THERMALLY STABILIZED (Ti,Si)N LAYER FOR CUTTING TOOL INSERT

Abstract

A cutting tool insert includes a body of cemented carbide, cermet, ceramics, cubic boron nitride based material or high speed steel and a hard and wear resistant coating including at least one metal nitride layer. The coating includes at least one layer of a thermally stabilized cubic structured (Ti1−(x+z)SixMez)N phase with 0.04

Description

BACKGROUND OF THE INVENTION

The present invention relates to a cutting tool insert comprising of a body of a hard alloy of cemented carbide, cermet, ceramics, cubic boron nitride based material or high speed steel and a coating designed to be used in metal cutting applications generating high temperatures, particularly machining of super alloys and stainless steel. Said coating is composed of at least one layer of a thermally stabilized homogeneous cubic (Ti, Si, Me)N phase, where Me is one or more of the metal elements Y, Hf, Nb, Ta, Mo, W, Mn, Fe and Zn. The coating is grown by physical vapour deposition (PVD) and preferably by cathodic arc evaporation.

TiN has been widely used as hard layer on cutting tools due to its poor oxidation resistance at elevated temperatures, however, the focus has shifted towards more complex ternary and quaternary compounds, e.g. Ti—Al—N, Ti—Al—Si—N and Ti—Cr—Al—N with improved high temperature performance. For example, Ti—Al—Si—N has been reported as super hard, H>40 GPa due to a two phase structure consisting of crystalline phase of NaCl-type in combination with x-ray amorphous Si₃N₄ or SiN_X.

EP 1174528 discloses a multilayer-coated cutting tool insert. The first hard coating film is formed on the insert and a second hard coating film formed on the first hard coating film. The first hard coating film comprises one or more of Ti, Al and Cr, and one or more of N, B, C and O. The second hard coating film comprises Si and one or more metallic elements selected from the group consisting of metallic elements of Groups 4, 5 and 6 of the Periodic Table and Al, and one or more non-metallic elements selected from the group consisting of N, B, C and O.

EP 1736565 discloses a cuffing tool insert, solid end mill, or drill, comprising a body and a coating. The coating is composed of one or more layers of refractory compounds of which at least one layer comprises a cubic (Me, Si)X phase, where Me is one or more of the elements Ti, V, Cr, Zr, Nb, Mo, Hf, Ta and Al, and X is one or more of the elements N, C, O or B.

WO 2006/118513 discloses a cutting tool insert, solid end mill or drill, comprising a body and a coating. The coating is composed of a cubic C—(Me, Si,) N-phase without coexisting amorphous phase.

EP 1722009 discloses a cutting tool insert, solid end mill, or drill, comprising a body and a coating. The coating is composed of one or more layers of refractory compounds of which at least one layer comprises a h-Me1Me2X phase, where Me 1 is one or more of the elements V, Cr, Nb, and Ta and Me2 is one or more of the elements Ti, Zr, Hf, Al, and Si and X is one or more of the elements N, C, O or B.

EP 0588350 discloses a hard layer of Ti—Si—N composite material on a body is carried out by using a source of evaporation possessing a composition of Ti_aSi_b with a in the range of 75- 85 at % and b 15-25at %.

U.S. Pat. No. 6,033,768 discloses a hard coating consisting of a layer of a binary, ternary or quaternary TiAl based multicomponent material comprising nitride or carbonitride with an Al-content of 10 to 70 at %. The layer contains about 0.1 to 4 at % yttrium unevenly distributed over the entire layer.

JP 2004-338058 discloses a hard coating comprising a compound nitride layer of Ti, Si and Y. The layer has a concentration distribution structure wherein a maximum Si content and a minimum Si content exist in alternate repetition with a spacing of 0.01-0.1 μm. JP 2004-338008 and JP 2004-322279 disclose similar hard coatings comprising a compound (Ti,Si,Cr)N layer and (Ti, Si, Zr)N, respectively.

The trends towards dry-work processes for environmental protection, i.e., metal cutting operation without using cutting fluids (lubricants) and accelerated machining speed with improved process put even higher demands on the characteristics of the tool materials due to an increased tool cutting-edge temperature. In particular, coating stability at high temperatures, e.g., oxidation- and wear-resistance have become even more crucial.

