CN103157815B - The surface-coated cutting tool of the wearability of excellence is played in high speed heavy cut - Google Patents
The surface-coated cutting tool of the wearability of excellence is played in high speed heavy cut Download PDFInfo
- Publication number
- CN103157815B CN103157815B CN201210528346.XA CN201210528346A CN103157815B CN 103157815 B CN103157815 B CN 103157815B CN 201210528346 A CN201210528346 A CN 201210528346A CN 103157815 B CN103157815 B CN 103157815B
- Authority
- CN
- China
- Prior art keywords
- layer
- mentioned
- alumina
- coated cutting
- cutting tool
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Landscapes
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
The present invention provides a kind of surface coating layer cutting element, and its hard coating layer, in the high speed heavy cut of cast iron, carbon steel etc. is processed, plays the lubricity of excellence, wearability.The surface-coated cutting tool of the present invention, at least most surface in tool base possesses and has the average thickness of 0.2～5 μm and the higher alumina layer of flatness, this alumina layer is made up of substrate and the spheroidal structure that is dispersed in substrate, above-mentioned substrate is made up of alumina crystalline phase and amorphous phase, and, above-mentioned spheroidal structure is made up of the aggregation of one or both in needle-like crystalline phase and tabular crystalline phase and amorphous phase, area ratio shared by the spheroidal structure of the longitudinal section being contained in alumina layer is 20～60 area %, and the radius of approximate circle is 0.02～0.5 μm.
Description
Technical field
The present invention relates to a kind of surface-coated cutting tool, its hard coating layer possesses the surface smoothness of excellence, lubrication
Property, chip discharge, deposit resistance property, even if thus add man-hour at the high speed heavy cut for cast iron, carbon steel etc., warp
Long-time use also plays the wearability of excellence.
Background technology
It is known that all the time by being formed by 4a, 5a, the 6a in periodic chart at tool base Surface coating
The hard film that the carbide of element more than at least one of race, nitride, carbonitride are constituted, it is achieved cutting
The raising of the wearability of instrument.
Further, in hard film, the especially Heat stability is good of alpha-type aluminum oxide layer, reactivity is low and hardness is high, because of
This as by 4a, 5a, 6a race in above-mentioned periodic chart at least one more than the carbide of element, nitride,
The top layer of the hard film that carbonitride is constituted, generally cladding form alpha-type aluminum oxide layer.
The method forming alumina layer as cladding, generally uses chemical vapor deposition (CVD) method, moreover, it is well known that
Alumina layer is formed also by physical vapor deposition (PVD) method, sol-gel process.
Such as, as Patent Document 1, in order to avoid tool base, the deterioration in characteristics/deformation of hard film, as
The method that (less than 1000 DEG C) form alpha-type aluminum oxide layer under cryogenic, proposes there is following content, i.e. passes through thing
Reason vapour deposition method (PVD) is formed on tool base surface by by A1 with in 4a race, 5a race, 6a race and Si
At least one element form as necessity nitride, carbide, carbonitride, boride, nitrogen oxides, carbon
After the hard film that nitrogen oxides is constituted, form oxycompound layer by aoxidizing this hard film, and at this containing oxidation
It is deposited with the α type crystalline substance forming the wearability as top layer and excellent heat resistance by physical vapor deposition (PVD) in nitride layer
Body structure is as the alumina layer of main body.
Further, as shown in patent documentation 2, proposition has by physical vapor deposition (PVD) method evaporation formation hard cladding
In the surface-coated cutting tool of layer, constitute the 1st layer with (Ti, Al) N shell, and with alumina layer (preferably
γ type alumina layer) constitute the 2nd layer.
It addition, as shown in patent documentation 3, as the system of the alumina-coated structure with mechanical property, durability
Making method, proposing crystal structure to have by sol-gel process is non crystalline structure or γ type aluminium oxide or their mixing
After the 1st alumina layer that thing is constituted is coated on mother metal, form the 2nd oxygen based on γ type by sputtering cladding
The method changing aluminium lamination.
Patent documentation 1: Japanese Unexamined Patent Publication 2004-124246 publication
Patent documentation 2: Japanese Unexamined Patent Publication 2007-75990 publication
Patent documentation 3: Japanese Unexamined Patent Publication 2006-205558 publication
Form alumina layer as the surface-coated cutting tool of hard coating layer by CVD cladding, to cast iron,
When steel etc. carry out machining, the raising of the wearability of available coating tool rake face, this is especially because α type oxygen
Change the heat stability of aluminum, non-reacted higher and obtain.
In above-mentioned patent documentation 1, propose have by physical vapor deposition (PVD) method formed under cryogenic α type aoxidize
Aluminium lamination, but when evaporation forms alumina layer, it is necessary first to oxidation hard film forms oxycompound layer on its surface,
But owing to oxycompound layer is insufficient with the adhesiveness of alumina layer, and do not only exist alpha-type aluminum oxide also as aluminium oxide
There is γ type aluminium oxide, it is impossible to obtain sufficient thermostability, the existence of its result cannot play satisfactory by long-term use
The problem of cutting ability.
