CN103173761B - Cutting tool improving coating structure and preparation method thereof - Google Patents

Cutting tool improving coating structure and preparation method thereof Download PDF

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CN103173761B
CN103173761B CN201110439260.5A CN201110439260A CN103173761B CN 103173761 B CN103173761 B CN 103173761B CN 201110439260 A CN201110439260 A CN 201110439260A CN 103173761 B CN103173761 B CN 103173761B
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transition layer
layer
coating
cutting tool
thickness
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CN103173761A (en
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陈响明
刘王平
王社权
李秀萍
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Zhuzhou Cemented Carbide Cutting Tools Co Ltd
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Zhuzhou Cemented Carbide Cutting Tools Co Ltd
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Abstract

The invention discloses a kind of cutting tool improving coating structure, the coating comprising matrix and cover on matrix, coating includes inner layer B, transition layer C and outer D from inside to outside; Inner layer B is made up of transition element and the nonmetal compound-material formed, and transition layer C includes transition layer C1 and/or transition layer C2; Transition layer C1, C2 all form primarily of the carbon nitrogen oxide of titanium, and outer D has the α-Al of single-phase 2o 3structure, the thickness of outer D is d=0.5 μm ~ 4 μm, and its mean grain size S is 0.2 μm≤S≤0.5 μm.Its preparation method first prepares tool matrix, then in same coating cycle, deposits inner layer B, transition layer C2, transition layer C1 and outer D successively thereon; Making is completed again after surface treatment.Cutting tool hardness of the present invention is high, wear resistance good, and the machining of the materials such as steel, stainless steel, cast iron has excellent cutting ability.

Description

Cutting tool improving coating structure and preparation method thereof
Technical field
The invention belongs to metal cutting process field, particularly relate to a kind of cutting tool and preparation technology thereof of band coating.
Background technology
Machine tools has the history more than 20 years with chemical Vapor deposition process (CVD) deposition of aluminium oxide coatings.Wear-resistant and the corrosion resistance nature of aluminum oxide excellence is discussed in the literature widely.The CVD aluminum oxide coating layer be deposited on cutting tool common are α-Al 2o 3with κ-Al 2o 3two kinds of phases, the Al when CVD produces 2o 3except stable α, also has κ and θ phase, CVD κ-Al 2o 3grain size is 0.5 μm ~ 1.0 μm, and is generally column crystal, κ-Al 2o 3in almost there is no dislocation and hole.κ-the Al when cutting rolled steel 2o 3there is good cutting ability; Its shortcoming is when cutting, and due to the high pressure that localized hyperthermia and extruding are formed, also can cause κ-Al 2o 3to α-Al 2o 3transformation because α-Al 2o 3compare κ-Al 2o 3finer and closely (be followed successively by 3.99g/cm 3and 3.67g/cm 3), change the contraction of rear nearly 8%, thus at α-Al 2o 3the obvious crackle of middle appearance, α-Al 2o 3with κ-Al 2o 3interface mechanical degradation, this will cause κ-Al 2o 3the tipping of coating.Therefore κ-Al 2o 3be not suitable for the cutting under high-speed and high-efficiency.Therefore the modern preferred α of cutter coat-Al 2o 3.
α-Al 2o 3being commonly called as corundum, is steady oxide, have the advantages such as high-temperature stability is good, anti-oxidant, hardness is high, wear-resistant, but CVD α is-Al 2o 3be generally equiax crystal, crystal grain is much larger than κ-Al 2o 3, must pass whole coating greatly, according to the difference of coat-thickness, grain size is between 1 μm ~ 6 μm.Test proves α-Al 2o 3can at Ti 2o 3surface and the bonding surface forming core of (Ti, Al) (C, O), or utilize CO/CO 2the oxidation potential that mixed gas controls deposition atmosphere makes α-Al 2o 3forming core.In these all methods, its basic concept only can generate κ-Al on the surface of TiC, TiN, TiCN, the TiCNO with fcc structure 2o 3.In many prior art products, when nucleation can not be controlled completely, the α-Al deposited 2o 3layer has at least part to be by κ-Al 2o 3formed through phase in version.This α-Al 2o 3layer is made up of crystal grain that the is thick and crackle that changes.With crystallite α-Al 2o 3α-the Al of composition 2o 3layer is compared, and this mechanical property reduces greatly.Therefore need to improve prior art, with control α-Al 2o 3the forming core of layer and growth, obtain the α-Al with ideal structure 2o 3coating.