It is an object of the present invention to provide a thermally stabilized (Ti,Si)N coated cutting tool yielding improved performance in metal cutting applications at elevated temperatures.

Surprisingly, it has been found that by introducing small amounts of the metal elements Y, Hf, Nb, Ta, Mo, W, Mn, Fe and Zn in (Ti,Si)N layers leads to improved high temperature metal cutting properties.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 X-ray diffraction patterns from (Ti_1−xSi_x)N layers as function of the Si content (x).

FIG. 2 Hardness (H) of (Ti_1−xSi_x)N layers as a function of the Si content (x) as obtained at room temperature, before and after heat treatment at 1000° C., 2 h.

FIG. 3 X-ray diffraction patterns from (Ti_1−xSi_x)N, x=0.09 at room temperature (I) and after heat treatment at 1000° C., 2 h (II).

FIG. 4 Cross-sectional transmission electron micrograph from a cubic (Ti_1−(x+z)Si_xY_z)N layer (x=0.09,z=0.02) according to the invention showing (A) cemented carbide and (B) layer.

DETAILED DESCRIPTION OF THE INVENTION

According to the present invention, there is provided a cutting tool for machining by chip removal comprising a body of a hard alloy of cemented carbide, cermet, ceramics, cubic boron nitride based material or high speed steel onto which a wear and high temperature resistant coating is deposited composed of at least one cubic structured (Ti_1−(x+z)Si_xMe_z)N layer 0.04<x<0.20, preferably 0.06<x<0.12 and 0<z<0.10, preferably 0.005<z<0.05, with a constant elemental composition throughout the layer, where Me is one or more of the metal elements Y, Hf, Nb, Ta, Mo, W, Mn, Fe and Zn, preferably Y, Nb, Mo and Fe. The layer has a thickness of 0.5 to 10 μm preferably 0.5 to 5 μm.

Said layer has a compressive stress level of −6.0<σ<−0.5 GPa, preferably of −4.0<σ<−1.0 GPa.

Said layer has a hardness at room temperature of 28<H<44, preferably 33<H<40 GPa.

The composition, x and z, of (Ti_1−(x+z)Si_xMe_z)N is determined by, e.g., EDS or WDS.

Said body may be coated with an inner single- and/or multilayer coating of, e.g., TiN, TiC, Ti(C,N) or (Ti,Al)N, preferably (Ti,ADN and/or an outer single- and/or multilayer coating of, e.g., TiN, TiC, Ti(C,N) or (Ti,Al)N, preferably (Ti,AON with a total coating thickness of 1 to 20 μm, preferably 1 to 10 μm and most preferably 2 to 7 μm according to prior art.

The deposition method for the coatings of the present invention is based on cathodic arc evaporation of an alloyed or composite cathode under the following conditions; c-(Ti,Si,Me)N layers are grown using Ti+Si+Me-cathodes with a composition expressed as Ti_1−(x+z)Si_xMe_z with 0.04<x<0.20, preferably 0.06<x<0.12 and 0<z<0.10, preferably 0.005<z<0.05, where Me is one or more of the metal elements Y, Hf, Nb, Ta, Mo, W, Mn, Fe and Zn, preferably Y, Nb, Mo and Fe. The evaporation current is between 50 A and 200 A. The layers are grown in an Ar+N₂ atmosphere, preferably in a pure N₂ atmosphere at a total pressure of 0.5 Pa to 7.0 Pa, preferably 1.5 Pa to 5.0 Pa. The bias is −10 V to −80 V, preferably −40 V to −60V. The deposition temperature is between 400° C. and 700° C., preferably between 500 and 600° C.

The invention also relates to the use of cutting tool inserts according to the above for machining of super alloys and stainless steel at cutting speeds of 50-400 m/min, preferably 75-0 300 m/min, with an average feed, per tooth in the case of milling, of 0.08-0.5 mm, preferably 0.1-0.4 mm depending on cutting speed and insert geometry.

EXAMPLE 1

Cemented carbide inserts with composition 94 wt % WC-6 wt % Co were used.