Further, in above-mentioned patent documentation 2,3, the aluminium oxide formed is γ type aluminium oxide, therefore lacks under high temperature
Stability, and in high-speed cutting is processed, there is the problem that cannot play gratifying cutting ability.
Summary of the invention
Therefore, the present inventor etc. in order to form the aluminium oxide of excellent in abrasion resistance by sol-gel process on tool base surface
Layer and conduct in-depth research, find: by constitute with sol-gel process formed substrate aluminium oxide in, dispersion
The excellent in abrasion resistance that distribution is made up of the aggregation of one or both in needle-like crystalline phase and tabular crystalline phase and amorphous phase
Spheroidal structure, is being used for producing high heat, and when high capacity acts in the high speed heavy cut processing of cutting edge, also can
Access the surface-coated cutting tool of excellent in abrasion resistance.
That is, it is found to have following content: when preparing alumina sol, processes as ripening at low temperature and carry out than generally more low temperature
Under stirring and keep for a long time, thus suppression hydrolysis and the response speed of polycondensation, and densely formed by Al-O key
During the alumina precursor constituted, it is possible to form more octahedra AlO being similar to corundum type structure6If, therefore by this oxygen
Change Alumina gel to be coated as the surface layer of tool base and be dried and burn till, then can be formed as follows by alumina layer structure
The surface layer of hard film become, above-mentioned alumina layer is higher in flatness and lubricity, resistance to deposition to chip
Property excellent aluminium oxide substrate in dispersed and distributed have by one or both in needle-like crystalline phase and tabular crystalline phase and amorphous
The alumina layer of the spheroidal structure of the excellent in abrasion resistance that the aggregation of phase is constituted.
It addition, the hard film adjacent with the alumina layer of surface layer to be formed as Al metal group in this hard film
During shared in the one-tenth nitride epithelium that content ratio is 40 more than atom %, viscous due to the alumina layer of surface layer
Attached intensity uprises, and sees from the generation of the stripping of alumina layer suppressed because impact during machining etc. causes, defect etc.
From the point of view of more satisfactory.
That is, finding following content: in the surface-coated cutting tool of the present invention, the surface layer of hard coating layer is by aoxidizing
Aluminium lamination is constituted, and this alumina layer is by flatness, lubricity, alumina host and the dispersion point of deposit resistance property excellence
The spheroidal structure of the excellent in abrasion resistance being distributed in this substrate is constituted, and the Surface coating therefore possessing this hard coating layer is cut
Instrument of cutting adds man-hour at the high speed heavy cut for cast iron, carbon steel etc., also plays the wearability of excellence through long-time use.
The present invention is to complete based on above-mentioned opinion, it is characterised in that
(1) a kind of surface-coated cutting tool, it is by tungsten carbide base carbide alloy, base titanium carbonitride structure
The Surface coating of the tool base become forms hard coating layer and forms, it is characterised in that
A () possesses the alumina layer surface layer as above-mentioned hard coating layer of the average thickness with 0.2～5 μm,
B () above-mentioned alumina layer is made up of substrate and the spheroidal structure that is dispersed in substrate,
C () above-mentioned substrate is made up of alumina crystalline phase and amorphous phase, and above-mentioned spheroidal structure is by needle-like crystalline phase and tabular
The aggregation of one or both and amorphous phase in crystalline phase is constituted.
(2) surface-coated cutting tool as described in described (1), it is characterised in that spheroidal structure is in above-mentioned oxidation
Area ratio shared in aluminium lamination is 20～60 area %.
(3) surface-coated cutting tool as described in described (2), it is characterised in that the approximation of above-mentioned spheroidal structure
The radius of circle is 0.02～0.5 μm.
(4) surface-coated cutting tool as described in any one in described (1) ~ (3), it is by tungsten carbide-base
The Surface coating of the tool base that hard alloy is constituted forms hard coating layer and forms, it is characterised in that
Define the matrix table of the average thickness with 0.5 ~ 3.0 μm towards depth direction from the surface of above-mentioned tool base
Face hardened layer, the average content as the Co of the combination phase metal being contained in this matrix surface hardened layer is less than 2.0 mass
%。
(5) surface-coated cutting tool as described in any one in claim (1) ~ (3), it is by carbon nitrogen
The Surface coating formation hard coating layer changing the tool base that titanium-based metal pottery is constituted forms, it is characterised in that
Define the matrix table of the average thickness with 0.5 ~ 3.0 μm towards depth direction from the surface of above-mentioned tool base
Face hardened layer, the grand mean content as Co and Ni of the combination phase metal being contained in this matrix surface hardened layer is less than
2.0 mass %.
