CN103962589A - Surface coated cutting tool - Google Patents
Surface coated cutting tool Download PDFInfo
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- CN103962589A CN103962589A CN201410034933.2A CN201410034933A CN103962589A CN 103962589 A CN103962589 A CN 103962589A CN 201410034933 A CN201410034933 A CN 201410034933A CN 103962589 A CN103962589 A CN 103962589A
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- 238000005520 cutting process Methods 0.000 title claims abstract description 52
- 239000010410 layer Substances 0.000 claims abstract description 131
- 239000011247 coating layer Substances 0.000 claims abstract description 67
- 238000000034 method Methods 0.000 claims abstract description 23
- 230000008020 evaporation Effects 0.000 claims abstract description 15
- 238000001704 evaporation Methods 0.000 claims abstract description 15
- 238000002425 crystallisation Methods 0.000 claims description 47
- 230000008025 crystallization Effects 0.000 claims description 47
- 150000004767 nitrides Chemical class 0.000 claims description 8
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims description 3
- 239000013078 crystal Substances 0.000 abstract description 14
- 230000006835 compression Effects 0.000 abstract 1
- 238000007906 compression Methods 0.000 abstract 1
- 239000000758 substrate Substances 0.000 abstract 1
- 239000011248 coating agent Substances 0.000 description 25
- 238000000576 coating method Methods 0.000 description 25
- 238000003754 machining Methods 0.000 description 12
- 239000000843 powder Substances 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 10
- 229910000599 Cr alloy Inorganic materials 0.000 description 9
- QQHSIRTYSFLSRM-UHFFFAOYSA-N alumanylidynechromium Chemical compound [Al].[Cr] QQHSIRTYSFLSRM-UHFFFAOYSA-N 0.000 description 9
- 229910000975 Carbon steel Inorganic materials 0.000 description 8
- 239000010962 carbon steel Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 238000009826 distribution Methods 0.000 description 7
- 229910000851 Alloy steel Inorganic materials 0.000 description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- 238000002441 X-ray diffraction Methods 0.000 description 6
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- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- 208000037656 Respiratory Sounds Diseases 0.000 description 4
- 238000004140 cleaning Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 230000000803 paradoxical effect Effects 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 238000005240 physical vapour deposition Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 229910052581 Si3N4 Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 238000003556 assay Methods 0.000 description 2
- 238000004364 calculation method Methods 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000008676 import Effects 0.000 description 2
- 238000007733 ion plating Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910017488 Cu K Inorganic materials 0.000 description 1
- 229910017541 Cu-K Inorganic materials 0.000 description 1
- 230000005260 alpha ray Effects 0.000 description 1
- 238000000498 ball milling Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000005229 chemical vapour deposition Methods 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000004453 electron probe microanalysis Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
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- 238000011068 loading method Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
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- 238000004904 shortening Methods 0.000 description 1
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Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
- B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B51/00—Tools for drilling machines
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23C—MILLING
- B23C5/00—Milling-cutters
- B23C5/16—Milling-cutters characterised by physical features other than shape
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
- C23C14/0641—Nitrides
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
Abstract
The invention provides a surface coated cutting tool. The surface coated cutting tool has a hard coating layer is formed on the surface of a tool substrate with an N layer (Al, Cr) through evaporation. When a residual stress is measured by using a two-dimensional method on a rear knife surface and a front knife surface near a cross ridge of the front knife face and the rear knife face, a compression residual stress sigma 11 in the direction parallel to the cross ridge satisfies 0.5 GPa<=sigma 11 <= 4.5 GPa and also sigma 11-sigma 22>=0.5GPa. Furthermore, in a position in a range from the cross ridge to at least 100 [mu]m, the hard coating layer is composed of a thin layer A in which fine grains with a crystal width smaller than 0.3 [mu]m accounts for 0 to 50 length% and a thin layer B in which fine grains with a crystal width smaller than 0.3 [mu]m accounts for 50 to 100 length%, the thin layer A and the thin layer B are alternatively stacked. Further, in a position being over 150 [mu]m from the cross ridge, the fine grains with a crystal width smaller than 0.3 [mu]m accounts for 0 to 50 length%.
Description
Technical field
Even if this invention relates to a kind of when carrying out the machining of carbon steel, steel alloy etc. with the thermogenetic high-speed cutting condition of height, hard coating layer is also brought into play the excellent resistance to surface-coated cutting tool (hereinafter referred to as coating tool) that collapses cutter, mar proof.
Background technology
Conventionally, in surface-coated cutting tool, have in the turning processing of the workpiece such as various steel and cast iron and slabbing processing, use with the mode freely of loading and unloading be arranged on the indexable insert tip, throw away tip of the leading section of lathe tool, for the solid formula slotting cutter of drill bit and miniature bur, the building up by welding processing that is also useful on described workpiece, groove processing and the shoulder processing etc. of the boring machining of described workpiece etc. etc., and knownly have to load and unload that mode is freely installed described indexable insert tip, throw away tip and carry out in the same manner the indexable slotting cutter instrument etc. of machining with described solid formula slotting cutter.
For example, as Patent Document 1, known to coating tool, forming by bed thickness at the surperficial evaporation of the tool base being made up of WC base cemented carbide is the hard coating layer that 0.8～5.0 Cr of μ m and the complex nitride of Al form, and this hard coating layer is configured to by the thin layer A of the granular crystal organizational composition of the complex nitride of Cr and Al with by the alternately laminated structure of the thin layer B of column crystallization organizational composition, and, the average crystallite particle diameter of the granular crystal that forms thin layer A is made as below 30nm, and the average crystallite particle diameter of the column crystallization that forms thin layer B is made as to 50～500nm, improve thus mar proof.