In the industry to polycrystalline α-Al 2o 3control started from for 20 end of the centurys, as in patent US5137774 adopt (Al xti y) (O wc z) y: x=2 ~ 4, z: w=0.6 ~ 0.8 modified layer is at α-Al 2o 3layer surface deposition κ-Al 2o 3coating.After this CVD α-Al 2o 3deposition technique is all utilize control forming core to obtain the α-Al with specific preferential growth orientation 2o 3.As ZL93121032.1 discloses a kind of coated cutting tool, scribble the cutter hub of one or more layers infusibility layer at least partly, one deck is wherein had at least to be aluminum oxide, the thickness of described alumina layer is d=0.5 μm ~ 25 μm, and be made up of the α-structure of single-phase, its grain-size (s) is: 0.5 μm of < S < 1 μm (for 0.5 μm of < d < 2.5 μm) and 0.5 μm of < S < 3 μm (for 2.5 μm of < d < 25 μm), for etc. (012) direction of growth in Jinping face, the Structure index of alumina layer is greater than 1.3 (preferably 1.5).
ZL94119184.2 discloses a kind of coated cutting tool, has the cutter hub of the thick coating of < 20 μm, and described coating comprises the alumina layer that at least one layer thickness is 1 ~ 10 μm, the essentially no cooling crack of this alumina layer.Coating at least comprises one deck alumina layer, and alumina layer is by the single-phase α-Al having texture in (110) direction 2o 3composition, its texture coefficient is greater than 1.5.It is 2 μm ~ 8 μm that this alumina layer comprises length, and length/width is than the flaky crystalline grain being 1 ~ 10.
ZL95191221.6 discloses a kind of oxide coated cutting tool, it scribbles one or more layers at least partly on tool matrix, wherein at least one deck is the infusibility layer of aluminum oxide, the thickness of this alumina layer is 0.5 ~ 25 μm, its grain-size (s) is: 0.5 μm of < S < 1 μm (for 0.5 μm of < d < 2.5 μm) and 0.5 μm of < S < 4 μm (for 2.5 μm of < d < 25 μm), and but there is in (104) direction the unidirectional α-structure composition of texture, texture coefficient is greater than 1.5 (preferably 2.5, 3.0).
These patents are by control α-Al 2o 3the oxidizing potential (lower than the water of 20PPM, being preferably lower than the water of 5PPM) of the hydrogen carrier gas before forming core, and control α-Al 2o 3in nucleation process, reactant gases passes into order, obtains the aluminum oxide coating layer with (012), (110), (104) growth texture respectively; The patents such as ZL96110196.2, CN96100514.9 also disclose the alumina coated cutting tool with (012), (110) or (104) growth texture.
US20070099029 adopts the TiAlCNO middle layer having Al% content and increasing towards surface direction, and this middle layer adopts and adds CO containing the process of aluminium gas pulses 2oxide treatment carry out surface modification, prepare the α-Al with strong (012) growth texture that forming core and growth are controlled completely 2o 3coating, this coating is the column α-Al of 2.5 ~ 3.5 at the texture coefficient TC (hkl) of (012) and (024) 2o 3brilliant composition, the reflection of using has (012) (104) (110) (113) (024) (116), and TC (104) (110) (113) (116) are less than 0.4.
US20060199026,20060115662, the patent such as US20070104945, US200601412271 by have TiAlCNO interlayer surfaces that Al% content increases towards surface direction adopt the oxide treatment containing the process of aluminium gas pulses and oxygen-containing gas to carry out the optimization of surface modification technology and parameter, prepared the α-Al with (104), (110), (006), (116) growth texture by force respectively 2o 3coating.
As everyone knows, the hardness of polycrystalline material (comprising coating) observes Hall-Petch formula usually: wherein H is the hardness of polycrystalline material, and H ° is the hardness of monocrystal material, and C is material constant, and d is grain-size.Can find out that the grain fineness number by reducing coating can improve the hardness of material from formula.But, when processing the very tiny nano material of grain-size, the effect that the increase of crystal boundary proportion in the material brings must be considered.Much research shows, when process has the nanocrystalline mechanically resistant material of very little grain-size, to find a kind of reverse Hall-Petch relation.Can be clearly seen that in US6472060, even if improve room temperature hardness when grain-size is reduced to nanocrystal region, the performance of anti-crescent hollow abrasion also reduces.This can explain with the increase of Grain Boundary Sliding amount.Therefore, when considering to improve coating wear resistance by crystal grain thinning, grain fineness number should remain on the top of nanocrystal.