The present invention is described in detail below.
The surface-coated cutting tool of the present invention passes through colloidal sol as what the surface layer of hard coating layer possessed 0.2～5.0 μm
The alumina layer of-gel method film forming, but if the thickness of alumina layer is less than 0.2 μm, the life of spheroidal structure the most described later
Become negligible amounts, so sufficient wearability cannot be played, on the other hand, if thickness is more than 5.0 μm, the most easily send out
The stripping of generating layer, so being set to 0.2～5.0 μm by the thickness of alumina layer.
Further, above-mentioned alumina layer can play its performance by direct formation of film at surface in tool base, but will contain
When the tungsten carbide base carbide alloy of titanium carbonitride is as matrix, make by carrying out burning till in blanket of nitrogen Ti, Ta, Nb,
The carbonitride that at least one wearability in Zr is high more contains at tool base near surface, is consequently formed matrix
Cementation zone, it is possible to increase alumina layer and the adhesion strength of tool base, extends life tools.It addition, formed
The hardness of the hard alloy substrate after this matrix surface hardened layer in terms of Vickers hardness (Hv) be preferably more than 2200 and
Less than 2800.Now, by more containing carbonitride, the Co near matrix surface can be made relatively to reduce, example
As utilized scanning electron microscope (SEM) to observe towards the cross section of depth direction 0.5 ~ 3.0 μm from surface,
And carry out quantitative analysis based on Wavelength dispersion type x ray spectrographic method in analyzing field of view 1 × 1 μ m, thus
When detecting the content as the Co combining phase metal, if the content of Co is less than 2.0 mass %, then it is sufficiently formed into
For the carbonitride of the main cause of matrix surface hardening, improve wearability further.
If the average thickness of matrix surface hardened layer is below 0.5 μm, then when giving full play to wearability
Wear and tear earlier, if more than 3.0 μm, the most easily collapse cutter.
It addition, when using base titanium carbonitride as matrix, by when sintering circuit heats up and be maintained at the highest
Atmosphere during temperature be set to regulation blanket of nitrogen, and keep midway in or cooling time reduce pressure, thus with by whole
The situation that individual sintering circuit is implemented in the blanket of nitrogen of certain pressure is compared, and can make Surface hardened layer.If this is because by one
When determining to implement under nitrogen pressure the operation till keeping with maximum temperature, disperse formation hardness high at collective's inner homogeneous
Carbonitride, if but will heat up or process under higher nitrogen pressure till the midway that keeps, and in the midway kept
Or when starting the blanket of nitrogen with further decompression processes when cooling, due to only in the most surface denitrogenation of matrix,
Therefore Ti and Nb etc. to the melting of Ni and Co metal bound phase and come to life to the diffusion of matrix surface from internal,
Promote the formation of the carbonitride of Ti and Nb etc. on surface, thus form matrix surface hardened layer.It addition, formed
The hardness of the metal-ceramic matrix after this matrix surface hardened layer in terms of Vickers hardness (Hv) be preferably more than 2000 and
Less than 2600.Further, now in the same manner as above-mentioned tool base, Ni with Co near matrix surface is relative to be reduced,
If the content as Ni and Co combining phase metal is less than 2.0 mass %, then it is sufficiently formed and becomes matrix surface hardening
The carbonitride of main cause, improve wearability further.
If the average thickness of matrix surface hardened layer is for being below 0.5 μm in the same manner as above-mentioned hard alloy substrate, then exist
Wear and tear earlier under the state that cannot give full play to wearability, if more than 3.0 μm, the most easily collapse cutter.
It addition, in the surface-coated cutting tool of the present invention, can not directly form above-mentioned oxygen on the surface of tool base
Change aluminum, but form this by physical vapor deposition (PVD) method, chemical vapor deposition (CVD) method or sol-gel process
Hard film known to the skilled person, i.e. by containing in 4a, 5a, 6a race in periodic chart and Si extremely
After lacking the hard film of the nitride of a kind of element or more than 1 layer of oxide composition, at the table of this hard film
Surface layer cladding forms above-mentioned alumina layer.
During it addition, form hard film by above-mentioned physical vapor deposition (PVD) method, for adjacent with alumina layer hard
For matter epithelium, from the viewpoint of improving adhesiveness, it is preferably formed in this hard film containing Al, and Al exists
Nitride epithelium (the such as TiAlN that content ratio is 40 more than atom % shared in the metal composition of this hard film
Film, CrAlN film etc.).
This is because, if in the metal composition that Al is in hard film shared content ratio be 40 atom % with
On nitride epithelium, then on the interface of nitride epithelium and aluminium oxide epithelium, form the oxide that aluminum concentration is higher,
This oxide becomes to have bonding nitride epithelium and the effect of aluminium oxide epithelium securely.
