CN102528104B - Cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material having high peeling resistance - Google Patents
Cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material having high peeling resistance Download PDFInfo
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Abstract
The invention provides a cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material, which develops good property of peeling resistance when high-rigidity steel undergoes high-speed cutting. The cutting tool is formed by forming hard coating layer on the surface of CBN-based ultra-pressure sintered body whose cubic boron nitride is 50-85 capacity%. The hard coating layer comprises a lower layer and an upper layer whose average layer thickness is 1.5-3Mum. The lower layer has a complex nitride layer satisfying a formula: [Ti1-XA1X]N, wherein in terms of atomic ratio, X is 0.30-0.60. The upper layer has a thin layer A and a thin layer B which is alternative and has 0.03-0.3Mum average layer thickness. The thin layer A includes a complex nitride layer satisfying a formula: [Ti1-XA1X]N, and the thin layer B includes TiN layer. The surface roughness, residual stress and nano-indentation hardness are set to be a predetermined value.
Description
Technical field
The present invention relates to a kind of Surface coating cubic boron nitride base ultra-high pressure sintered material cutting tool (following, be called coated cBN base sintering instrument), the hard coating layer of this cutting element possesses excellent high temperature hardness, elevated temperature strength, the adhesiveness of heat resistance and excellence, even if therefore at steel alloy, when using in the high-speed cutting processing of the glass hard steels such as the quenching material of bearing steel, also excellent peel resistance can be played, and the polished surface precision of the excellence of workpiece also can be maintained through long-time cutting, it forms hard coating layer on the surface of the cutting element matrix be made up of cubic boron nitride base ultra-high pressure sintered material.
Background technology
Usually, there will be a known following instrument in coated cBN base sintering instrument: in the turnery processing of the workpiece such as various steel or cast iron, be detachably arranged on lathe tool leading section and the indexable insert tip, throw away tip used; Or with indexable insert tip, throw away tip is detachably installed and the face that is used in cut process or the solid formula slotting cutter of slot machining and step processing etc. identical carry out the indexable slotting cutter etc. of machining.
And, as coated cBN base sintering instrument, there will be a known (following by various cubic boron nitride base ultra-high pressure sintered material, being called cBN based sintered fuel) the surperficial evaporation of the tool body that forms forms the complex nitride ([Ti of Ti nitride (TiN) layer, Ti and Al, Al] N) the coated cBN base sintering instrument of the surface coating layer such as layer, also these instruments known are for the machining of such as various steel or cast iron etc.
In addition, also known described coated cBN base sintering instrument is by following steps manufacture: what such as illustrate using brief description in FIG loads described cutting element matrix in a kind of arc ion plating apparatus of physical vapor deposition device, with heater by be heated to such as 500 DEG C in device state under, at the electric current comprising metal Ti or there is additional such as 90A respectively between the cathode electrode (evaporation source) of Ti-Al alloy of predetermined composition and anode electrode to produce arc discharge, in device, import nitrogen as reacting gas simultaneously, and be set as the reaction atmosphere of such as 2Pa, on the other hand, under the condition of the bias voltage to the additional such as-100V of described cutting element matrix, TiN layer or [Ti is formed at the surperficial evaporation of described cutting element matrix, Al] layer that is grouped into of the desired one-tenth such as N layer is (such as, referenced patent document 1).In addition, also there will be a known adjustment and be formed at the surface roughness of the hard coating layer on the surface of described cutting element matrix and residual stress to improve the surface-coated cutting tool (such as, referenced patent document 2) of wearability, fracture resistance.
Patent document 1: Japanese Patent Publication 2007-190668 publication
Patent document 2: Japanese Patent Publication 2006-263857 publication
The FAization of cutting apparatus is surprising in recent years, on the other hand to the saving labourization of machining and the requirement of energy-saving and cost degradation strong, with this, machining has requirement except except common machining condition, the tendency of the machining also under more high-speed condition, but in described coating tool in the past, special problem can not be produced when the various steel of machining or cast iron at typical condition.But, when the high-speed and continuous this being used in steel alloy, the quenching material etc. of bearing steel has the glass hard steel of the higher hardness of Vickers hardness (C scale) more than 50 is cut or high rate intermittent cuts, because the adhesive strength of cBN based sintered fuel and hard coating layer is insufficient, therefore point of a knife is peeling, there is the problem of working durability decline and so on.
Therefore, the present inventor etc. consider from such as above-mentioned viewpoint, especially to cut or high rate intermittent cuts (following in the high-speed and continuous of the glass hard steel such as quenching material of steel alloy, bearing steel to develop, only being called " high-speed cutting ") hard coating layer plays the coated cBN base sintering instrument of excellent peel resistance and is studied in processing, obtains the result of study shown in following (a) ~ (d).
A () forms the complex nitride ([Ti of Ti and Al of hard coating layer
1-Xal
x] N) and layer containing Al ratio X (atomic ratio) value be 0.30 ~ 0.60 scope in there is predetermined heat resistance, high temperature hardness and elevated temperature strength, and wearability required under having usual Cutting and machining conditions, but at blade part with very big heating or apply in the high-speed cutting processing of glass hard steel of intermittence or the larger mechanicalness load of impact to blade part, owing to comprising the complex nitride ([Ti of Ti and Al simultaneously
1-Xal
x] N) elevated temperature strength of hard coating layer of layer is not enough, therefore produce border Abnormal damage at the boundary member of blade, and therefore cannot maintain the polished surface precision of workpiece, within a short period of time reaches service life.