In sum, all prior aries are all utilize transition layer technical controlling α-Al 2o 3forming core obtains the α-Al with specific growth texture 2o 3coating, and on directly affecting α-Al 2o 3the research that the grain fineness number of coating microhardness and abrasion resistance properties is not deep and description, do not consider α-Al 2o 3the grain fineness number of coating is to the influence of coating and coated cutting tool performance.We are necessary to do further adjustment, combination and design to the coating microstrueture of cutting tool, to improve the hardness of coating, wear resisting property and stability.
Summary of the invention
The technical problem to be solved in the present invention overcomes the deficiencies in the prior art, there is provided cutting tool and its preparation technology of the improvement coating structure that a kind of hardness is high, wear resistance is good, cutting tool of the present invention has excellent cutting ability in the machining of the materials such as steel, stainless steel, cast iron.
For solving the problems of the technologies described above, the present invention proposes following technical scheme:
A kind of cutting tool improving coating structure, (coated substrate can be Wimet, sintering metal to comprise matrix A, the material such as nonmetallic ceramics, PCD or CBN) and the coating that covers at least partly on matrix A, described coating includes inner layer B, transition layer C and outer D from inside to outside;
The compound-material that described inner layer B forms primarily of the transition element in the periodic table of elements and non-metallic element is formed, described transition element is selected from least one in IVB race in the periodic table of elements, VB race, group vib, and described non-metallic element is selected from least one in carbon, nitrogen, oxygen, boron;
It is characterized in that, described transition layer C includes transition layer C1 and/or transition layer C2 from outside to inside;
Described transition layer C1 is primarily of the carbon nitrogen oxide TiC of titanium x1n y1o z1composition, described x1, y1, z1 represent TiC respectively x1n y1o z1the atomic percent of middle C, N, O, and meet 0.5≤z1/ (x1+y1+z1)≤1, y1≤x1≤z1;
Described transition layer C2 is primarily of the carbon nitrogen oxide TiC of titanium x2n y2o z2composition, described x2, y2, z2 represent TiC respectively x2n y2o z2the atomic percent of middle C, N, O, and meet 0.5≤x2/ (x2+y2+z2)≤1,
Described outer D has the α-Al of single-phase 2o 3structure, the thickness of outer D is d=0.5 μm ~ 4 μm, and its mean grain size S is 0.2 μm≤S≤0.5 μm.
The cutting tool of above-mentioned improvement coating structure, in described transition layer C1, described x1, y1, z1 preferably meet 0.5≤z1/ (x1+y1+z1)≤0.8; Described transition layer C1 is preferably sheet or granular nanocrystalline structure, and the grain fineness number of described transition layer C1 is preferably less than 200nm, and the preferred thickness of described transition layer C1 is less than 0.5 μm.
The cutting tool of above-mentioned improvement coating structure, in described transition layer C2, described x2, y2, z2 preferably meet 0.8≤x2/ (x2+y2+z2)≤1 (preferred, described x2=1, y2=0, z2=0, namely transition layer C2 is TiC coating.); Described transition layer C2 is preferably the nanometer equant grains structure of discrete distribution, and the grain fineness number of described transition layer C2 is preferably less than 200nm, and the thickness of described transition layer C2 is less than 0.5 μm (being more preferably less than 0.3 μm).
In the cutting tool of above-mentioned improvement coating structure, one or more preferably in carbide, nitride, boride, oxide compound, carbonitride, boron nitride, boron carbonitride of the compound-material of described inner layer B, have at least one to have column crystal or fibrous crystal structure in described compound-material.Preferred, described inner layer B comprises one deck MT-TiCN, and its thickness is greater than 3 μm.
In the cutting tool of above-mentioned improvement coating structure, the total thickness of described transition layer C is preferably 0.1 μm ~ 0.8 μm.