The alumina layer of the surface layer constituting the surface-coated cutting tool of the present invention is become by sol-gel process described later
Film, thus its substrate is made up of alumina crystalline phase and amorphous phase, and is formed by needle-like crystalline phase and plate in this substrate
The spheroidal structure that the aggregation of one or both and amorphous phase in shape crystalline phase is constituted.
About above-mentioned spheroidal structure, when observing alumina layer by scanning electron microscope (SEM), as shown in Figure 1, Figure 2
Shown in, it was observed that radius is the conglobulation soma of 0.02～0.5 μm, and if with transmission electron microscope (TEM)
Further this spheroidal structure is observed, it is known that be formed as amorphous phase and needle-like crystalline phase, the aggregation group of tabular crystalline phase
Knit.
Further, such as in the range of field of view 5 × 7 μm, this spheroidal structure is obtained by observing longitudinal section SEM
Area ratio shared in aluminium oxide, it is known that be 20～60 area %.
It addition, can be observed on the interface of the aluminium oxide in spheroidal structure with substrate according to Fig. 2 to surround spheroidal structure
Mode be formed with recess (in Fig. 2, black annulus).
Its shape of spheroidal structure is exactly that each phase is arranged in complex tissue in various directions originally, and therefore isotropism is relatively
By force, by its stress dispersion effect, even if also contributing to the wearability played stably in the heavy cut applying high capacity.
If the area ratio that above-mentioned spheroidal structure is shared by aluminium oxide is more than 60 area %, then fix the substrate of spheroidal structure
Diminishing than regular meeting, so embrittlement tendency occurring at alumina layer, and surrounding the recess (with reference to Fig. 2) of spheroidal structure
Ratio become big, load uneven when carrying out machining acts on layer, destroys it is therefore possible to produce.The opposing party
Face, when area ratio is less than 20 area %, tails off owing to being favorably improved the spheroidal structure of wearability, so aluminium oxide
The wearability of layer declines.
Therefore, in the present invention, the area ratio that spheroidal structure is shared in alumina layer is set to 20～60 area %.
When the radius of the circle of the area as the area equation having with this spheroidal structure obtains the radius of above-mentioned spheroidal structure
Time, if radius is less than 0.02 μm, then the effect of the raising wearability in alumina layer diminishes, on the other hand, if radius
More than 0.5 μm, then become thick tissue, easily become the former of be full of cracks and thus result in the resistance to reduction collapsing cutter.
Therefore, above-mentioned spheroidal structure is dimensioned to radius 0.02～0.5 μm.
Constitute the surface-coated cutting tool of the present invention surface layer alumina layer can by colloidal sol shown below-
Gel method is formed.
The preparation of alumina sol:
First, the alkoxide (such as aluminium secondary butylate, Aluminum tripropoxide) of aluminum adds alcohol (such as ethanol, n-butyl alcohol), enters
One step interpolation (can also simultaneously add the alpha alumina particles that mean diameter is 10～300nm) acid (such as hydrochloric acid,
Nitric acid) after, stir within the scope of the temperature below 15～30 DEG C, and, by carrying out such as more than 12 hours
Maturation process form alumina sol.
It addition, when adding alcohol, promoting during in order to form alumina layer generates the film formation at low temp of nucleus and crystalline
Improve, preferably add from the viewpoint of making uniform colloidal sol in advance containing the α oxygen that mean diameter is 10～300nm
Change the alcohol of alumina particles.Further, this is because, when coating, alpha alumina particles becomes and becomes the starting point of crystal growth
Core, has as center effect of the conglobulation tissue of favorable dispersibility landform uniformly diameter in alumina layer,
But when adding the alcohol containing alpha alumina particles, if the mean diameter of alpha alumina particles is less than 10nm, then do not reach
The critical nucleus size of the starting point of crystal growth can be become, so the alumina sol around alpha alumina particles is not sent out
Raw crystal growth, and isolating from substrate, easily becomes the position that the adhesion of crystal grain with surrounding is more weak after burning till.Separately
On the one hand, if mean diameter is more than 300nm, then can grow into excessive using alpha alumina particles as the nucleus of starting point
Big particle, defect in the induction reduction of film hardness and film, the mean radius of alpha alumina particles therefore will added
It is set to 10～300nm.
If it addition, the content that alpha alumina particles is in alcohol is less than 0.5 mass % relative to the alkoxide of aluminum, then cannot expire
Foot is evenly distributed the karyogenesis quantity needed for the nucleus of more than certain density in film, and the crystallinity in film is according to position
Different and uneven, therefore easily induce inordinate wear during cutting.If relative to the alkoxide of aluminum more than 5 mass %, then
Being easily generated the cohesion of alpha alumina particles in alumina sol, when forming alumina layer, this cohesion portion is formed as in film
Big particle, defect in induction film, therefore preferably the addition of alpha alumina particles is set to relatively from this reason
Alkoxide in aluminum is the scope of 0.5～5 mass %.