But, in recent years, along with high speed, the high efficiency of machining, except coating tool is required to improve mar proof, also require to improve the resistance to cutter that collapses, carried out various improvement in order to tackle these cutting abilities, and as one of them, also proposing there is the residual stress by controlling cutting element to improve the resistance to scheme that collapses cutter, mar proof.
For example, as shown in patent documentation 2, propose to have following scheme: form by the 4a that is selected from periodic table coated, 5a, 6a family element, Si, the carbide of Al, nitride, oxide, in the coating tool of the hard coating layer that the single or multiple lift of at least one in boride and these solid solution each other forms, form following residual stress, while being expressed as σ A by near the compressive residual stress of this hard films of part cutting edge, 0GPa≤σ A≤1.0GPa, and when the compressive residual stress of this hard films of middle body is expressed as to σ B, 1.5GPa≤σ B≤2.5GPa, improve thus the resistance to cutter that collapses of coating tool, mar proof.
And illustrate can utilize plasma current for 150A, Ar gas flow be 50cc/min, N
2gas flow is 100cc/min, C
2h
2gas flow is 10cc/min, become film pressure is that 0.53～0.8Pa and bias voltage are that the physical vapor deposition of-150～-200V is made above-mentioned coating tool.
And, in patent documentation 3, be not for example for coating tool, but itself propose there is following scheme for the cutting element being formed by silicon nitride sinter: utilize 2D method (two-dimensional x-ray diffraction/full debye ring fitting process (FullDebye rings Fitting method)) in the time that the point of a knife of rake face is measured residual stress, by parallel with rake face and towards the center from rake face the compressive residual stress σ 11 of the direction of the point of a knife of close measuring point be made as 10～30MPa, and, the compressive residual stress σ 22 of parallel with rake face and vertical with σ 11 directions direction is made as below 10MPa, improve thus the resistance to cutter that collapses of the cutting element being formed by silicon nitride sinter, mar proof.
Patent documentation 1: Japanese Patent Publication 2010-94744 communique
Patent documentation 2: Japanese Patent Publication 2005-28520 communique
Patent documentation 3: Japanese Patent Publication 2010-264574 communique
In recent years, the high performance of cutting apparatus is remarkable, and on the other hand, the requirement of saving labourization, energy-saving and cost degradation to machining is strong, and with this, machining will be carried out under harsher machining condition.
In above-mentioned coating tool in the past, can expect to improve resistance to cutter, the mar proof of collapsing to a certain degree, but present situation is, be used in carbon steel, steel alloy etc. with in the thermogenetic high-speed cutting of height processing time, still easily produce and collapse cutter or wear away change greatly, and because these are former thereby reach service life within a short period of time.
Summary of the invention
Therefore, the inventor etc. in order to provide resistance to cutter and the excellent in wear resistance of collapsing in the high-speed cutting processing of carbon steel, steel alloy etc., and in long-term use, bring into play the coating tool of excellent cutting ability, and the result that the control of residual stress to hard coating layer and the layer structure of hard coating layer are furtherd investigate obtains following opinion.
In the past, while making coating tool, as the method that forms hard coating layer, conventionally adopt chemical vapor deposition method, physical vapor deposition etc., and, for example, while utilizing a kind of arc ion plating (AIP) method of physical vapor deposition to carry out film forming to hard coating layer, as Patent Document 1, by in tool base charging apparatus and apply the bias voltage of regulation, and be heated under the state of set point of temperature in by device, between the Al-Cr of anode electrode and composition requirement alloys target, produce arc discharge, simultaneously carry out evaporation as reacting gas and in the reaction atmosphere of authorized pressure to importing nitrogen in device, thus hard coating layer is carried out to film forming.
The inventor etc. utilize above-mentioned AIP method in the past to by (Al, Cr) when the hard coating layer that N layer forms carries out film forming, between tool base and target, apply magnetic field, the Investigational following situation that found that is carried out in the impact of the compressive residual stress for magnetic field on hard coating layer: the film forming of utilizing the hard coating layer that AIP method carries out in the magnetic field that shows prescribed strength and specified distribution, can control thus the value of the compressive residual stress that is formed at hard coating layer and the distribution of crystallization control width, and, as the value of the compressive residual stress of above-mentioned adjustment hard coating layer, and possesses (the Al by the distribution of adjusted crystallization width, the coating tool of the hard coating layer that Cr) N layer forms is at carbon steel, steel alloys etc. are with in the thermogenetic high-speed cutting processing of height, the resistance to cutter that collapses that performance is excellent, mar proof, and bring into play excellent cutting ability in long-term use.
This invention proposes according to above-mentioned opinion, has following feature:
(1) surface-coated cutting tool, its surperficial evaporation in the tool base being made up of tungsten carbide base carbide alloy forms the hard coating layer being made up of the complex nitride layer of Al and Cr, wherein,
(a), in above-mentioned hard coating layer, average film thickness is 1～10 μ m, Cr shared content ratio in the total amount of Al and Cr be 0.2～0.5(wherein, be atomic ratio),
(b) surface on the rear knife face of above-mentioned hard coating layer or on rake face, using in the time that the position of the distance 50 μ m of the crest line portion of intersecting of rear knife face and rake face utilizes 2D method to measure residual stress in the scope of the radius 50 μ m of center, meet the relation of 0.5GPa≤σ 11≤4.5GPa with the above-mentioned compressive residual stress σ 11 that intersects the parallel direction of crest line portion, meet the relation of 0GPa≤σ 22≤4.0GPa with the compressive residual stress σ 22 of the orthogonal direction of above-mentioned σ 11, and, above-mentioned σ 11 and σ 22 meet the relation of σ 11-σ 22 >=0.5GPa
(c) from above-mentioned intersection crest line portion till the position of the scope of at least 100 μ m, the fine-grain that above-mentioned hard coating layer is less than 0.3 μ m by crystallization width accounts for fine-grain that the thin layer A of 0～50 length % and crystallization width be less than 0.3 μ m and accounts for that the thin layer B of 50～100 length % is alternately laminated to be formed, the difference of the ratio of the fine-grain of thin layer A and thin layer B is more than 10 length %, and alternately laminated most surface is made up of thin layer A, on the other hand, in the position more than the above-mentioned intersection crest line distance 150 μ m of portion, the fine-grain that in above-mentioned hard coating layer, crystallization width is less than 0.3 μ m accounts for 0～50 length %.