As to the above-mentioned further improvement improving the cutting tool of coating structure, one deck is also coated with containing Ti Compound Identification layer E in the outside of described outer D, this label layer is preferably TiN or TiCN, and the described thickness containing Ti Compound Identification layer is preferably 0.1 μm ~ 1 μm.
As a total technical conceive, the present invention also provides a kind of preparation method of cutting tool of above-mentioned improvement coating structure, comprise the following steps: the tool matrix first preparing Wimet, sintering metal, nonmetallic ceramics, PCD or CBN material, then deposits following coating on described tool matrix in same coating cycle:
(1) inner layer B of conventional CVD deposit those on described tool matrix A is utilized;
(2) the transition layer C2 of conventional HT-CVD technique deposit those in described inner layer B is utilized;
(3) the transition layer C1 of conventional HT-CVD method deposit those on described transition layer C2 is utilized;
(4) the outer D of conventional HT-CVD method deposit those on described transition layer C1 is utilized;
(5) sandblasting or siliceous nylon brush polishing is adopted to carry out surface treatment to above-mentioned obtained hard alloy coated blade;
(6) utilize conventional CVD deposit again on outer D one deck above-mentioned containing Ti Compound Identification layer; Again after surface treatment, remove aforementioned label layer at the regional area of the cutting edge of described coated chip, rake face or rear knife face and outer B is exposed, complete making.
As the further improvement to above-mentioned preparation method, the deposition of described outer D refers to and utilize CO, CO on this transition layer C1 2and H 2the mixed gas of S is optimized forming core to transition layer C1, then after the aluminum oxide forming core effect of outer D, utilizes H 2s or SF 6the growth of aluminum oxide coating layer is optimized, obtains α-Al described in compact grained 2o 3structure; The deposition process of described outer D controls 900 DEG C ~ 1020 DEG C temperature ranges.
Compared with prior art, the invention has the advantages that:
1. the outer D of cutting tool of the present invention is designed to the α-Al with single-phase 2o 3the oxide coating of the Ultra-fine Grained of structure, is preferably pure α-Al 2o 3coating, the thickness of coating is d=0.5 μm ~ 4 μm, and its grain fineness number S is 0.2 μm≤S≤0.5 μm.The grain fineness number design of this kind of outer D is combined by the coating structure improved-type with the present invention, and this makes cutting tool of the present invention have excellent anti-oxidant and crater wear resistance energy.The present invention is by the outer α of optimized restriction-Al 2o 3grain fineness number, this not only further increases top layer α-Al 2o 3the homogeneity of coating, hardness and abrasion resistance properties, and avoid a kind of reverse Hall-Petch phenomenon because of the too small appearance of grain-size, and the decline of the hardness caused and abrasion resistance properties.
2. the transition layer C2 that cutting tool of the present invention is arranged effectively can improve forming core homogeneity and the density of transition layer C1, avoids single TiO, TiCO thin layer or TiAlCO thin layer problem pockety on the surface of inner layer B; Meanwhile, transition layer C2 has the TiC nanometer equant grains layer of discrete distribution, and it can improve the surface irregularity that inner layer B is formed in process of growth to a certain extent, reduces the roughness of coating; The present invention, by being optimized the composition of transition layer C2 (0.5≤x2/ (x2+y2+z2)≤1), effectively can improve the isometry degree of transition layer C2; And the coarsening of transition layer C2 crystal grain can be avoided to the optimization of transition layer C2 thickness, and then avoid the decline of external oxide coated grains density, avoid the reduction of strength of coating and anchoring strength of coating.
3. cutting tool of the present invention is also provided with transition layer C1, by being optimized its thickness, coarsening and the abnormal growth of transition layer C1 crystal grain can be avoided, thus obtain the transition layer C1 of fine uniform, and then by induced nucleation effect, even, highdensity external oxide coating forming core layer can be obtained thereon; Meanwhile, the present invention is by being optimized (0.5≤z1/ (x1+y1+z1)≤1 to the composition of transition layer C1, y1≤x1≤z1), desirable crystalline structure can be obtained, such as this transition layer C1 can control the forming core of the oxide crystal with corundum structure, and this is for the outer field α-Al of preparation 2o 3or its doping coating has vital role.
4. in the preferred cutting tool of the present invention skin be also provided with color be different from internal layer containing Ti Compound Identification layer, this layer can adopt CVD or PVD method to deposit, and brushing method or spraying method also can be adopted to apply.For ensureing the cutting ability of cutter, label layer is partly or entirely removed on cutting edge, rake face or rear knife face.