B () on the other hand, Ti nitride (TiN) layer has excellent elevated temperature strength, impact strength, but because heat resistance, high temperature hardness are not very abundant, therefore with larger heating and apply larger mechanicalness load glass hard steel high-speed cutting processing in, even if only form hard coating layer by Ti nitride (TiN) layer, be also not really and possess sufficient wearability.
If c () is [Ti with heat resistance, high temperature hardness and predetermined high temperature intensity of 30 ~ 60 atom % with the state alternately laminated above-mentioned (a) that average for respective one deck thickness is set as the thin layer of 0.03 ~ 0.3 μm containing Al ratio X
1-Xal
x] N (wherein, with atomic ratio measuring, X is 0.30 ~ 0.60) layer is (below, be called thin layer A), although with heat resistance compared with described thin layer A, but high temperature hardness is poor has excellent elevated temperature strength on the other hand, Ti nitride (TiN) layer (hereinafter referred to as thin layer B) of impact strength forms the upper layer of hard coating layer, then the hard coating layer of this alternatively layered structure possesses the heat resistance of the excellence that thin layer A has, high temperature hardness, and have more excellent elevated temperature strength and impact strength that thin layer B has concurrently, its result improves peel resistance.
D () is on above-mentioned hard film layer surface, further enforcement process for treating surface, such as wet blast or peening process etc., thus surface roughness, residual stress and nano-indentation hardness in the rear knife face of hard coating layer, rake face and cutting edge reconditioning portion can be made to become predetermined value respectively, can suppress thus to produce tipping, its result improves wearability.
Summary of the invention
The present invention completes based on above-mentioned result of study, and it has following feature:
The Surface coating cubic boron nitride base ultra-high pressure sintered material cutting tool of a kind of long-term performance peel resistance, wearability, it is the surperficial evaporation formation hard coating layer of the cutting element of the cubic boron nitride base high-pressure sintered body of 50 ~ 85 capacity % at the content comprising cubic boron nitride, wherein
Described hard coating layer comprises:
A () lower layer, has the average thickness of 1.5 ~ 3 μm, and comprise and meet composition formula: [Ti
1-Xal
x] the composite nitride nitride layer of Ti and Al of N (wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60); And
B () upper layer, makes to meet composition formula: [Ti
1-Xal
x] N (wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60) the composite nitride nitride layer of Ti and Al and each thickness of Ti nitride (TiN) layer become 0.03 ~ 0.3 μm to come alternately laminated in average thickness, and formed at outermost layer and there is the average thickness of 0.3 ~ 2 μm and meet composition formula: [Ti
1-Xal
x] the composite nitride nitride layer of Ti and Al of N (wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60) forms, the average thickness of total of this upper layer is 0.5 ~ 3 μm, and,
C the surface roughness Ra on () hard coating layer surface is 0.08 ~ 0.20 μm in rear knife face and rake face, be 0.07 ~ 0.10 μm in cutting edge reconditioning portion,
D the residual stress of the TiAlN of () hard coating layer is-1 ~-2GPa in rear knife face and rake face, be-1.5 ~-3.0GPa in cutting edge reconditioning portion, and residual stress (rear knife face, rake face) is greater than residual stress (cutting edge reconditioning portion)
(e) outermost layer TiAlN with nano-indentation hardness during 100mg load measurement in rear knife face and rake face for 30 ~ 38GPa, be 33 ~ 50GPa in cutting edge reconditioning portion, and nano-indentation hardness (rear knife face, rake face) is less than nano-indentation hardness (cutting edge reconditioning portion).
Then, the cooperation composition of the cBN based sintered fuel of the cutting insert body forming this instrument and the composition of hard coating layer are limited to coated cBN base sintering instrument of the present invention, the reason of thickness is described.
The cooperation composition of the cBN based sintered fuel of (a) cutting insert body
If the content of cubic boron nitride is more than 85 capacity %, then the agglutinating property of boron nitride-base itself declines, and its result easily produces tipping on the cutting edge.On the other hand, if be less than 50 capacity %, then the wearability of desired excellence cannot be guaranteed.Therefore, the content of cubic boron nitride is defined as 50 ~ 85 capacity %.
The lower layer of (b) hard coating layer
Owing to forming the complex nitride ([Ti of Ti and Al of the lower layer of hard coating layer
1-Xal
x] N) Ti composition in layer contributes to maintaining elevated temperature strength, Al composition contributes to improving high temperature hardness and heat resistance, therefore forms the complex nitride ([Ti of Ti and Al of the lower layer of hard coating layer
1-Xal
x] N) and layer for possessing the layer of predetermined elevated temperature strength, high temperature hardness and heat resistance, substantially undertake and guarantee that the high-speed cutting of the glass hard steels such as hardened steel adds the effect of the wearability of the blade part in man-hour.Wherein, if containing Al ratio X more than 60 atom %, then the high temperature hardness of lower layer and heat resistance improve, but elevated temperature strength declines along with the relative minimizing containing Ti ratio, and easily produces tipping, on the other hand, if be less than 30 atom % containing Al ratio X, then high temperature hardness and heat resistance decline, and its result can see that wearability declines, and therefore will be defined as 0.30 ~ 0.60 containing Al ratio X value.
And, when the average thickness of lower layer is less than 1.5 μm, heat resistance, high temperature hardness and the elevated temperature strength that cannot have hard coating layer imparting for a long time itself and become life tools shorten reason, on the other hand, if its average thickness is more than 3 μm, then easily can produce tipping, therefore its average thickness is defined as 1.5 ~ 3 μm.