Before deposition, the inserts were cleaned in ultrasonic baths of an alkali solution and alcohol. The system was evacuated to a pressure of less than 2.0×10⁻³ Pa, after which the inserts were sputter cleaned with Ar ions. (Ti_1−xSi_x)N layers, 0<x<0.20 were grown by cathodic arc evaporation using cathodes with a composition varying between pure Ti and

_0.75Si_0.25, 63 mm in) diameter at 500° C. The layers were deposited in pure N₂ atmosphere at a total pressure of 4 Pa, using a bias of −50 V and an evaporation current of 60 A to a total thickness of about 3 μm.

The composition, x, of the (Ti_1−xSi_x)N layers was estimated by energy dispersive spectroscopy (EDS) analysis using a LEO Ultra 55 scanning electron microscope with a Thermo Noran EDS detector operating at 10 kV. The data were evaluated using a Noran System Six (NSS ver 2) software.

X-ray diffraction (XRD) patterns of the as-deposited (Ti_1−xSi_x)N layers were obtained using Cu K alpha radiation and a θ-2θconfiguration as function of the Si content (x), see FIG. 1, corresponding to a NaCl structure of all layers.

Residual stresses, σ, of the (Ti_1−xSi_x)N layers were evaluated by XRD measurements using the sin²ψ method (see e.g. I. C. Noyan, J. B. Cohen, Residual Stress Measurement by Diffraction and Interpretation, Springer-Verlag, N.Y., 1987). The measurements were performed using CuKΔ-radiation on the (Ti_1−xSi_x)N (422)-reflection. The residual stress values were within −4.0<σ<−2.0 GPa for the different layers as evaluated using a Possion's ratio of v=0.25 and Young's modulus of E=450 GPa.

In order to simulate the apparent heat effect that occur during metal machining, controlled experiments by isothermal heat treatments were made of the inserts in inert Ar atmosphere at 1000° C. for 120 min.

Hardness data was estimated by the nanoindentation technique of the layers after mechanical polishing of the surface using a MTS Nanolndenter XP system with a Berkovich diamond tip with a maximum tip load of 25 mN. FIG. 2 shows the hardness (H) of (Ti_1−xSi_x)N layers as a function of the Si content (x) as obtained at room temperature, before and after heat treatment at 1000° C. for 2h. Optimum hardness is obtained for the (Ti₁₋Si_x)N layer with x=0.09 corresponding to the best layer composition for metal machining applications.

FIG. 3 shows the XRD pattern of a (Ti_1−xSi_x)N layer, x=0.09, before (I) and after (II) heat treatment at 1000° C. using CuKa-radiation and a θ-2θconfiguration. The heat treatment has no effect on the NaCl structure.

EXAMPLE 2

Grade A: Inserts from example 1 with a (Ti_1−xSi_x)N, x=0.09 composition having a hardness of 39 GPa and a compressive stress level of −3.1 GPa were used.

EXAMPLE 3

Grade B: Example 1 was repeated using a Ti₁₋(_x+z)Si_xY_z cathode, x=0.10 and z=0.03.

The composition of the resulting (Ti_1−(x+z)Si_xY_z)N layer was x=0.09 and z=0.02. The hardness of the as-deposited layer was 38 GPa and the residual stress level −3.5 GPa.

FIG. 4 shows a cross-sectional transmission electron micrograph from a cubic (Ti_1−xSi_xY_z)N layer (x=0.09, z=0.02), which exhibits a dense, columnar and homogenous microstructure.

EXAMPLE 4

Grade C: Example 1 was repeated using a Ti_1−(x+z)-Si_xNb_z cathode, x=0.10 and z=0.06.

The composition of the resulting Ti_1−(x+z)Si_xNb_z)N layer was x=0.10 and z=0.05. The hardness of the as-deposited layer was 38 GPa and the residual stress level −3.1 GPa.

EXAMPLE 5

Grade D: Example 1 was repeated using a Ti_1−(x+z)Si_xMo_z cathode, x=0.10 and z=0.03.

The composition of the resulting Ti_1−(x+z)Si_xMo_z)N layer was x=0.08 and z=0.03. The hardness of the as-deposited layer was 36 GPa and the residual stress level −2.1 GPa.

EXAMPLE 6

Grade E: Example 1 was repeated using a Ti_1−(x+z)Si_xFe_x cathode, x=0.08 and z=0.05.

The composition of the resulting Ti_1−(x+z)Si_xFe_z)N layer was x=0.08 and z=0.04. The hardness of the as-deposited layer was 38 GPa and the residual stress level −2.5 GPa.