In addition, the microtexture waiting the transition layer C2 of axle high-carbon and the transition layer C1 of thin sheet to be formed thin in the present invention, this structure effectively can improve the Enhancing Nucleation Density of transition layer C1 and the homogeneity of distribution, thus improves outer α-Al 2o 3the Enhancing Nucleation Density of the oxide coating of structure, crystal grain thinning, improve the homogeneity of surface oxides coating, hardness and abrasion resistance properties, visible, adopt the transition layer with suitable construction to contribute to providing on cutter and have desirable microstructural oxide coating, and then improve the cutting ability of cutter on the whole.
Accompanying drawing explanation
Fig. 1 is the structural representation of cutting tool in the embodiment of the present invention 1 ~ 4.
Fig. 2 is the scanning electron photomicrograph (magnification is respectively 10000) of the outer D of cutting tool in the embodiment of the present invention 1.
Fig. 3 is the scanning electron photomicrograph (magnification is respectively 30000) of the transition layer C1 of cutting tool in the embodiment of the present invention 1.
Fig. 4 is the scanning electron photomicrograph (magnification is respectively 10000) of the outer D of cutting tool in the embodiment of the present invention 3.
Fig. 5 is the scanning electron photomicrograph (magnification is respectively 10000) of the outer D contrasting cutting tool one in the specific embodiment of the invention.
Fig. 6 is the scanning electron photomicrograph (magnification is respectively 10000) of the outer D contrasting cutting tool two in the specific embodiment of the invention.
Fig. 7 is the scanning electron photomicrograph (magnification is respectively 10000) of the transition layer C1 contrasting cutting tool two in the specific embodiment of the invention.
Marginal data:
1, matrix A; 2, coating; 21, inner layer B; 22, transition layer C; 221, transition layer C1; 222, transition layer C2; 23, outer D.
Embodiment
Embodiment 1:
The cutting tool improving coating structure of the present invention as shown in Figure 1, the coating 2 comprising matrix A1 and cover at least partly on matrix A1, coating 2 at least includes inner layer B 21, transition layer C22 and outer D23 from inside to outside.
Wherein:
Inner layer B 21 is formed primarily of MT-TiCN material, and thickness is 6 μm;
Outer D23 is primarily of α-Al 2o 3material is formed, and thickness d=4 μm, outer D23 is the oxide coating of Ultra-fine Grained, the α-Al of outer D 2o 3mean grain size S is 0.46 μm;
Transition layer C22 includes transition layer C1 221 and transition layer C2 222 from outside to inside:
Transition layer C1 221 is primarily of the carbon nitrogen oxide TiC of titanium x1n y1o z1composition (is specially TiC 0.5o 0.5), x1, y1, z1 represent TiC respectively x1n y1o z1the atomic percent of middle C, N, O, and x1=0.5, y1=0, z1=0.5, z1/ (x1+y1+z1)=0.5; Transition layer C1 is sheet (or granular) nanocrystalline structure, and the thickness of transition layer C1 is 0.2 μm, and the grain fineness number of transition layer C1 is less than 200nm;
Transition layer C2 222 is primarily of the carbon nitrogen oxide TiC of titanium x2n y2o z2composition (being specially TiC), x2, y2, z2 represent TiC respectively x2n y2o z2the atomic percent of middle C, N, O, and x2=1, y2=0, z2=0, and x2/ (x2+y2+z2)=1; Transition layer C2 is the nanometer equant grains structure of discrete distribution, and the thickness of transition layer C2 is 0.2 μm, and the grain fineness number of transition layer C2 is less than 200nm.