The upper layer of (c) hard coating layer
(I) the thin layer A of upper layer
Form the complex nitride ([Ti of Ti and Al of the thin layer A of upper layer
1-Xal
x] N) layer (wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60) be in fact identical with lower layer layer, possess predetermined heat resistance, high temperature hardness and elevated temperature strength, and have and guarantee that the high-speed cutting of the glass hard steels such as hardened steel adds the effect of the wearability of the blade part in man-hour.
(II) the thin layer B of upper layer
The main purpose comprising the thin layer B of Ti nitride (TiN) layer is, in the upper layer of alternatively layered structure comprising thin layer A and thin layer B, makes up the not enough characteristic of thin layer A (elevated temperature strength, impact strength).
As described, the thin layer A of upper layer is the layer with predetermined heat resistance, high temperature hardness and elevated temperature strength, but in the larger mechanicalness load of applying and with in the high-speed cutting processing of the thermogenetic glass hard steel of height, its elevated temperature strength, impact strength be cannot say for sure very abundant, therefore produce border Abnormal damage at the boundary member of the point of a knife of blade.
Therefore, the thin layer B and thin layer A that comprise Ti nitride (TiN) layer with excellent elevated temperature strength and impact strength are replaced arranging to form alternatively layered structure, the elevated temperature strength deficiency and the impact strength that make up adjacent thin layer A are thus not enough, overall as upper layer, Not a hair of one's head shall be touched, and become homeless heat resistance, high temperature hardness, the elevated temperature strength and being formed of stating the excellence that thin layer A has possesses the upper layer of more excellent elevated temperature strength that described thin layer B has and impact strength.
Ti nitride (TiN) layer possesses excellent elevated temperature strength and impact strength, and have and applying larger mechanicalness load and high-speed cutting with glass hard steels such as the thermogenetic hardened steel of height adds man-hour, prevent the effect of the border Abnormal damage that the boundary member of the point of a knife of blade produces.
(III) the thin layer A of upper layer and the average thickness of one deck of thin layer B
When the thin layer A of upper layer and the average thickness of thin layer B one deck are separately less than 0.03 μm, the characteristic of the excellence that each thin layer possesses cannot be played, its result cannot guarantee excellent high temperature hardness to upper layer, elevated temperature strength and heat resistance and more excellent elevated temperature strength and impact strength, if and the average thickness of respective one deck is more than 0.3 μm, the then shortcoming that has of each thin layer, namely be elevated temperature strength during thin layer A, be heat resistance when the deficiency of impact strength and thin layer B, the deficiency of high temperature hardness is apparent in layer partly, produce the stripping of blade point of a knife thus, or wearing and tearing rapid progression, therefore the average thickness of respective one deck is defined as 0.03 ~ 0.3 μm.
Namely, thin layer B is the layer in order to arrange the upper layer more excellent elevated temperature strength of imparting and impact strength, if but thin layer A, the average thickness of thin layer B one deck is separately in the scope of 0.03 ~ 0.3 μm, then comprise the upper layer of the alternatively layered structure of thin layer A and thin layer B just as possessing excellent heat resistance, high temperature hardness and more excellent elevated temperature strength, 1 layer of impact strength equally plays a role, if but thin layer A, the average thickness of thin layer B one deck is separately more than 0.3 μm, the then elevated temperature strength of thin layer A, the deficiency of impact strength or the heat resistance of thin layer B, high temperature hardness deficiency is apparent in layer partly, upper layer cannot present the good characteristic as 1 layer as a whole, therefore by thin layer A, the average thickness of thin layer B one deck is separately defined as 0.03 ~ 0.3 μm.
The upper layer that the average thickness of one deck comprising thin layer A and thin layer B is set to the alternatively layered structure within the scope of 0.03 ~ 0.3 μm is formed on lower layer surface, can obtain having concurrently the hard coating layer of excellent heat resistance, high temperature hardness and more excellent elevated temperature strength and impact strength thus, its result can prevent when the high-speed and continuous machining of the glass hard steels such as hardened steel or high rate intermittent machining the Abnormal damage that the boundary member of the point of a knife of blade produces.
(IV) outermost layer of upper layer and its average thickness
In coated cBN base sintering instrument of the present invention, if the thickness of outermost layer TiAlN is less than 0.3 μm, then cannot obtain desired wearability.And sometimes produce different interference colours respectively knifeedge because of the difference of the thickness of the clad of outmost surface, instrument outward appearance becomes irregular.Now, as the outermost layer of upper layer, instrument outward appearance can be prevented irregular by complex nitride (TiAlN) layer of thicker ground evaporation formation Ti and Al.Further, if its average thickness is 2 μm to the maximum, then can fully prevent outward appearance irregular, therefore the average thickness of complex nitride (TiAlN) layer of Ti and Al be defined as 0.3 ~ 2 μm.
(V) the average thickness of the total of upper layer
And, when upper layer the average thickness of total (namely, add up to the thickness of the average thickness forming the thin layer A of alternatively layered structure and each layer of thin layer B and add up to the thickness of outermost average thickness) when being less than 0.5 μm, sufficient heat resistance, high temperature hardness, elevated temperature strength and impact strength required in the high-speed cutting processing of the glass hard steels such as hardened steel cannot be given to upper layer, become the reason shortened life tools, if its average thickness is more than 3 μm on the other hand, then easily produce tipping, therefore preferably it adds up to average thickness to be set to 0.5 ~ 3 μm.