EXAMPLE 7

Grade F: Example 1 was repeated using a Ti_1−(x+z)Si_xY_z/2Fe_z/2 cathode, x=0.10 and z=0.04.

The composition of the resulting Ti_1−(x+z)Si_xY_z/2Fe_z/2 layer was x=0.09 and z=0.04. The hardness of the as-deposited layer was 36 GPa and the residual stress level −2.2 GPa.

EXAMPLE 8

Grades A-F were tested in hardened steel according to:

Geometry: CNMG120408-MF1

Application: Continuous turningWork piece matererial: AISI 5115Cutting speed: 180 m/minFeed: 0,15 mm/rev

Depth of cut: 1 mm

Tool life criteria, flank wear (vb) >0,3 mm

      Tool life
Grade (min)
A     16.1
B     20.6
C     17.5
D     18.2
E     17.2
F     19.2

EXAMPLE 9

Grades A-F were tested in super alloy according to:

Geometry: CNMG120412-MR3

Application: Continuous turningWork piece material: Inconel 718Cutting speed: 90 m/minFeed: 0,2 mm/rev

Depth of cut: 0,5 mm

Tool life criteria, flank wear (vb) >0,2 mm

      Tool life
Grade (min)
A     8.5
B     10.5
C     9.3
D     9.9
E     9.1
F     10.2

Claims

1. Cutting tool insert comprising a body of cemented carbide, cermet, ceramics, cubic boron nitride based material or high speed steel and a hard and wear resistant coating comprising at least one metal nitride layer characterised in that said layer is a cubic structured (Ti1−(x+z)SixMez)N with 0.04<x<0.20, preferably 0.06<x<0.12 and 0<z<0.10, preferably 0.005<z<0.05 with a constant elemental composition throughout the layer, where Me is one or more of the metal elements Y, Hf, Nb, Ta, Mo, W, Mn, Fe and Zn, preferably Y, Nb, Mo and Fe with a layer thickness of 0.5 to 10 μm, preferably 0.5 to 5 μm.

2. Cutting tool insert according to claim 1 characterised in that said layer has a hardness at room temperature of 28<H<44, preferably 33<H<40 GPa.

3. Cutting tool insert according to claim 1 characterised in that said layer has a compressive stress level of −6.0<σ<−0.5 GPa, preferably of −4.0<σ<−1.0 GPa.

4. Cutting tool insert according to claim 1 characterised in that said layer has been deposited with PVD, preferably cathodic arc evaporation.

5. Cutting tool insert according to claim 1 characterised in that said body is coated with an inner single- and/or multilayer coating of, e.g., TiN, TiC, Ti(C,N) or (Ti,Al)N, preferably (Ti,Al)N and/or an outer single- and/or multilayer coating of, e.g., TiN, TiC, Ti(C,N) or (Ti,Al)N, preferably (Ti,Al)N, to a total coating thickness of 1 to 20 μm, preferably 1 to 10 μm and most preferably 2 to 7 μm according to prior art.

6. Method of making a cutting tool insert according to claim 1 characterised in that said layer is a cubic (Ti,Si,Me)N phase grown by cathodic arc evaporation, with a thickness of 0.5 to 10 μm, preferably 1 to 5 μm using a Ti+Si+Me-cathode with a composition expressed as Ti1−(x+z)SixMez with 0.04<x<0.20, preferably 0.06<x<0.12 and 0<z<0.10, preferably 0.005<z<0.05, where Me is one or more of the metal elements Y, Hf, Nb, Ta, Mo, W, Mn, Fe and Zn, preferably Y, Nb, Mo and Fe, and with an evaporation current between 50 A and 200 A depending on the cathode size, in an Ar+N2 atmosphere, preferably in pure N2 at a total pressure of 0.5 Pa to 7.0 Pa, preferably 1.5 Pa to 5.0 Pa, with a bias between −10 V and −80 V at a temperature between 400° C. and 700°.

7. Method of using a cutting tool inserts according to claim 1 for machining of stainless steel and super alloys at cutting speeds of 50-400 m/min, preferably 75-300 m/min, with an average feed, per tooth in the case of milling, of 0.08-0.5 mm, preferably 0.1-0.4 mm depending on cutting speed and insert geometry.