Further, preferably added acid concentration be 0.01～4.0N, and preferred acid relative to the addition of alcohol be 0.5～
5 times (capacity).
In the preparation of the alumina sol generally carried out, carry out the stirring at 40～80 DEG C and the number under this whipping temp
The maturation process of about individual hour, but in the present invention, such as, spend more than 12 hours carry out for a long time
The ripening at low temperature of the stirring in the low temperature range of 15～30 DEG C processes.
Wherein, if temperature when stirring and holding is more than 30 DEG C, then hydrolysis and polycondensation reaction can quickly be carried out, before institute
Body cannot densely be formed, and is formed without alpha-aluminium oxide in as follow-up operation firing process, so will stirring and guarantor
30 DEG C it are defined to, on the other hand, if temperature when stirring and holding is less than 15 DEG C, then in oxidation in temperature when holding
Alumina gel is formed uniformly multiple dense Al-O joint portion constructed, but is intended to be formed the ball of the size with the present invention
Shape tissue, then be formed locally the joint portion of a small amount of Al-O closely preferably in alumina sol, thus will stirring and
Temperature during holding is set to the cryogenic temperature scope of 15～30 DEG C that hydrolysis, polycondensation reaction are carried out the most partly.
It addition, to be set to more than 12 hours long-time the curing time, it is because the most gradually promoting hydrolysis, makes
Alumina precursor densely generates.
Be dried/burn till:
Alumina sol in above-mentioned middle preparation is coated directly onto the surface of tool base or is applied to pass through physical vapor deposition
(PVD) method is formed at the most surface of hard film on tool base surface, then, be repeated more than 1 time 100～
400 DEG C, the more preferably dried at 250～350 DEG C, then burn within the temperature range of 750～1000 DEG C
One-tenth processes and is coated with formation alumina layer.
Formed the dry colloidal sol of aluminium oxide by above-mentioned dried, burn till process by then carry out, at hard skin
Film surface forms with alumina crystalline phase and amorphous phase the alumina layer as substrate, meanwhile, in substrate, by needle-like
The spheroidal structure dispersed and distributed that the aggregation of one or both and amorphous phase in crystalline phase and tabular crystalline phase is constituted is in substrate
In and formed.
The thickness of above-mentioned alumina layer depends on coating thickness and the application frequency of alumina sol, if cladding formation is upper
The thickness stating oxide layer is less than 0.2 μm, then cannot play excellence as surface-coated cutting tool by long-term use
Wearability, on the other hand, if thickness is more than 5.0 μm, then alumina layer is easily peeling, so by above-mentioned oxidation
The thickness of aluminium lamination is set to 0.2～5.0 μm.
Further, the temperature range of dried is set to 100～400 DEG C, more preferably 250～350 DEG C, and place will be burnt till
The temperature range of reason is set to the reason of 750～1000 DEG C and is, for baking temperature, if less than 100 DEG C, and cannot be abundant
Being dried, if more than 400 DEG C, sol volume is shunk and is drastically carried out, and produces be full of cracks etc., is easily generated the stripping etc. of film,
For firing temperature, if less than 750 DEG C, then cannot being formed and there is the crystalline alumina layer fully meeting heavy cut,
Therefore wearability is insufficient, on the other hand, if burning till with the temperature more than 1000 DEG C, can be formed because of alumina layer and base
The be full of cracks that the coefficient of expansion difference at the end causes, and produce the oxidation of hard alloy or metal-ceramic matrix etc., can not show
The advantage of film formation at low temp.
According to the surface-coated cutting tool of the present invention, the most surface in tool base is coated with formation and passes through sol-gel process
The aluminium oxide of film forming, but the above-mentioned alumina layer formed possesses the surface smoothness of excellence, lubricity, wearability,
Therefore it it is used for producing high heat, and high capacity acts on the high speed heavy cut processing of the cast iron of cutting edge, carbon steel etc.
Time, the most do not collapse the abnormal damage such as cutter, stripping, play excellent wearability through long-time use.
Accompanying drawing explanation
Fig. 1 represents the macrograph of the longitudinal section observing its alumina layer for inventive article 1 SEM.
Fig. 2 represents that the surface SEM of dispersed and distributed spheroidal structure in its alumina layer in inventive article 1 shines
Sheet.
Detailed description of the invention
Then according to embodiment, the present invention is carried out more specific description.