(VI) surface roughness Ra on hard coating layer surface
The surface roughness Ra on hard coating layer surface is set in rear knife face and rake face to be less than 0.08 μm be because can involve the rising of manufacturing cost, therefore not preferred, if more than 0.20 μm, then the cutting resistance change of epithelial surfaces produces tipping greatly and easily, is therefore defined as 0.08 ~ 0.20 μm.Further, be set to that to be less than 0.07 μm be because can involve the rising of manufacturing cost in cutting edge reconditioning portion, therefore preferred, if more than 0.10 μm, then the cutting resistance of epithelial surfaces becomes and produces tipping greatly and easily, is therefore defined as 0.07 ~ 0.10 μm.
(VII) residual stress of the TiAlN of hard coating layer
If the residual stress of the TiAlN of hard coating layer is less than-1GPa in rear knife face and rake face, then cannot obtain desired hardness and wearability declines, therefore not preferred, if exceed-2GPa, then in high capacity is cut, easily inner at epithelium or epithelium and matrix interface produces and chaps, and produces tipping.Therefore ,-1 ~-2GPa is defined as.Further, if be less than-1.5GPa in cutting edge reconditioning portion, then desired hardness cannot be obtained and wearability declines, therefore not preferred, if exceed-3.0GPa, then in high capacity is cut, easily inner at epithelium or epithelium and matrix interface produces and chaps, and produces tipping.Therefore ,-1.5 ~-3.0GPa is defined as.In addition, if-1 ~-2GPa and-1.5 ~-3.0GPa, and the residual stress of rear knife face and rake face is less than the residual stress in cutting edge reconditioning portion, then easily produce the tipping in cutting edge reconditioning portion, be therefore defined as residual stress (rear knife face, rake face) and be greater than residual stress (cutting edge reconditioning portion).By the residual stress in rear knife face, rake face and cutting edge reconditioning portion is set to above-mentioned relation, the stress in the cutting edge reconditioning portion produced when can relax cutting thus, and when can suppress to cut, cutting resistance becomes the stripping in maximum cutting edge reconditioning portion.
(VIII) outermost layer TiAlN with nano-indentation hardness during 100mg load measurement
Outermost layer TiAlN in rear knife face and rake face, be less than 30GPa with the nano-indentation hardness when 100mg load measurement time, cannot obtain wearability and improve effect, therefore preferred, if more than 38GPa, then wearability improves, but easily produces tipping.Therefore, 30 ~ 38GPa is defined as.Further, when being less than 33GPa in cutting edge reconditioning portion, cannot obtaining wearability and improve effect, therefore not preferred, if more than 50GPa, then wearability improves, but easily produces tipping.Therefore, 33 ~ 50GPa is defined as.In addition, if 30 ~ 38GPa, 33 ~ 50GPa and the nano-indentation hardness of rear knife face and rake face are greater than the nano-indentation hardness in cutting edge reconditioning portion, then easily produce the tipping in cutting edge reconditioning portion, be therefore defined as nano-indentation hardness (rear knife face, rake face) and be less than nano-indentation hardness (cutting edge reconditioning portion).By the nano-indentation hardness in rear knife face, rake face and cutting edge reconditioning portion is set to above-mentioned relation, impact when can relax cutting thus in cutting edge reconditioning portion, and when can suppress to cut, cutting resistance becomes the stripping in maximum cutting edge reconditioning portion.
At this, the Using Nanoindentation obtaining nano-indentation hardness is described.Using Nanoindentation is the one of the hardness test described in detail in document " ト ラ イ ボ ロ ジ ス ト, the 47th volume, No. 3, (2002) p177 ~ 183 (tribology; the 47th volume; No. 3, (2002) p177 ~ 183) ".Nu Shi (ヌ mono-プ) hardness determination in the past or Vickers (PVC Star カ mono-ス) hardness determination obtain hardness from the indentation shape after press-in, but Using Nanoindentation is the method obtaining hardness or Young's modulus from the relation of load during press-in pressure head and the degree of depth.
Fig. 3 illustrates these test methods.As in the hardness determination in the past of Vickers hardness or Knoop hardness, owing to artificially measuring with light microscope, if therefore indentation shape not quite, cannot measure.Therefore, as shown in (B) of Fig. 3, the press-in load of increase pressure head 30 of having to, and the width W increasing impression measures.But at this moment because impression is additional to the both sides of coating film 20 and base material 10, therefore obtain the hardness affected by base material.
In contrast, obtained the hardness being only coating film of the impact without base material in the present invention by Using Nanoindentation.Specifically, as shown in (A) of Fig. 3, with become the thickness of coating film 20 about less than 1/10 the mode 100mg load press-in pressure head 30 of the degree of depth, remove the impact of base material 10 and carry out the mensuration of hardness.Such as, when the outermost hardness of mensuration 1 μm, preferred compression distance is set to below 100nm.Owing to mechanically obtaining the degree of depth in Using Nanoindentation, even if therefore also can with high accuracy measure under the such as above-mentioned less degree of depth.Pressure head 30 is only pressed into maximum compression distance hmax, and from hmax and carry calculation hardness etc.If elimination capacity, then only have elastic part to recover former state, therefore depth of cup becomes and is shallower than hmax.
Due to according to the impact by the concavo-convex or average grain diameter on coating film surface, residual stress and coating film thickness of the hardness of Using Nanoindentation, therefore different from hardness in the past, its value according to circumstances has sizable deviation.But, be on one of cutting ability factor bringing impact according to the outermost hardness of the coated cutting tool of indentation method.
When being process for treating surface, such as, when being the process according to wet blast, carry out under such as following condition.