(2) according to the surface-coated cutting tool of recording in described (1), wherein,
In Self-crossover crest line portion, till the position of the scope of 100 μ m, the average film thickness of above-mentioned thin layer A and thin layer B is respectively 0.5～5.0 μ m.
(3) according to the surface-coated cutting tool of recording in described (2), wherein,
In Self-crossover crest line portion, till the position of the scope of 100 μ m, total number of plies of above-mentioned thin layer A and thin layer B is 2～20 layers.
(4) according to the surface-coated cutting tool of recording in described (3), wherein,
In Self-crossover crest line portion, till the position of the scope of 100 μ m, the average film thickness of the thin layer A ratio shared with respect to the average film thickness of hard coating layer is 50～70%.
Then, the coating tool of this invention is elaborated.
(a) classification of hard coating layer, average film thickness:
The hard coating layer of this invention is made up of the complex nitride layer ((Al, Cr) N layer) of Al and Cr.
As everyone knows, as hard coating layer, above-mentioned (Al, Cr) in N layer, Al composition improves high temperature hardness and heat resistance, Cr composition improves elevated temperature strength, and by contain Cr and Al simultaneously, high temperature oxidative resistance is improved, its high temperature hardness, heat resistance, elevated temperature strength and high temperature oxidative resistance excellence thus.
In the present invention, if Cr account for its with the content of the total amount of Al than (atomic ratio, lower same) be less than 0.2, be difficult to guarantee that high-speed cutting adds the elevated temperature strength in man-hour, on the other hand, if accounting for it, Cr exceedes 0.5 with the content of the total amount of Al than (atomic ratio), the content of Al is than relatively reducing, thereby cause high temperature hardness reduction, heat resistance to reduce, its result, deteriorated because producing the mar proof such as eccentric wear, generation pyroplastic deformation, thus Cr is accounted for to it and be set as 0.2～0.5 with the content of the total amount of Al than (atomic ratio).
And, by (Al, when the average film thickness of the hard coating layer that Cr) N layer forms is less than 1 μ m, cannot bring into play for a long time excellent mar proof, thereby become the reason shortening life tools, on the other hand, if its average film thickness exceedes 10 μ m, easily produce and collapse cutter in nose part, therefore its average film thickness is set as to 1～10 μ m.
(b) be formed at the compressive residual stress of hard coating layer:
In the present invention, above-mentioned by (Al, on the rear knife face of the hard coating layer that Cr) N layer forms or on rake face, value σ 11, the σ 22 of the compressive residual stress of measuring in the scope of the radius 50 μ m of center from rear knife face and the position of the distance 50 μ m of the crest line portion of intersecting (hereinafter referred to as " cutting edge crest line portion ") of rake face are being set in the number range of regulation, and the relation each other of regulation σ 11 and σ 22, improves resistance to cutter, the mar proof of collapsing thus.
Utilize Fig. 1, Fig. 2 to describe, (a) of Fig. 1 is the schematic diagram of ball end mill entirety, (b) of Fig. 1 is the schematic diagram of ball end mill front end, and (a) of Fig. 2 is the schematic diagram of perpendicular type slotting cutter entirety, and (b) of Fig. 2 is the schematic diagram of perpendicular type slotting cutter front end.
In (b) of Fig. 1, (b) of Fig. 2, being tangential in the Al of rear knife face and the complex nitride layer of Cr within the scope of the radius 50 μ m of a point with cutting edge crest line portion, utilize 2D method (two-dimensional x-ray diffraction/full debye ring fitting process) to measure compressive residual stress σ 11, the σ 22 of both direction.σ 11 is and the compressive residual stress that intersects the parallel direction of crest line portion of rear knife face and rake face, and σ 22 is the compressive residual stress of the direction orthogonal with above-mentioned σ 11.Be made as in addition the region that measurement range all comprises rear knife face, and do not exceed the region of rear knife face.
According to the present invention, need σ 11 to meet the relation of 0.5GPa≤σ 11≤4.5GPa, σ 22 meets the relation of 0GPa≤σ 22≤4.0GPa, and above-mentioned σ 11, σ 22 meet the relation of σ 11-σ 22 >=0.5GPa.
At this, if σ 11 is less than 0.5GPa and σ 22 and is less than 0GPa(this mean that σ 22 becomes stretching residual stress), the lower hardness of hard coating layer, therefore mar proof reduces, on the other hand, if σ 11 exceedes 4.5Gpa and σ 22 exceedes 4.0GPa, hard coating layer easily causes and peels off, thus, and in the present invention, σ 11 is set as to 0.5GPa≤σ 11≤4.5GPa, and σ 22 is set as to 0GPa≤σ 22≤4.0GPa.
And, in the present invention, σ 11, σ 22 relation being each other set as to σ 11-σ 22 >=0.5GPa, this is due to following reason.
; when machining; there is larger compressive residual stress with the orthogonal direction (direction of σ 11) of the direction (direction of σ 22) that causes the power that collapses cutter, wearing and tearing; thus; collapse the effect of the power of cutter, wearing and tearing by these σ 11 performance opposing generations, suppress to collapse generation and the aggravation of cutter, wearing and tearing.