[embodiment 1]
As material powder, prepare in the microgranule WC powder of mean diameter 0.8 μm, mean diameter 2 ~ 3 μm
Grain WC powder and be respectively provided with the TiCN powder of mean diameter of 1～3 μm, ZrC powder, TaC powder, NbC
Powder, Cr3C2Powder and Co powder, coordinate these material powders with the predetermined cooperation composition shown in table 1, enter
One step adds paraffin and mixes 24 hours, with the pressure punching press of 98MPa after drying under reduced pressure with ball mill in acetone
It is molded into the pressed compact of reservation shape, in the vacuum of 5Pa, in the condition keeping 1 hour with the temperature of 1400 DEG C
Lower this pressed compact of vacuum-sintering, after sintering, processes by cutting edge portion is implemented the cutting edge reconditioning of R:0.05mm,
Manufacture the blade shapes in ISO CNMG120408 with regulation WC base cemented carbide tool base A,
B, a, b, C1, C2, C3, C4 and C5(be referred to as tool base A, B, a, b, C1, C2, C3,
C4 and C5).
But, about 1400 DEG C of processes keeping being cooled to 1320 DEG C after 1 hour, for tool base C2
It is to carry out in the blanket of nitrogen of 3.3kPa 40 minutes, is to carry out in the blanket of nitrogen of 1kPa for tool base C3
40 minutes, be to carry out in the blanket of nitrogen of 2kPa 10 minutes, for tool base C5 for tool base C4
It is to carry out 120 minutes cooling down in the blanket of nitrogen of 3.3kPa, thus matrix surface has been carried out at hardening
Reason.
Then, lower floor is defined for above-mentioned tool base A ~ C5.
Further, when forming lower floor, above-mentioned tool base a and b are loaded in chemical evaporation plating device, with table 2
Shown membrance casting condition, by by having the TiN layer of granular crystal tissue, TiCN layer, TiCO layer, TiCNO
The Ti compound layer that layer, the TiCN layer (following, be expressed as 1-TiCN) of longitudinal growth crystalline structure are constituted with
Epithelium composition shown in table 4 has been pre-formed basal layer.On the other hand, for above-mentioned tool base A, load
Be in arc ion plating apparatus to one of physical vapor deposition device, be pre-formed the thickness shown in table 4 by
Ti0.5Al0.5The basal layer that N shell is constituted.
Further, by above-mentioned tool base B, load arc ion plating apparatus equally, be pre-formed shown in table 4
Thickness by Al0.7Cr0.3The basal layer that N shell is constituted.
On the other hand, basal layer is not especially formed for above-mentioned tool base C1, C2, C3, C4 and C5.
On the other hand, being carried out as follows and prepare alumina sol, this alumina sol is for by sol-gel process bag
Cover the alumina layer forming the surface layer as hard coating layer.
(a) first, with the solution composition of each composition in reaction raw materials with molar ratio computing for (aluminium secondary butylate):
(water): (ethanol): (hydrochloric acid)=1:(40～60): after the mode of 20:0.8 is added, shown in table 3
Under the conditions of be stirred in temperature chamber, keep, be thus prepared for alumina sol.
B () then, the underlying surfaces at above-mentioned tool base A ~ C5 is coated with above-mentioned alumina sol.
C alumina sol after above-mentioned dip coated then, is entered by () the most in an atmosphere
Row dried, and carry out in an atmosphere 800 DEG C, 1 hour burn till process, thus by the aluminium oxide of the present invention
Layer (that is, in the substrate having alumina crystalline phase and amorphous phase to constitute dispersed and distributed by needle-like crystalline phase and tabular crystalline phase
In the alumina layer of spheroidal structure that constitutes of the aggregation of one or both and amorphous phase) cladding is formed at table
Face, the coating tool 1 ~ 12(producing the present invention shown in table 4 is referred to as inventive article 1 ~ 12).
For the invention described above instrument 1～12, by scanning electron microscope (SEM) alumina layer indulged and cut
The result that face carries out observing confirms: its substrate is made up of alumina crystalline phase and amorphous phase, on the other hand, and dispersion point
The spheroidal structure being distributed in substrate is by one or both in needle-like crystalline phase and tabular crystalline phase and the gathering of amorphous phase
Body is constituted.Transmission electron microscope (TEM) is utilized to confirm alumina crystalline phase and amorphous phase, by constituency electricity
Sub-diffraction approach analyzes its substrate and spheroidal structure respectively, has all obtained clearly electron diffraction pattern and halation pattern.
In FIG, the longitudinal section SEM photograph of the alumina layer of inventive article 1 is shown as an example,
And in fig. 2, equally for inventive article 1, it is shown that in its alumina host spherical group of dispersed and distributed
The surface SEM photograph knitted.Can determine that spheroidal structure is by amorphous phase and acicular crystal, plate crystal according to Fig. 2
Aggregation is constituted.
For the invention described above instrument 1～12, about spheroidal structure in the area ratio shared by the longitudinal section of alumina layer
The mean radius of example and spheroidal structure by scanning electron microscope (Carl zeiss society system, ultra55) with 50,000
Visual field again is observed, for its result, it is assumed that measure the area ratio of spheroidal structure for plane, and
Measure 5 points using the area of this spheroidal structure as the area of a circle calculate time the radius of approximate circle, and will
Its meansigma methods is as average-size.