The expulsion pressure of sandblasting is set to 0.1 ~ 0.15MPa, and injecting time is set to 1 ~ 5sec, this is repeated 3 ~ 10 times.If pressure is less than 0.1MPa, time is less than 1sec or number of repetition is less than 2 times, then the effect of sandblasting is more weak, the peel resistance that cannot obtain in the rear knife face of hard coating layer, rake face and cutting edge reconditioning portion improves effect, if and pressure is greater than 0.15MPa, time is longer than 5sec, number of repetition is more than 10 times, surface roughness then in the rear knife face of hard coating layer, rake face and cutting edge reconditioning portion, residual stress, nano-indentation hardness cannot obtain predetermined relation, therefore cannot obtain peel resistance and improve effect.In addition, the slurry used in sandblasting uses alumina particle, and particle diameter is 220 ~ No. 1500, slurry concentration is 15 ~ 60wt%.
Coated cBN base sintering instrument of the present invention comprises upper layer and lower layer due to hard coating layer, the upper layer of hard coating layer is set to the alternatively layered structure of thin layer A and thin layer B, and respectively according to rear knife face, rake face and cutting edge reconditioning portion specify the surface roughness of hard coating layer, residual stress, nano-indentation hardness, thus have excellent heat resistance concurrently, high temperature hardness, elevated temperature strength and impact strength, even if therefore especially as steel alloy, the glass hard steels such as the quenching material of bearing steel produce with high heat and in machining under the harsh conditions that high-speed and continuous blade part being applied to the mechanicalness load of intermittence or impact is cut or high rate intermittent cuts and so on, also can not be peeling in described hard coating layer, excellent wearability can be played for a long time, and maintain the polished surface precision of the excellence of workpiece.
Accompanying drawing explanation
Fig. 1 represents the arc ion plating apparatus for the formation of the hard coating layer forming coated cBN base sintering instrument of the present invention, and wherein, (a) is schematic top, (b) is concise and to the point front view.
Fig. 2 is the brief description figure of common arc ion plating apparatus.
The key diagram that (A) of Fig. 3 is Using Nanoindentation, (B) is the key diagram of hardness determination in the past.
Detailed description of the invention
Then, by embodiment, coated cBN base sintering instrument of the present invention is specifically described.
[embodiment]
As material powder, prepare cubic boron nitride (cBN) powder of the average grain diameter all had within the scope of 0.5 ~ 4 μm, titanium nitride (TiN) powder, Al powder and aluminium oxide (Al
2o
3) powder, these material powders are fitted in the cooperation composition shown in table 1, by ball mill wet mixed 80 hours, after drying with punch forming under the pressure of 120MPa for having diameter: 50mm × thickness: the pressed compact of 1.5mm size, then at pressure: in the vacuum atmosphere of 1Pa, sinter under the predetermined temperature of this pressed compact within the scope of 900 ~ 1300 DEG C is kept the condition of 60 minutes, be made cutting edge piece presintering body, by this presintering body with to prepare separately there is Co:8 quality %, WC: remaining composition and diameter: 50mm × thickness: under the state of the WC base cemented carbide supporting slice overlap of 2mm size, load in usual ultra-high pressure sintering device, in usual conditions, i.e. pressure: 5GPa, temperature: the predetermined temperature within the scope of 1200 ~ 1400 DEG C carries out ultra-high pressure sintering under keeping the condition of 0.8 hour, skive grinding top and bottom are used after sintering, electricity consumption wire electric discharge machine is divided into while be the equilateral triangle shape of 3mm, in addition, use has Cu:26% in mass %, Ti:5%, Ni:2.5%, Ag: the solder of the Ag alloy of remaining composition, there is Co:5 quality %, TaC:5 quality %, WC: the brazed portion (nose part) of the WC base cemented carbide vane body of remaining composition and the shape (thickness: the equilateral triangle of 4.76mm × mono-edge lengths: 12.7mm) of CIS specification SNGA120412 carries out soldering, after preliminary dimension is processed in periphery, implement wide at blade part: 0.13mm, angle: the cutting edge reconditioning processing of 25 °, and implement fine finishining grinding, produce the tool base A ~ J of the blade shapes with ISO specification SNGA120412 thus respectively.