But when σ 22 becomes large, and the relation of σ 11 and σ 22 is while becoming σ 11-σ 22 < 0.5GPa, residual stress concentrations, in cutting edge crest line portion, therefore easily produces and collapses cutter.
Therefore,, in the present invention, σ 11, σ 22 relation are each other set as to σ 11-σ 22 >=0.5GPa.
(c) the layer structure of hard coating layer:
In this invention, according to the distance with the crest line portion of intersecting of rake face from rear knife face, by changing the layer structure of hard coating layer, improve resistance to cutter, the mar proof of collapsing.
; be constructed as follows hard coating layer: in Self-crossover crest line portion till the position of the scope of at least 100 μ m; the fine-grain that is less than 0.3 μ m by crystallization width accounts for fine-grain that the thin layer A of 0～50 length % and crystallization width be less than 0.3 μ m and accounts for that the thin layer B of 50～100 length % is alternately laminated to be formed, and the difference of the ratio of the fine-grain of thin layer A and thin layer B is more than 10 length %.
On the other hand, in the position that exceedes 150 μ m from above-mentioned intersection crest line portion, the fine-grain that in above-mentioned hard coating layer, crystallization width is less than 0.3 μ m accounts for 0～50 length %,, forms hard coating layer by the crystallization with the crystallization width distribution identical with described thin layer A that is.
In addition, exceeding 100 μ m and be less than the position of the scope of 150 μ m from above-mentioned intersection crest line portion, layer structure gradually changes into the transitional region of the crystallization of the demonstration crystallization width distribution identical with thin layer A from thin layer A and the alternately laminated structure of thin layer B.
In addition, " length % " in the present invention refers to, by in the cross section of the cross section of knife face side cutting out from tool base point of a knife or rake face side, and the parallel direction in tool base surface while spreading all over distance between the crystal boundary of scope mensuration of the width 20 μ m of the zone line of each layer as crystallization width, the total of the crystallization width of paid close attention to big or small crystal grain (for example, crystallization width is less than the fine-grain of 0.3 μ m) is defined as to " length % " with respect to the ratio of measured total crystallization width 20 μ m.
In this invention, first, hard coating layer is configured in Self-crossover crest line portion till the position of the scope of at least 100 μ m, the fine-grain that is less than 0.3 μ m by crystallization width accounts for fine-grain that the thin layer A of 0～50 length % and crystallization width be less than 0.3 μ m and accounts for the alternately laminated structure (in addition, alternately laminated most surface is made as thin layer A) of thin layer B of 50～100 length %.
This be because, in the time that near hard coating layer point of a knife is only made up of the less thin layer A of fine-grain, under with the thermogenetic high-speed cutting condition of height, bring into play excellent mar proof, but easily crack near point of a knife, its result, the resistance to cutter that collapses reduces, thus, hard coating layer is configured in Self-crossover crest line portion till near the point of a knife of the position of the scope of at least 100 μ m, the fine-grain that is less than 0.3 μ m by crystallization width accounts for fine-grain that the thin layer A of 0～50 length % and crystallization width be less than 0.3 μ m and accounts for the alternately laminated structure of thin layer B of 50～100 length %, thereby guarantee the mar proof of regulation and improve the resistance to cutter that collapses.
At this, in thin layer A, it is because if it exceedes 50 length %, because the increase of compressive residual stress easily produces peeling off of film, and mar proof reduces below that the fine-grain proportion that crystallization width is less than to 0.3 μ m is made as 50 length %.
And in thin layer B, it is because if it is less than 50 length %, because crystal grain increases and crystal boundary reduces, therefore the resistance to cutter that collapses reduces above that the fine-grain proportion that crystallization width is less than to 0.3 μ m is made as 50 length %.
By the difference of the ratio of the fine-grain of thin layer A and thin layer B be made as 10 length % be above because, in thin layer A, fine-grain is less, therefore crackle is more, and easily produces the be full of cracks being caused by crackle near point of a knife.On the other hand, in thin layer B, the ratio of fine-grain is more, therefore can prevent that crackle from becoming large.Now, if the difference of the ratio of the fine-grain of thin layer A and thin layer B is not more than 10 length % in the ratio of fine-grain, the crackle that prevents thin layer B becomes large effect and reduces, and the resistance to cutter that collapses when high-speed cutting reduces.
About near the hard coating layer of (Self-crossover crest line portion is till the position of the scope of 100 μ m) point of a knife being formed by above-mentioned thin layer A and the alternately laminated structure (alternately laminated most surface is thin layer A) of thin layer B, the average film thickness of preferred coating A and thin layer B is respectively 0.5～5.0 μ m, by thering is this average film thickness separately, can balancedly improve near resistance to cutter and the mar proof of collapsing of point of a knife.
When the average film thickness of thin layer A and thin layer B exceedes respectively 5 μ m, easily produce and collapse cutter, and average film thickness is separately while being less than 0.5 μ m, in long-term use, cannot bring into play excellent cutting ability, therefore preferred Self-crossover crest line portion is till the locational thin layer A of the scope of 100 μ m and the average film thickness of thin layer B are respectively 0.5～5.0 μ m.
And, same about near hard coating layer point of a knife, till the position of the scope of 100 μ m while measuring, is 2～20 layers in total number of plies of thin layer A and thin layer B, can balancedly improve near resistance to cutter and the mar proof of collapsing point of a knife in Self-crossover crest line portion.
In addition, same about near hard coating layer point of a knife, in Self-crossover crest line portion till the position of the scope of 100 μ m while measuring, at the average film thickness with respect to by thin layer A and the alternately laminated hard coating layer forming of thin layer B, the average film thickness of thin layer A accounts in 50～70% the situation of average film thickness of hard coating layer, can balancedly improve near resistance to cutter and the mar proof of collapsing point of a knife.