Further, utilize scanning electron microscope that the average thickness of alumina layer is carried out cross-section determination, result simultaneously
All demonstrate actually identical with target thickness meansigma methods (meansigma methodss at 5).
Measurement result is shown in table 4.
And then, about in the invention described above instrument 1 ~ 12 be not provided with basal layer and on hard substrate direct formation of film at surface oxygen
Changing the instrument of aluminium lamination, the Co content to tool base surface, by utilizing scanning electron microscope (SEM)
Wavelength dispersion type x ray spectrographic method, from substrate surface towards depth direction in the observation visual field, longitudinal section of tool base
In the range of 0.5 ~ 3.0 μm, 1 × 1 μm carries out surface analysis, 5 visual fields is carried out quantitative analysis, and uses its meansigma methods.
Table 4 shows the combination phase amount of metal in cementation zone thickness and cementation zone.
[comparative example 1]
In order to compare, manufacture surface-coated cutting tool by following manufacture method.
(a) similarly to Example 1, with the solution composition of each composition in reaction raw materials with molar ratio computing for (secondary
Aluminium butoxide): (water): (ethanol): (hydrochloric acid)=1:(40～60): the mode of 20:0.8 is added.
(b) then, with embodiment 1 differently, with shown in table 3 temperature chamber temperature keep state under, hold
Stirring in continuous 12 hours, and then ripening 24 hours, be prepared for alumina sol by such process.
C () then, will be formed through the Ti compound layer of above-mentioned chemical vapor deposition method formation with through physical vapor deposition respectively
Formed TiAlN layer, the above-mentioned tool base A ~ D of AlCrN layer and do not implement special surface process work
The surface of tool matrix C1 ~ C5 is coated with above-mentioned alumina sol.
D the above-mentioned alumina sol having been coated with then, is done under conditions of shown in table 3 by () in an atmosphere
Dry process, and then coating is repeated and is dried till reaching predetermined thickness, the most in an atmosphere with 800 DEG C
Carrying out 1 hour burning till process, the surface-coated cutting tool 1 ~ 9(thus producing the comparative example shown in table 4 claims
For comparative example instrument 1 ~ 9).
For above-mentioned comparative example 1～9, also utilize scanning electron microscope (SEM) and transmission electron microscope
(TEM) result observing alumina layer confirms: spheroidal structure is not dispersed in film.
Then, with following condition, to the invention described above instrument 1～12 and comparative example instrument 1～9 carried out spheroidal graphite
The high speed heavy cut processing experiment of cast iron.
To the high speed high cutting-in cutting test (common cutting speed and the cutting-in that carry out spheroidal graphite cast-iron under the conditions of following
Amount is respectively 200m/min, 1.0mm) after the state of wear of each instrument observe, and cutter after measuring
The wear extent in face.
Workpiece: the pole of JIS FCD600
Cutting speed: 380/min
Cutting-in amount: 2.0mm
The amount of feeding: 0.3mm/rev.
Cutting time: 5 minutes
These results are shown in Table 5.
Table 1
Table 2
Table 3
Table 4
Table 5
[embodiment 2]
A (), as material powder, prepares to be respectively provided with the TiCN of the mean diameter of 0.5～2 μm (by quality ratio
TiC/TiN=50/50) powder, Mo2C powder, NbC powder, TaC powder, WC powder, Co powder and
Ni powder, and these raw materials are fitted in the predetermined cooperation composition shown in table 6, little by ball mill wet mixed 24
Time and dried, become pressed compact with the pressure punch forming of 98MPa, by this pressed compact in 1.3KPa nitrogen atmosphere,
Under conditions of keeping 1 hour with the temperature of 1540 DEG C after sintering, by cutting edge part being implemented R:
0.07mm cutting edge reconditioning, thus manufactures the TiCN fund of the blade shapes with iso standard CNMG190612
Belong to ceramic tool base D, E, d, e, F1, F2, F3, F4 and F5(be referred to as tool base D, E, d,
E, F1, F2, F3, F4 and F5).But, for tool base F2 be in the blanket of nitrogen of 1.3kPa with
The programming rate of 0.2 DEG C/min, from room temperature to 1540 DEG C and after keeping 30 minutes, is set to the vacuum of 13Pa
And cooling makes its Surface hardened layer after keeping 30 minutes at 1540 DEG C further.It is always for tool base F3
Gentle holding 60 minutes, for tool base F4 at 1.3kPa is risen at 1540 DEG C in the vacuum of 13Pa
From room temperature to 1540 DEG C and after keeping 30 minutes in blanket of nitrogen, it is set to the vacuum of 13Pa and exists further
1540 DEG C keep 5 minutes, are from room temperature to 1540 in the blanket of nitrogen of 1.3kPa for tool base F5
DEG C and after keeping 30 minutes, cooling after being set to the vacuum of 13Pa and keeping 90 minutes at 1540 DEG C further and
Make its Surface hardened layer.