The cutting tool of above-mentioned the present embodiment prepares mainly through following methods:
(1) hard alloy substrate is prepared: first with ball mill, the WC powder of 10wt%Co, 12wt%Ti and Ta cubic carbonitride and surplus is passed through wet mixing 20h, compound is dry, be pressed into pressed compact, pressed compact is sintered into inserted tool matrix, wet abrasive blasting process is adopted to its surface and cutting edge; Then on described tool matrix, in same coating cycle, following coating is deposited respectively:
(2) inner layer B 21 of conventional CVD deposit those on tool matrix A1 is utilized;
(3) the transition layer C2 222 (TiC) of conventional HT-CVD technique deposit those in inner layer B 21 is utilized;
(4) the transition layer C1 221 (TiC of conventional HT-CVD technique deposit those on transition layer C2 is utilized 0.5o 0.5);
(5) the outer D23 (α-Al of following method deposit those on transition layer C1 221 is adopted 2o 3): transition layer C1 deposited before the aluminum oxide forming core effect of outer D; The deposition of outer D23 refers to and utilize CO, CO on this transition layer C1 2and H 2the mixed gas of S is optimized forming core to transition layer C1, then after the aluminum oxide forming core effect of outer D23, utilizes H 2s (or SF 6) growth of aluminum oxide coating layer is optimized, obtain α-Al described in compact grained 2o 3structure; The deposition process of outer D23 controls at 1000 DEG C;
(6) sandblasting or siliceous nylon brush polishing is adopted to carry out surface treatment, surface roughness Ra=0.2 μm that the length of 300 μm records to above-mentioned obtained hard alloy coated blade.
In the preparation method that the present embodiment is above-mentioned, CVD coating furnace is when depositing various coating, and its atmosphere composition, temperature and pressure control as shown in table 1 below, and the thickness of each layer coating is then controlled by adjustment depositing time.
Table 1: the process parameter control of the cutting tool in embodiment 1 in coating furnace
The coating substance adopting XRD obtained to the present embodiment 1 carries out qualitative analysis mutually; Analyze the surface microstructure of top layer oxide outer layer D23 and transition layer C1 221 with SEM and EDS, result respectively as shown in Figure 2 and Figure 3; The mean grain size of top layer oxide outer layer D23 is measured: on photo, arbitrarily draw three parallel straight lines (length is L μm) by trilinear method, counting lines pass the number n of crystal boundary, then mean grain size d is L/n, calculates α-Al in the present embodiment mesectoderm D 23 thus 2o 3mean grain size S be 0.46 μm; Scratch method is adopted to measure the bonding strength of the coating that the present embodiment obtains.
Embodiment 2:
The cutting tool improving coating structure of the present invention as shown in Figure 1, its coating structure, moiety, microcosmic composition etc. are all identical with the cutting tool in embodiment 1, are only outer α-Al 2o 3with embodiment 1 slightly difference.In the present embodiment, the thickness d of outer D is 2 μm, and mean grain size S is 0.4 μm.The preparation method of the present embodiment 2 is substantially the same manner as Example 1, only need do accommodation on processing parameter.
Embodiment 3:
The cutting tool improving coating structure of the present invention as shown in Figure 1, the coating 2 comprising matrix A1 and cover at least partly on matrix A1, coating 2 at least includes inner layer B 21, transition layer C22 and outer D23 from inside to outside;
Wherein:
Inner layer B 21 is formed primarily of MT-TiCN material, and thickness is 4 μm;
Outer D23 is primarily of α-Al 2o 3material is formed, and thickness is d=3 μm, and outer D23 is the oxide coating of Ultra-fine Grained, the α-Al of outer D 2o 3mean grain size S is 0.49 μm;
Transition layer C22 includes transition layer C1 221 and transition layer C2 222 from outside to inside:
Transition layer C1 221 is primarily of the carbon nitrogen oxide TiC of titanium x1n y1o z1composition (is specially TiC 0.3o 0.7), i.e. x1=0.3, y1=0, z1=0.7, z1/ (x1+y1+z1)=0.7; Transition layer C1 is sheet (or granular) nanocrystalline structure, and the thickness of transition layer C1 is 0.3 μm, and the grain fineness number of transition layer C1 is less than 200nm;
Transition layer C2 222 is primarily of the carbon nitrogen oxide TiC of titanium x2n y2o z2composition (is specially TiC 0.8n 0.15o 0.05), i.e. x2=0.8, y2=0.15, z2=0.05, and x2/ (x2+y2+z2)=0.8; Transition layer C2 is the nanometer equant grains structure of discrete distribution, and the thickness of transition layer C2 is 0.2 μm, and the grain fineness number of transition layer C2 is less than 200nm.