In Self-crossover crest line portion till in the locational hard coating layer of the scope of 100 μ m, in the time that the average film thickness of thin layer A and thin layer B is less than 0.5 μ m, when total number of plies of thin layer A and thin layer B exceedes 20 layers, and the ratio of the thin layer A average film thickness shared with respect to the average film thickness of hard coating layer is while being less than 50%, cannot in long-term use, bring into play excellent mar proof, and in the time that the average film thickness of thin layer A and thin layer B exceedes 5.0 μ m, when total number of plies of thin layer A and thin layer B is less than 2 layers, and the ratio of the thin layer A average film thickness shared with respect to the average film thickness of hard coating layer easily produces and collapses cutter while exceeding 70%, therefore, preferably Self-crossover crest line portion is till the locational thin layer A of the scope of at least 100 μ m and the average film thickness of thin layer B are respectively 0.5～5.0 μ m, and total number of plies of preferred coating A and thin layer B is 2～20 layers, and the average film thickness of preferred coating A with respect to the average film thickness of hard coating layer account for its 50～70%.
And, in this invention, position more than the distance 150 μ m of Self-crossover crest line portion, away from the position of point of a knife, without the generation of too considering that cutter is collapsed in inhibition, therefore about hard coating layer, the crystal grain that the fine-grain that can be less than 0.3 μ m with crystallization width accounts for 0～50 length % show that with described thin layer A the crystal grain that identical crystal grain electrical path length distributes forms hard coating layer, and improve mar proof.
In addition, if crystallization width is less than more than the fine-grain of 0.3 μ m accounts for 50 length %, the compressive residual stress in layer increases, easily produce peeling off of film, and, because the impact mar proof naturally damaging of film reduces, the shared ratio of fine-grain that therefore preferred crystallization width is less than 0.3 μ m is below 50 length %.
(d) evaporation of hard coating layer forms
The hard coating layer of this invention for example utilizes the arc ion plating apparatus (AIP device) as shown in the (a) and (b) of Fig. 3 that the temperature of tool base is maintained to 370～450 DEG C, and by making tool base rotation-revolution in AIP device, and carry out evaporation and form apply the magnetic field of regulation between target and tool base in.
For example, cleaned in a side setting of AIP device the cathode electrode forming with Ti electrode by matrix, the target (cathode electrode) that opposite side setting is made up of 80～50at%Al-20～50at%Cr alloy,
First, the tool base being made up of tungsten carbide (WC) base cemented carbide is cleaned, is dried, and be arranged on the turntable in AIP device, under vacuum, between cleaning with Ti electrode and anode electrode, matrix produces the arc discharge of 100A, thereby the bias voltage to apply-1000V of tool base and Bombardment and cleaning is carried out in tool base surface
Then, apply magnetic field, so that in the time that the surperficial maximum field of Al-Cr alloys target is 100mT, also can prevent the generation of the paradoxical discharge being produced to the outer side shifting of target by arc spot,
Then, in device, import nitrogen as reacting gas and be made as the atmosphere pressures of 9.3Pa, the temperature of tool base is maintained to 370～450 DEG C, and bias voltage to apply-50V of tool base, and between Al-Cr alloys target (cathode electrode) and anode electrode, produce the arc discharge of 100A, and supporting tool matrix make its rotation-revolution, and the surperficial maximum field of Al-Cr alloys target is controlled to 45～100mT evaporation thin layer A, in addition, the surperficial maximum field of Al-Cr alloys target is controlled to 0～22mT evaporation thin layer B, by replacing evaporation thin layer A and thin layer B, can form by (the Al with compressive residual stress of the present invention and crystal habit by evaporation, Cr) hard coating layer that N layer forms.
In addition, when the surperficial maximum field of above-mentioned Al-Cr alloys target is that 100mT is when above, in order to prevent the generation of the paradoxical discharge being produced to the outer side shifting of target by arc spot, for example, as shown in Fig. 4 (a), can be solenoid in the rear side of target one side of tool base (not towards) configuration generation source, magnetic field, and adopt that configuration permanent magnet is (for example around target, ferrite lattice) magnetic field applying method, thus, as shown in Fig. 4 (b), in the Distribution of Magnetic Field of target, make recess (representing with " arrow " in Fig. 4 (b)), by arc spot in this segment set, even if thereby be that 100mT is when above at the surperficial maximum field of target, also can prevent the generation of paradoxical discharge.
In the coating tool of this invention, hard coating layer is by (Al, Cr) N layer forms, and the value σ 11 of the compressive residual stress of near rear knife face cutting edge crest line portion or the hard coating layer of rake face and σ 22 maintain (0.5GPa≤σ 11≤4.5GPa in particular range, 0GPa≤σ 22≤4.0GPa), and σ 11 and σ 22 have particular kind of relationship (σ 11-σ 22 >=0.5GPa), in addition, the fine-grain that near hard coating layer cutting edge crest line portion is less than 0.3 μ m by crystallization width accounts for fine-grain that the thin layer A of 0～50 length % and crystallization width be less than 0.3 μ m and accounts for that the thin layer B of 50～100 length % is alternately laminated to be formed, thus at carbon steel, steel alloys etc. are with the excellent resistance to cutter that collapses of performance in the thermogenetic high-speed cutting processing of height, mar proof, and bring into play excellent cutting ability in long-term use.
Brief description of the drawings
The overall schematic that (a) of Fig. 1 is ball end mill, (b) represents the σ 11 of ball end mill front end and the relation of σ 22.