A () then, distinguish Ultrasonic Cleaning above-mentioned tool base A ~ J in acetone, under the state of drying, circumferentially portion be arranged in the arc ion plating apparatus shown in Fig. 1 from the central shaft turntable to radial direction away from the position of preset distance, using the cathode electrode (evaporation source) of the thin layer B formation metal Ti of upper layer as a side side, and will there is the thin layer A that forms the upper layer that corresponding one-tenth is grouped into respectively with the target shown in table 3 and the lower layer formation Ti-Al alloy cathode electrode (evaporation source) as the opposing party side, they are clipped described turntable arranged opposite,
B () first, the vacuum of below 0.1Pa is remained to being exhausted also limit in device, while 500 DEG C will be heated to be in device with heater, import Ar gas afterwards and be set to 0.7Pa atmosphere, and the Dc bias of opposite side additional-200V of tool base that rotation limit rotates on described platform, and then by argon ion bombardment cleaning means matrix surface
C () imports nitrogen as reacting gas to be set to the reaction atmosphere of 3Pa in device, and the Dc bias of opposite side additional-100V of tool base that rotation limit rotates on described turntable, and make 100A electric current flow through described thin layer A and produce arc discharge between lower layer formation Ti-Al alloy and anode electrode, and then [the Ti of the target composition shown in table 3 and target thickness is formed at the surperficial evaporation of described tool base, Al] N layer is as the lower layer of hard coating layer
D () then adjusts nitrogen flow as the reacting gas be directed in device to be set to the reaction atmosphere of 2Pa, and under the state of the predetermined direct current bias voltage in opposite side additional-10 ~-100V scope of tool base that rotation limit rotates on described turntable, scheduled current within the scope of 50 ~ 200A is flow through between the cathode electrode of described thin layer B formation metal Ti and anode electrode and produces arc discharge, the thin layer B of predetermined thickness is formed on the surface of described tool base, and stop arc discharge after forming described thin layer B, replace this, scheduled current within the scope of same 50 ~ 200A is flow through between the cathode electrode of described thin layer A and lower layer formation Ti-Al alloy and anode electrode and produces arc discharge, arc discharge is stopped after forming the thin layer A of predetermined thickness, alternate repetition carries out the formation based on the formation of the thin layer B of the arc discharge between the cathode electrode and anode electrode of described thin layer B formation metal Ti and the thin layer A based on the arc discharge between the cathode electrode and anode electrode of described thin layer A and lower layer formation Ti-Al alloy again, and then on the surface of described tool base, to be formed along thickness direction evaporation with the total thickness (average thickness) shown in same table 3 and comprise the target composition shown in table 3 and the thin layer A of one deck target thickness and the alternately laminated upper layer of thin layer B.
(e) in addition, with blasting pressure: 0.1 ~ 0.15MPa, blast time: 2 ~ 5 seconds, number of repetition: 5 ~ 10 times, incidence angle: relative to rake face 40 ~ 50 °, particle diameter: 220 ~ No. 1500, slurry concentration: 15 ~ 60 quality %, particle type: Al
2o
3blasted condition intermittently carry out blasting treatment, thus produce the present invention's coated cBN base sintering instrument 1 ~ 10 respectively.Table 2 illustrates blasted condition.By carrying out this interrupted blasting treatment, thus can not accumulated fatigue between each layer of and laminated section inner at epithelium, it is higher and improved the epithelium of hardness by the residual stress increased as the TiAlN of hard film that its result can be produced on the flatness of epithelial surfaces under the state that there is not be full of cracks.Respectively according to rear knife face, rake face and cutting edge reconditioning portion, table 3 illustrate the residual stress of the surface roughness Ra of epithelial surfaces, the TiAlN of epithelium, outermost layer TiAlN with nano-indentation hardness during 100mg load measurement.
And, for the purpose of comparing, a () distinguishes Ultrasonic Cleaning above-mentioned tool base A ~ J in acetone, under dry state, circumferentially portion be arranged in the arc ion plating apparatus shown in Fig. 1 from the central shaft turntable to radial direction away from the position of preset distance, using the cathode electrode (evaporation source) of the thin layer B formation metal Ti of upper layer as a side side, and will there is the thin layer A that forms the upper layer that corresponding one-tenth is grouped into respectively with the target shown in table 4 and the lower layer formation Ti-Al alloy cathode electrode (evaporation source) as the opposing party side, clip described turntable arranged opposite,
B () first, also the vacuum of below 0.1Pa is remained limit to exhaust in device, while 500 DEG C will be heated to be in device with heater, import Ar gas afterwards and be set to 0.7Pa atmosphere, and the Dc bias of opposite side additional-200V of tool base that rotation limit rotates on described platform, and then by argon ion bombardment cleaning means matrix surface
C () imports nitrogen as reacting gas to be set to the reaction atmosphere of 3Pa in device, and the Dc bias of opposite side additional-100V of tool base that rotation limit rotates on described turntable, and make 100A electric current flow through described thin layer A and produce arc discharge between lower layer formation Ti-Al alloy and anode electrode, and then [the Ti of the target composition shown in table 4 and target thickness is formed at the surperficial evaporation of described tool base, Al] N layer is as the lower layer of hard coating layer
D () then adjusts nitrogen flow as the reacting gas be directed in device to be set to the reaction atmosphere of 2Pa, and under the state of the predetermined direct current bias voltage in opposite side additional-10 ~-100V scope of tool base that rotation limit rotates on described turntable, scheduled current in the scope of 50 ~ 200A is flow through between the cathode electrode of described thin layer B formation metal Ti and anode electrode and produces arc discharge, the thin layer B of predetermined thickness is formed on the surface of described tool base, and stop arc discharge after forming described thin layer B, replace this, scheduled current in the scope of same 50 ~ 200A is flow through between the cathode electrode of described thin layer A and lower layer formation Ti-Al alloy and anode electrode and produces arc discharge, arc discharge is stopped after forming the thin layer A of predetermined thickness, alternate repetition carries out the formation based on the formation of the thin layer B of the arc discharge between the cathode electrode and anode electrode of described thin layer B formation metal Ti and the thin layer A based on the arc discharge between the cathode electrode and anode electrode of described thin layer A and lower layer formation Ti-Al alloy again, and then on the surface of described tool base, to be formed along thickness direction evaporation with the total thickness (average thickness) shown in table 4 equally and comprise the target composition shown in table 4 and the thin layer A of one deck target thickness and the alternately laminated upper layer of thin layer B, produce coated cBN base sintering instrument 1 ~ 10 in the past thus respectively.The hard coating layer of coated cBN base sintering instrument included the stepped construction of [Ti, Al] N layer and TiN layer in the past, and different from product of the present invention, surface roughness, residual stress and hardness are not controlled.