The cutting tool of above-mentioned the present embodiment prepares mainly through following methods:
(1) hard alloy substrate is prepared: first with ball mill, the WC powder of 6wt%Co, 3.5wt%Ti and Ta cubic carbonitride and surplus is passed through wet mixing 20h, compound is dry, be pressed into pressed compact, pressed compact is sintered into inserted tool matrix, wet abrasive blasting process is adopted to its surface and cutting edge; Then on described tool matrix, in same coating cycle, following coating is deposited respectively:
The operation of step (2) ~ (6) of the present embodiment is substantially the same manner as Example 1, is only that process parameter control in coating furnace is adjusted accordingly can (see table 1).
Analyze the surface microstructure of the outer D23 of the present embodiment surface oxides with SEM and EDS, result as shown in Figure 4; Calculate α-Al in the present embodiment mesectoderm D23 2o 3mean grain size S be 0.49 μm.
Embodiment 4:
The cutting tool improving coating structure of the present invention, its matrix is substantially the same manner as Example 3, and coating structure, moiety, microcosmic composition etc. are all identical with the cutting tool in embodiment 3, are only outer α-Al 2o 3with embodiment 3 slightly difference.In the present embodiment, the thickness d of outer D is 1.4 μm, and mean grain size S is 0.32 μm.Step (1) ~ (6) of the preparation method of the cutting tool of the present embodiment are substantially the same manner as Example 3, only need do accommodation on processing parameter; Finally recycle conventional CVD deposit again on outer D one deck above-mentioned containing Ti Compound Identification layer; Again after surface treatment, remove aforementioned label layer at the regional area of the cutting edge of described coated chip, rake face or rear knife face and outer B is exposed, complete making.
Select 4 kinds of contrast cutting tools else:
Cutting tool one (comparative example 1) matrix is identical with embodiment 1, and inner layer B coating process is identical with embodiment 1, lacks transition layer C, and in the present embodiment, the thickness d of outer D is 3.5 μm, and mean grain size S is 1.1 μm.
Cutting tool two (comparative example 2) matrix is identical with embodiment 1, and inner layer B coating process is identical with embodiment 1, and transition layer C only has C1 thickness to be 1 μm, and the thickness d of outer D is 4.2 μm, and mean grain size S is 1.3 μm.
Cutting tool three (comparative example 3) matrix is identical with embodiment 3, inner layer B coating process is identical with embodiment 3, the scheme preparation that outer D provides according to CN1091683A Chinese patent literature, the thickness d of outer D is 7 μm, and mean grain size S is 1.7 μm.
The main coating structure of each embodiment and comparative example sees table 2 above, and wherein, the surface microstructure of the outer D of comparative example 1 as shown in Figure 5; The outer D of comparative example 2 and the surface microstructure of transition layer C1 are as shown in Figure 6, Figure 7.
Table 2: the thickness contrast of the main coating structure of various cutting tool
The cutting tool of above-described embodiment 1, embodiment 2 and contrast cutting tool 1,2 are carried out respectively Cutting experiment as shown in Table 3 below and the milling test shown in following table 4.
Table 3: Cutting experiment pattern
Table 4: milling test pattern
The result of above-mentioned Cutting experiment and milling test is as shown in table 5 below.
Table 5: comparison of test results
As can be seen from Table 5: the cutting tool surface of comparative example has occurred for α and κ mixed crystal aluminum oxide in various degree, and coarse grains or thickness uneven etc., and the cutting tool surface uniform of the embodiment of the present invention; The grain fineness number of outer D under the condition that coat-thickness is suitable, the obvious refinement of oxide coating prepared by the grain fineness number hinge structure of outer D of the present invention; Visible, adopt technology of the present invention can prepare the tiny oxide coating with the α-Al2O3 structure of single-phase of crystal grain.
The cutting tool surface microstructure of comparative example is extremely thick and have the thick phenomenon of folder, and cutter life fluctuation is larger; And the cutting tool surface microstructure of the embodiment of the present invention is tiny, evenly, in scratch test, show good bonding strength, in cutting experiment, show longer work-ing life and stability.