(a) of Fig. 2 is the overall schematic of perpendicular type slotting cutter, (b) represents the relation of σ 11 with the σ 22 of perpendicular type slotting cutter front end.
Fig. 3 represents the schematic diagram of the AIP device for making surface-coated cutting tool of the present invention.
Fig. 4 represent in the present invention for prevent paradoxical discharge generation target is applied to an example of the method in magnetic field, (a) summary of the position relationship of target, solenoid and permanent magnet is shown, the summary of the Distribution of Magnetic Field on the target surface that is formed at tool base side (b) is shown.(a) represent top view, (b) represent side view.
Fig. 5 represent to cut out from the point of a knife of tool base the schematic cross sectional views of knife face side and rake face side.Locating while representing to utilize the mensuration crystallization width that SEM observes in this schematic cross sectional views, i.e. the zone line of each layer and from rear knife face and the μ m of the crest line portion to 50 of intersecting of rake face and the position of 200 μ m.
Detailed description of the invention
Then, according to embodiment, the coating tool of this invention is specifically described.
At this, the situation that is applicable to slotting cutter is described, but be not limited thereto, certainly, certainly also can be applicable to blade, drill bit etc.
[embodiment]
As material powder, preparation has the middle coarse grain WC powder that average grain diameter is 5.5 μ m, and average grain diameter is that particulate WC powder, the average grain diameter of 0.8 μ m is that TaC powder, the average grain diameter of 1.3 μ m is that NbC powder, the average grain diameter of 1.2 μ m is that ZrC powder, the average grain diameter of 1.2 μ m is the Cr of 2.3 μ m
3c
2powder, average grain diameter is the VC powder of 1.5 μ m, average grain diameter is the (Ti of 1.0 μ m, W) C[by quality ratio, TiC/WC=50/50] powder and average grain diameter be the Co powder of 1.8 μ m, and these material powders are fitted in respectively to the mix proportion shown in table 1, further add paraffin and in acetone ball milling mix 24 hours, various pressed compacts taking the pressure punch forming of 100MPa as regulation shape after drying under reduced pressure, these pressed compacts are warming up to the set point of temperature within the scope of 1370～1470 DEG C with the programming rate of 7 DEG C/min in the vacuum atmosphere of 6Pa, at this temperature, keep after 1 hour with stove cool condition sintering, thereby forming, the tool base that formation diameter is 8mm uses pole sintered body, and by grinding, by described pole sintered body, to produce respectively the diameter × length with cutting blade be 6mm × 13mm that size and helical angle are WC base cemented carbide tool base processed (slotting cutter) A～C of the twolip spherical form of 30 degree, and there is WC base cemented carbide tool base processed (slotting cutter) D of Double-blade straight angular shape, E.
Produce respectively by the following method as the surface of coating tool of the present invention and be coated slotting cutter 1～15(hereinafter referred to as the present invention 1～15):
(a) the above-mentioned each tool base A～E of Ultrasonic Cleaning in acetone, and be arranged on central shaft on the turntable of the AIP device shown in Fig. 3 to radial direction on the position apart from predetermined distance with the state that is dried along peripheral part, at a side configuration Bombardment and cleaning Ti cathode electrode of AIP device, configure the target (cathode electrode) being formed by the Al-Cr alloy of composition requirement at opposite side
(b) first, when remaining vacuum to carrying out exhaust in installing, with heater, tool base is heated to after 500 DEG C, to the DC offset voltage of apply-1000V of the tool base being rotated in rotation on described turntable, and the electric current that makes 100A between Ti cathode electrode and anode electrode flows through and produces arc discharge, and Bombardment and cleaning is carried out in tool base surface
(c) then, as shown in Figure 4, at the back side of target configuration solenoid, and the above-mentioned Al-Cr alloys target that disposes ferrite lattice around target is applied to the various magnetic fields shown in table 2, so that surperficial maximum field is in the scope of 0～22mT and 45～100mT,
(d) then, in device, import nitrogen as reacting gas and be made as the reaction atmosphere of 9.3Pa, and the temperature of the tool base being rotated in rotation on described turntable is maintained within the scope of 370～450 DEG C and the DC offset voltage of apply-50V, and the electric current that makes 100A flows through between described Al-Cr alloys target and anode electrode and produces arc discharge, apply magnetic field so that surperficial maximum field within the scope of 45～100mT, thereby evaporation thin layer A, and apply magnetic field so that surperficial maximum field within the scope of 0～22mT, thereby evaporation thin layer B, by replacing evaporation thin layer A and thin layer B, surperficial evaporation in tool base forms by having forming shown in table 1, (the Al of alternatively layered structure and target film thickness, Cr) hard coating layer that N layer forms.
Utilize EPMA in Self-crossover crest line portion till five somes mensuration are carried out in the position of the scope of 100 μ m, go out forming of hard coating layer by their mean value calculation.
Comparative example:
Taking relatively as object, for above-mentioned tool base (slotting cutter) A～E, (for example change the condition of (c), (d) in above-described embodiment, the size that do not form magnetic field, does not form magnetic field, magnetic field configuring ferrite lattice around target is outside the scope of 0～22mT or 45～100mT etc.), and under other conditions condition identical with embodiment, produce respectively the coated slotting cutter (hereinafter referred to as comparative example 1～15) in surface of coating tool as a comparative example.
About the present invention 1～15 by above-mentioned making and comparative example 1～15, with the Al of rear knife face and the complex nitride layer of Cr that are tangential on apart from the cutting edge crest line portion of 2.0mm from slotting cutter front end within the scope of the radius 50 μ m of a point in, utilize 2D method (two-dimensional x-ray diffraction/full debye ring fitting process) to measure compressive residual stress σ 11, the σ 22 of both direction.σ 11 is and the compressive residual stress that intersects the parallel direction of crest line portion of rear knife face and rake face, and σ 22 is the compressive residual stress of the direction orthogonal with above-mentioned σ 11.