To the cBN based sintered fuel of the cutting insert body of the various coated cBN base sintering instrument that formation obtains according to this result, utilize scanning electron microscope to observe it when organizing, arbitrary cutting insert body all demonstrates ultra-high pressure sintering product in fact between the tissue of the cBN phase with the interface of the TiN phase of formation continuous phase that form decentralized photo.
In addition, to this surface coating layer, by utilize transmission electron microscope energy dispersion-type X-ray assay its composition time, illustrate respectively and form identical composition with target in fact, and when utilizing transmission electron microscope pair cross-section to measure its average thickness, mean value (mean values at 5 positions) identical with target thickness in fact is all shown.
Then, all under the state of the fastening above-mentioned various coated cBN base sintering instrument of the leading section stationary fixture of instrument steel lathe tool, with machining condition A ~ C to the present invention coated cBN base sintering instrument 1 ~ 10 and in the past coated cBN base sintering instrument 1 ~ 10 implement high-speed and continuous cutting test.
Carry out [machining condition A]
The pole of the carburizing and quenching material (hardness: HRC61) of workpiece: JISSCM415,
Cutting speed: 295m/min.,
Cutting-in amount: 0.23mm,
Feed speed: 0.13mm/rev.,
Cutting time: 6 minutes
Steel alloy under condition dry type continuous high speed machining test (common cutting speed is 200m/min.),
Carry out [machining condition B]
The pole of the carburizing and quenching material (hardness: HRC60) of workpiece: JISSCr420,
Cutting speed: 270m/min.,
Cutting-in amount: 0.23mm,
Feed speed: 0.13mm/rev.,
Cutting time: 6 minutes
Chromium steel under condition dry type continuous high speed machining test (common cutting speed is 160m/min.),
Carry out [machining condition C]
The pole of the quenching material (hardness: HRC61) of workpiece: JISSUJ2,
Cutting speed: 240m/min.,
Cutting-in amount: 0.23mm,
Feed speed: 0.13mm/rev.,
Cutting time: 6 minutes
Dry type continuous high speed machining test (common cutting speed is 150m/min.) of the bearing steel under condition, arbitrary machining test all measures the wear of the tool flank width (mm) of blade and the polished surface precision (arithmetic mean roughness according to JIS B0601-2001) (Ra μm) of workpiece.This measurement result is shown in Table 5.
[table 1]
[table 2]
From the result shown in table 2 ~ 4, the hard coating layer of the present invention coated cBN base sintering instrument includes to be had the average thickness of one deck and is respectively the thin layer A of 0.03 ~ 0.3 μm and the alternatively layered structure of thin layer B and average thickness and is 0.3 ~ 2 μm and comprises [Ti, Al] the outermost average thickness (total thickness) of N layer is the upper layer of 0.5 ~ 3 μm, with the lower layer of average thickness with 1.5 ~ 3 μm, described lower layer possesses excellent heat resistance, elevated temperature strength and excellent high temperature hardness, described upper layer has excellent heat resistance in addition, high temperature hardness and more excellent elevated temperature strength and impact strength, therefore, even if at steel alloy, in the high-speed cutting processing of the glass hard steels such as the hardened steel of bearing steel, also can not produce border Abnormal damage and tipping and excellent wearability can be played, and guarantee the polished surface precision of the excellence of workpiece, on the other hand, the hard coating layer of coated cBN base sintering instrument included [Ti in the past, Al] stepped construction of N layer and TiN layer, different from product of the present invention, surface roughness, residual stress and hardness are not controlled, its result, especially because of the elevated temperature strength of hard coating layer, impact strength is not enough and on point of a knife, produce border Abnormal damage or tipping, not only cannot maintain the polished surface precision of workpiece, and reaching service life than in the short period.
As above-mentioned, the machining of coated cBN base sintering instrument of the present invention much less under the usual machining condition of various steel or cast iron etc., even especially as steel alloy, the glass hard steels such as the quenching material of bearing steel, to produce with high heat and high-speed and continuous blade part being applied to the mechanicalness load of great intermittence or impact is cut or high rate intermittent cuts, described hard coating layer also plays the excellent Abnormal damage of resistance to border, and the workpiece polished surface precision of long term maintenance excellence, and demonstrate excellent wearability, therefore, can the high performance of corresponding cutting apparatus and the saving labourization of machining and energy-saving and cost degradation fully contentedly.
Claims (1)
1. one kind plays the Surface coating cubic boron nitride base ultra-high pressure sintered material cutting tool of peel resistance, wearability for a long time, it is the surperficial evaporation formation hard coating layer of the cutting element of the cubic boron nitride base high-pressure sintered body of 50 ~ 85 quality % at the content comprising cubic boron nitride, it is characterized in that
Described hard coating layer comprises:
A () lower layer, has the average thickness of 1.5 ~ 3 μm, and comprise and meet composition formula: [Ti
1-Xal
x] the composite nitride nitride layer of Ti and Al of N, wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60; And
B () upper layer, makes to meet composition formula: [Ti
1-Xal
x] composite nitride nitride layer and the Ti nitride layer of Ti and Al of N and each thickness of TiN layer become 0.03 ~ 0.3 μm to come alternately laminated in average thickness, wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60, and has the average thickness of 0.3 ~ 2 μm in outermost layer formation and meet composition formula: [Ti
1-Xal
x] the composite nitride nitride layer of Ti and Al of N forms, the average thickness of total of this upper layer is 0.5 ~ 3 μm, and wherein, with atomic ratio measuring, X represents 0.30 ~ 0.60, and,
C the surface roughness Ra on () hard coating layer surface is 0.08 ~ 0.20 μm in rear knife face and rake face, be 0.07 ~ 0.10 μm in cutting edge reconditioning portion,
D the residual stress of () hard coating layer is-1 ~-2GPa in rear knife face and rake face, be-1.5 ~-3.0GPa in cutting edge reconditioning portion, and the residual stress in rear knife face, rake face is greater than the residual stress in cutting edge reconditioning portion,
(e) Ti and Al that described outermost layer is formed composite nitride nitride layer with nano-indentation hardness during 100mg load measurement in rear knife face and rake face for 30 ~ 38GPa, be 33 ~ 50GPa in cutting edge reconditioning portion, and the nano-indentation hardness in rear knife face, rake face is less than the nano-indentation hardness in cutting edge reconditioning portion.
