:Si is 95:5 (at.%); target size: 800x200 mm
Deposition: Temperature: 550°C
0.43 Pa argon partial pressure
Reactive gas: Oxygen (partial pressure: 4x10 "5 mbar)
Power (dMs): 30 kW
Operating point: 480 V Bias current: 6.5 A
Substrate bias voltage: 125 V unipolar (45 kHz, 10 offtime) The thickness of the single coats was about 4.4 nm.
The oxide layer of Experiment A was analyzed with XRD and only gamma phase peaks were detected. Both the Al 2 0 3 and (AISi) 2 0 3 single coats can therefore be concluded to be of single phase gamma structure.
Experiment B: ΑΙ?0 2 single layer
The production was - if not indicated otherwise - under the same conditions as in example A. However, two targets have been used, consisting exclusively of aluminium (Al):
Al 2 0 3 single layer
PVD process: Dual magnetron sputtering (dMS)
Targets: Target 1 : Al; target size: 800x200 mm
Target 2: Al; target size: 800x200 mm
Deposition:
Power (DMS): 20 kW
Operating point: 510 V
Bias current: 5.5 A
Example C: ΑΙ?0 2 single layer by the CVD process
For this comparative example instead using the PCD process for coating the body of hard metal, a conventional thermal CVD process has been applied.
A summary of the production conditions is provided in the table 1 below.
Table 1 :
Example 2: Comparison of properties of the coatings:
For comparing the properties of the coatings the following parameters have been measured: Fracture toughness:
Using a Vickers type indenter (a four-sided square-based pyramid having an included angle of 136°) has been pushed onto the surface for 20 s. The (maximum) load for the indentations (test load) was 200 N. The applied load increase and load decrease was 20 N/s without holding time. During the application of the load cracks were formed within the coating. Upon release of the load images were produced by means of scanning electron microscopy and the crack lengths \- \ to l 4 visible on the surface and extending from the four corners of the indentation, were measured.
A HPG 2500/1 apparatus from Gesellschaft fur Fertigungstechnik und Entwicklung Schmalkalden mbH was used for producing the indentations.
For each example from 5 to 1 1 Vickers indentations were produced. The crack length of the single cracks was determined by a commercially available software (AnalySIS docu from Olympus Soft Imaging Solutions GmbH) and the mean crack length (arithmetic average) l| aye r was calculated thereof.
The mean crack length l| aye r was used as a measure for the resistance against crack propagation of the hard material layer applied by means of PVD.
Vickers hardness:
The Vickers hardness was determined by means of nano indentation (load-depth graph). The apparatus used was a Helmut Fischer GmbH, Sindelfingen, Germany, Picodentor HM500. The maximum force used was 15 mN, the time period for load increase and load decrease was 20 seconds each and the holding time was 10 seconds. After having applied the load using the Vickers indenter as described above, the length of the diagonal lines di and d 2 of the projected cross-sectional area of the impressions were measured. Using the measures of the diagonal lines and calculating the mean diagonal (arithmetic average) the Vickers hardness was calculated.
Reduced modulus of elasticity:
The reduced modulus of elasticity was determined by means of nano indentation (load-depth graph) as described for determining the Vickers hardness. Thickness:
Determining the thickness was done using the calotte grinding. Thereby a steel ball was used having a diameter of 30 mm for grinding the dome shaped recess and further the ring diameter was measured.
The results of these measurements are summarized in the table 2 below: Table 2:
For determining the crack length the test load was set to be 200 N for these examples, as less load would lead to short cracks being difficult to measure and difficult to compare, while greater load caused spalling of the coat.