2D method (two-dimensional x-ray diffraction/full debye ring fitting process) refers to, all diffracted rays that expand by detect two dimension simultaneously, thereby according to the method for the deformation calculation total stress component of full debye ring.
About σ 11, σ 22, carry out respectively five points and measure, and using the mean value of this measured value as σ 11, σ 22.
Shown in table 2, table 3 by the value of the above-mentioned σ that measures, calculates 11, σ 22 and σ 11-σ 22.
In addition, concrete residual stress analysis condition is roughly as follows.
Analytic method: 2D method (two-dimensional x-ray diffraction/full debye ring fitting process)
X-ray source: Cu-K alpha ray, output=50kV, 22mA
X-ray diffraction peak value: the peak value that uses 2 θ=80 ° (220) face
In addition, utilize Poisson's ratio=0.200 of (Al, Cr) N, Young's modulus=300000MPa calculates residual stress.
In addition, about the present invention 1～15 by above-mentioned making and comparative example 1～15, first, respectively for Self-crossover crest line portion till locational thin layer A, the thin layer B of the scope of at least 100 μ m obtain the mean value that crystallization width is less than the fine-grain ratio of 0.3 μ m, and, obtain Self-crossover crest line portion is less than the fine-grain ratio of 0.3 μ m mean value apart from crystallization width in locational hard coating layers more than 150 μ m.
In the ratio that is less than the fine-grain of 0.3 μ m shown in table 2, table 3 by the each locational crystallization width of said determination.
Assay method is as follows more specifically.
Cut out the cross section of rear knife face side from tool base point of a knife, utilize SEM to observe this cross section.Cross section roughly shown in Fig. 5.Zone line between thin layer A and the boundary portion of thin layer B is (in the time that each thin layer is present in Surface and interface, for the zone line between the boundary portion between Surface and interface and thin layer A, B), draw a straight line parallel with tool base surface, and be crystallization width by the distance definition between crystal boundary.Measure by the crest line portion of intersecting from rear knife face and rake face apart from crystallization width centered by the position of 50 μ m, that be present in the crystallization within the scope of width 100 μ m, and the width sum of crystallization that crystallization width is less than to 0.3 μ m with respect to the ratio of measured all crystallization width sums as " Self-crossover crest line portion is till the ratio (length %) of the fine-grain that is less than 0.3 μ m in the position of the scope of 100 μ m ".And, measure crystallization width centered by the Self-crossover crest line portion distance position of 200 μ m, that be present in the crystallization within the scope of width 100 μ m, and the crystallization width sum that crystallization width is less than to 0.3 μ m with respect to the ratio of measured all crystallization width sums as " ratio (length %) of the fine-grain that is less than 0.3 μ m in positions more than the distance 150 μ m of Self-crossover crest line portion ".
In addition, about the present invention 1～15 by above-mentioned making and comparative example 1～15, measure, calculate thin layer A and thin layer B average film thickness, Self-crossover crest line portion till the locational thin layer A of the scope of 100 μ m and total number of plies of thin layer B and the average film thickness of thin layer A with respect to the ratio of the average film thickness of hard coating layer.
At these measured values, calculated value shown in table 2, table 3.
Concrete assay method is, as shown in Figure 5, the cross section of knife face side from tool base point of a knife cuts out, utilizes SEM to observe this cross section, measure from rear knife face and distance 25 μ m, the 50 μ m of the crest line portion of intersecting of rake face and the locational thickness of 75 μ m, and using this mean value of 3 as average film thickness.
[table 1]
[table 2]
Then, to the slotting cutter of the invention described above 1～15 and comparative example 1～15,
Implement the high speed groove cutting processing experiment of carbon steel with following condition (being called machining condition A),
The sheet material of the JISS55C of workpiece-planar dimension: 100mm × 250mm, thickness: 50mm,
Cutting speed: 284m/min,
Groove depth (cutting-in amount): 2.0mm,
Cutting width: 0.3mm,
Feed speed: 2000mm/min,
Length of cut: 340m,
In addition, implement stainless high speed groove cutting processing experiment with following condition (being called machining condition B),
The sheet material of the JISSUS304 of workpiece-planar dimension: 100mm × 250mm, thickness: 50mm,
Cutting speed: 100m/min,
Groove depth (cutting-in amount): 10mm,
Cutting width: 1mm,
Feed speed: 450mm/min,
Length of cut: 90m,
And measure the wear of the tool flank width of cutting edge.
In addition, wear of the tool flank width is considered as reaching the life-span while exceeding 0.1mm, and record length of cut now.This measurement result is shown in to table 4.
[table 4]
In table, the * in comparative example hurdle represents because collapsing the length of cut (m) till service life (more than wear of the tool flank width 0.1mm) that reaches that cutter, aggravation damaged, wearing and tearing cause
From the result shown in table 4, the coating tool of the present invention that there is the value of the σ 11, the σ 22 that specify in the present invention, σ 11-σ 22 and possess the thin layer A, the thin layer B that specify in the present invention carbon steel, stainless steel etc. with the thermogenetic high-speed cutting processing of height in excellent resistance to of performance collapse cutter and bring into play excellent mar proof.
With respect to this, comparative example coating tool outside the scope that the value of the known compressive residual stress at hard coating layer specifies in the present invention or do not there is the present invention in the comparative example coating tool of the thin layer A, the thin layer B that specify, because collapsing the generation of cutter or the reduction of mar proof, can within the shorter time, reach service life.