Claims (10)

1. improve a cutting tool for coating structure, the coating comprising matrix A and cover at least partly on matrix A, described coating includes inner layer B, transition layer C and outer D from inside to outside;
The compound-material that described inner layer B forms primarily of the transition element in the periodic table of elements and non-metallic element is formed, described transition element is selected from least one in IVB race in the periodic table of elements, VB race, group vib, and described non-metallic element is selected from least one in carbon, nitrogen, oxygen, boron;
It is characterized in that, described transition layer C includes transition layer C1 and/or transition layer C2 from outside to inside;
Described transition layer C1 is primarily of the carbon nitrogen oxide TiC of titanium x1n y1o z1composition, described x1, y1, z1 represent TiC respectively x1n y1o z1the atomic percent of middle C, N, O, and meet 0.5≤z1/ (x1+y1+z1)≤1, y1≤x1≤z1;
Described transition layer C2 is primarily of the carbon nitrogen oxide TiC of titanium x2n y2o z2composition, described x2, y2, z2 represent TiC respectively x2n y2o z2the atomic percent of middle C, N, O, and meet 0.5≤x2/ (x2+y2+z2)≤1,
Described outer D has the α-Al of single-phase 2o 3structure, the thickness of outer D is d=0.5 μm ~ 4 μm, and its mean grain size S is 0.2 μm≤S≤0.5 μm.
2. the cutting tool improving coating structure according to claim 1, is characterized in that: in described transition layer C1, and described x1, y1, z1 meet 0.5≤z1/ (x1+y1+z1)≤0.8; Described transition layer C1 is sheet or granular nanocrystalline structure, and the grain fineness number of described transition layer C1 is less than 200nm, and the thickness of described transition layer C1 is less than 0.5 μm.
3. the cutting tool improving coating structure according to claim 1, is characterized in that: in described transition layer C2, and described x2, y2, z2 meet 0.8≤x2/ (x2+y2+z2)≤1; Described transition layer C2 is the nanometer equant grains structure of discrete distribution, and the grain fineness number of described transition layer C2 is less than 200nm, and the thickness of described transition layer C2 is less than 0.5 μm.
4. the cutting tool improving coating structure according to claim 3, it is characterized in that: described x2=1, y2=0, z2=0, described transition layer C2 is TiC coating, the thickness of described transition layer C2 is less than 0.3 μm.
5. the cutting tool of the improvement coating structure according to any one of Claims 1 to 4, it is characterized in that: the compound-material of described inner layer B be selected from carbide, nitride, boride, oxide compound, carbonitride, boron nitride, boron carbonitride one or more, have at least one to have column crystal or fibrous crystal structure in described compound-material.
6. the cutting tool improving coating structure according to claim 5, it is characterized in that: described inner layer B comprises one deck MT-TiCN, its thickness is greater than 3 μm.
7. the cutting tool of the improvement coating structure according to any one of Claims 1 to 4, is characterized in that: the total thickness of described transition layer C is 0.1 μm ~ 0.8 μm.
8. the cutting tool of the improvement coating structure according to any one of Claims 1 to 4, is characterized in that: be also coated with one deck in the outside of described outer D containing Ti Compound Identification layer E, and the described thickness containing Ti Compound Identification layer is 0.1 μm ~ 1 μm.
9. the preparation method of the cutting tool of the improvement coating structure according to any one of claim 1 ~ 8, comprise the following steps: the tool matrix first preparing Wimet, sintering metal, nonmetallic ceramics, PCD or CBN material, then deposits following coating on described tool matrix in same coating cycle:
(1) inner layer B of conventional CVD deposit those on described tool matrix A is utilized;
(2) the transition layer C2 of conventional HT-CVD technique deposit those in described inner layer B is utilized;
(3) the transition layer C1 of conventional HT-CVD method deposit those on described transition layer C2 is utilized;
(4) the outer D of conventional HT-CVD method deposit those on described transition layer C1 is utilized;
(5) sandblasting or siliceous nylon brush polishing is adopted to carry out surface treatment to above-mentioned obtained hard alloy coated blade;
(6) utilize conventional CVD deposit again on outer D one deck above-mentioned containing Ti Compound Identification layer; Again after surface treatment, remove aforementioned label layer at the regional area of the cutting edge of described coated chip, rake face or rear knife face and outer B is exposed, complete making.
10. preparation method according to claim 9, is characterized in that: the deposition of described outer D refers to and utilize CO, CO on this transition layer C1 2and H 2the mixed gas of S is optimized forming core to transition layer C1, then after the aluminum oxide forming core effect of outer D, utilizes H 2s or SF 6the growth of aluminum oxide coating layer is optimized, obtains α-Al described in compact grained 2o 3structure; The deposition process of described outer D controls 900 DEG C ~ 1020 DEG C temperature ranges.
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