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| JP2010-243772 | 2010-10-29 | ||
| JP2010243772A JP5574277B2 (en) | 2010-10-29 | 2010-10-29 | Cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material with excellent peeling resistance |
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| CN102528104A CN102528104A (en) | 2012-07-04 |
| CN102528104B true CN102528104B (en) | 2015-07-22 |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US12263513B2 (en) | 2018-12-03 | 2025-04-01 | Proterial, Ltd. | Coated die for use in hot stamping |
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| JP5686253B2 (en) * | 2011-04-28 | 2015-03-18 | 三菱マテリアル株式会社 | Cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material with excellent peeling resistance |
| JP5757232B2 (en) * | 2011-12-26 | 2015-07-29 | 三菱マテリアル株式会社 | Surface coated cutting tool with excellent chipping resistance and wear resistance due to hard coating layer |
| JP6198142B2 (en) * | 2014-03-26 | 2017-09-20 | 三菱マテリアル株式会社 | Cutting tool made of cubic boron nitride super high pressure sintered material |
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| WO2020079953A1 (en) * | 2018-10-15 | 2020-04-23 | 住友電工ハードメタル株式会社 | Cutting tool |
| WO2020079952A1 (en) * | 2018-10-15 | 2020-04-23 | 住友電工ハードメタル株式会社 | Cutting tool |
| WO2020116291A1 (en) * | 2018-12-03 | 2020-06-11 | 日立金属株式会社 | Coated die for use in hot stamping |
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| US20230058739A1 (en) * | 2020-01-20 | 2023-02-23 | Kyocera Corporation | Coated tool |
| JP7108966B2 (en) * | 2020-06-24 | 2022-07-29 | 株式会社タンガロイ | coated cutting tools |
| JP7568566B2 (en) | 2021-03-30 | 2024-10-16 | 京セラ株式会社 | Inserts and Cutting Tools |
| US12109628B2 (en) | 2022-08-10 | 2024-10-08 | Iscar, Ltd. | Cutting tool with a TiAlN coating having rake and relief surfaces with different residual stresses |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1137959A (en) * | 1994-12-01 | 1996-12-18 | 住友电气工业株式会社 | Sintered body cutter head for cutting and manufacturing method thereof |
| CN1642682A (en) * | 2002-01-21 | 2005-07-20 | 三菱综合材料神户工具株式会社 | Surface-coated cutting tool member having coating layer exhibiting superior wear resistance during high speed cutting operation and method for forming hard coating layer on surface of cutting tool |
| JP2006263857A (en) * | 2005-03-24 | 2006-10-05 | Kyocera Corp | Surface-coated cutting tool and manufacturing method thereof |
| JP2007190668A (en) * | 2005-12-22 | 2007-08-02 | Mitsubishi Materials Corp | Cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material that provides excellent long-term surface accuracy in high-speed cutting of hardened steel |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0773802B2 (en) * | 1987-07-10 | 1995-08-09 | 住友電気工業株式会社 | Coated cemented carbide tool |
| JP4446469B2 (en) * | 2004-03-12 | 2010-04-07 | 住友電工ハードメタル株式会社 | Coated cutting tool |
| KR100576321B1 (en) * | 2004-12-14 | 2006-05-03 | 한국야금 주식회사 | Tough Cutting Tools / Wear Resistant Tools |
| JP4841201B2 (en) * | 2005-08-25 | 2011-12-21 | 京セラ株式会社 | Throwaway tip |
-
2010
- 2010-10-29 JP JP2010243772A patent/JP5574277B2/en not_active Expired - Fee Related
-
2011
- 2011-10-26 CN CN201110329048.3A patent/CN102528104B/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1137959A (en) * | 1994-12-01 | 1996-12-18 | 住友电气工业株式会社 | Sintered body cutter head for cutting and manufacturing method thereof |
| CN1642682A (en) * | 2002-01-21 | 2005-07-20 | 三菱综合材料神户工具株式会社 | Surface-coated cutting tool member having coating layer exhibiting superior wear resistance during high speed cutting operation and method for forming hard coating layer on surface of cutting tool |
| JP2006263857A (en) * | 2005-03-24 | 2006-10-05 | Kyocera Corp | Surface-coated cutting tool and manufacturing method thereof |
| JP2007190668A (en) * | 2005-12-22 | 2007-08-02 | Mitsubishi Materials Corp | Cutting tool made of surface-coated cubic boron nitride-based ultra-high pressure sintered material that provides excellent long-term surface accuracy in high-speed cutting of hardened steel |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US12263513B2 (en) | 2018-12-03 | 2025-04-01 | Proterial, Ltd. | Coated die for use in hot stamping |
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| JP2012096304A (en) | 2012-05-24 |
| CN102528104A (en) | 2012-07-04 |
| JP5574277B2 (en) | 2014-08-20 |
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