Utilizability in industry
As mentioned above, the coating tool of this invention not only can show excellent cutting ability for a long time in the high speed such as carbon steel, steel alloy machining, and also can show for a long time excellent cutting ability in machining under the usual conditions that are supplied to ordinary steel etc., and, not only can be suitable for and make Milling Process coating tool, can also be suitable for and make turning processing, drill bit processing coating tool.
Claims (4)
1. a surface-coated cutting tool, its surperficial evaporation in the tool base being made up of tungsten carbide base carbide alloy forms the hard coating layer being made up of the complex nitride layer of Al and Cr, and this surface-coated cutting tool is characterised in that,
(a) in above-mentioned hard coating layer, average film thickness is 1～10 μ m, and Cr shared content in the total amount of Al and Cr compares taking atomic ratio measuring as 0.2～0.5,
(b) surface on the rear knife face of above-mentioned hard coating layer or on rake face, using in the time that the position of the distance 50 μ m of the crest line portion of intersecting of rear knife face and rake face utilizes 2D method to measure residual stress in the scope of the radius 50 μ m of center, meet the relation of 0.5GPa≤σ 11≤4.5GPa with the above-mentioned compressive residual stress σ 11 that intersects the parallel direction of crest line portion, meet the relation of 0GPa≤σ 22≤4.0GPa with the compressive residual stress σ 22 of the orthogonal direction of above-mentioned σ 11, and, above-mentioned σ 11 and σ 22 meet the relation of σ 11-σ 22 >=0.5GPa
(c) from above-mentioned intersection crest line portion till the position of the scope of at least 100 μ m, the fine-grain that above-mentioned hard coating layer is less than 0.3 μ m by crystallization width accounts for fine-grain that the thin layer A of 0～50 length % and crystallization width be less than 0.3 μ m and accounts for that the thin layer B of 50～100 length % is alternately laminated to be formed, the difference of the ratio of the fine-grain of thin layer A and thin layer B is more than 10 length %, and alternately laminated most surface is made up of thin layer A, on the other hand, in the position more than the above-mentioned intersection crest line distance 150 μ m of portion, the fine-grain that in above-mentioned hard coating layer, crystallization width is less than 0.3 μ m accounts for 0～50 length %.
2. surface-coated cutting tool according to claim 1, is characterized in that,
In Self-crossover crest line portion, till the position of the scope of 100 μ m, the average film thickness of above-mentioned thin layer A and thin layer B is respectively 0.5～5.0 μ m.
3. surface-coated cutting tool according to claim 2, is characterized in that,
In Self-crossover crest line portion, till the position of the scope of 100 μ m, total number of plies of above-mentioned thin layer A and thin layer B is 2～20 layers.
4. surface-coated cutting tool according to claim 3, is characterized in that,
In Self-crossover crest line portion, till the position of the scope of 100 μ m, the average film thickness of the thin layer A ratio shared with respect to the average film thickness of hard coating layer is 50～70%.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107530786A (en) * | 2015-04-27 | 2018-01-02 | 株式会社泰珂洛 | Coated cutting tool |
| CN108188419A (en) * | 2017-12-04 | 2018-06-22 | 沈阳兴华航空电器有限责任公司 | For the cutoff tool of electric connector contact pin reversing processing and reversing processing method |
| CN108723404A (en) * | 2017-04-21 | 2018-11-02 | 株式会社泰珂洛 | Coated cutting tool |
| CN114641362A (en) * | 2019-11-06 | 2022-06-17 | 千贝克科技有限公司 | Chamfering tool and chamfering method for workpiece |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005028520A (en) * | 2003-07-07 | 2005-02-03 | Tungaloy Corp | Hard film coated tool |
| CN101090790A (en) * | 2004-12-28 | 2007-12-19 | 住友电工硬质合金株式会社 | Coated cutting tool and manufacturing method thereof |
| JP2008284624A (en) * | 2007-05-15 | 2008-11-27 | Sumitomo Electric Hardmetal Corp | Surface coated cutting tool |
| CN101842179A (en) * | 2008-04-30 | 2010-09-22 | 住友电气工业株式会社 | The cutting element that the surface is coated |
| JP5340028B2 (en) * | 2009-05-18 | 2013-11-13 | 京セラ株式会社 | Cutting tools |
-
2014
- 2014-01-24 CN CN201410034933.2A patent/CN103962589B/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005028520A (en) * | 2003-07-07 | 2005-02-03 | Tungaloy Corp | Hard film coated tool |
| CN101090790A (en) * | 2004-12-28 | 2007-12-19 | 住友电工硬质合金株式会社 | Coated cutting tool and manufacturing method thereof |
| JP2008284624A (en) * | 2007-05-15 | 2008-11-27 | Sumitomo Electric Hardmetal Corp | Surface coated cutting tool |
| CN101842179A (en) * | 2008-04-30 | 2010-09-22 | 住友电气工业株式会社 | The cutting element that the surface is coated |
| JP5340028B2 (en) * | 2009-05-18 | 2013-11-13 | 京セラ株式会社 | Cutting tools |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107530786A (en) * | 2015-04-27 | 2018-01-02 | 株式会社泰珂洛 | Coated cutting tool |
| CN107530786B (en) * | 2015-04-27 | 2020-05-05 | 株式会社泰珂洛 | Coated cutting tool |
| CN108723404A (en) * | 2017-04-21 | 2018-11-02 | 株式会社泰珂洛 | Coated cutting tool |
| CN108188419A (en) * | 2017-12-04 | 2018-06-22 | 沈阳兴华航空电器有限责任公司 | For the cutoff tool of electric connector contact pin reversing processing and reversing processing method |
| CN114641362A (en) * | 2019-11-06 | 2022-06-17 | 千贝克科技有限公司 | Chamfering tool and chamfering method for workpiece |
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