Table 6
B () then, defines lower floor for above-mentioned tool base D ~ F5.
Further, when forming lower floor, above-mentioned tool base d and e are loaded in chemical evaporation plating device, utilize
Membrance casting condition shown in table 2, the epithelium constituted with the Ti compound of table 8 is constituted has been pre-formed basal layer.Separately
On the one hand, for above-mentioned tool base D, being encased in one of physical vapor deposition device is in arc ion plating apparatus,
Be pre-formed the thickness shown in table 8 by Ti0.5Al0.5The basal layer that N shell is constituted.
Further, by above-mentioned tool base E, load arc ion plating apparatus equally, be pre-formed shown in table 8
Thickness by Al0.7Cr0.3The basal layer that N shell is constituted.
On the other hand, basal layer is not especially formed for above-mentioned tool base F1, F2, F3, F4 and F5.
Then, it is being formed with above-mentioned tool base D of basal layer, E, d, e and is being formed without the upper of basal layer
State tool base F1 ~ F5 the most similarly to Example 1 by the colloidal sol of the preparation condition of table 7 and drying condition-solidifying
Glue method makes it film forming alumina layer till thickness.
Then, carry out at 800 DEG C in an atmosphere 1 hour burn till process, manufactured the present invention's shown in table 8
Coating tool 13 ~ 24(is referred to as inventive article 13 ~ 24).
For the invention described above instrument 13 ~ 24, by scanning electron microscope (SEM) alumina layer indulged and cut
The result that face carries out observing confirms: its substrate is made up of alumina crystalline phase and amorphous phase, on the other hand, and dispersion point
The spheroidal structure being distributed in substrate is by one or both in needle-like crystalline phase and tabular crystalline phase and the gathering of amorphous phase
Body is constituted.
For the invention described above instrument 13 ~ 24, about spheroidal structure in the area ratio shared by the longitudinal section of alumina layer
The mean radius of example and spheroidal structure is observed with the visual field of 50,000 times by scanning electron microscope, for it
Result, it is assumed that measure the area ratio of spheroidal structure for plane, and measure 5 points by this spheroidal structure
The radius of area approximate circle when calculating as the area of a circle, and be averaged value as average-size.
Measurement result is shown in table 8.
[comparative example 2]
In order to compare, manufacture coating tool by following manufacture method.
Use above-mentioned tool base D, E, d, e, with the temperature chamber temperature shown in the table 7 different from embodiment 2
Under the state kept continuously stirred 12 hours, and then ripening 24 hours, use aluminium oxide by such process
Colloidal sol is to reach film forming alumina layer till the predeterminated target thickness shown in table 8, then, by an atmosphere with
800 DEG C of process of burning till carrying out 1 hour, thus the coating tool 10 ~ 18(having manufactured the comparative example shown in table 8 claims
For comparative example instrument 10 ~ 18).
For comparative example instrument 10 ~ 18, utilize scanning electron microscope (SEM) and transmission electron microscope (TEM)
The result observing alumina layer confirms: spheroidal structure is not dispersed in film.
Then, with following condition, to the invention described above instrument 13～24 and comparative example instrument 10 ~ 18 cast
The high speed heavy cut processing experiment of ferrum.
To carry out high speed high feeding machining test (the common cutting speed and entering of cast iron under the conditions of following
Be respectively 250m/min, 0.3mm/rev. to amount) after the state of wear of each instrument observe, and survey
The wear extent of knife face after fixed.
Workpiece: the pole of JIS FC350
Cutting speed: 400/min
Cutting-in amount: 1.5mm
The amount of feeding: 0.4mm/rev.
Cutting time: 20 minutes
These results are shown in Table 9.
Table 7
Table 8
Table 9
From the point of view of the result being shown in table 5,9, in the surface-coated cutting tool 1～24 of the present invention, by molten
Glue-gel method is coated with formation aluminium oxide in the most surface of tool base, and this alumina layer possesses the surface of excellence and smooths
Property, lubricity, chip discharge, deposit resistance property, so being used for the high speed heavy cut of cast iron, carbon steel etc. by this
Time in processing, also will not produce and collapse the abnormal damage such as cutter, stripping, play excellent wearability through long-time use.
On the other hand, it is clear that and on the alumina layer of most surface, does not contains spheroidal structure and only by matrix organization
In the surface-coated cutting tool 1～18 of the comparative example constituted, bear the high capacity of incessantly heavy cut, especially because of
Abnormal damage in rake face and produce crescent hollow abrasion the most drastically, therefore wear no resistance and at short notice
Arrive service life.
It addition, in described embodiment, although utilize the instrument of blade shapes that the performance of hard coating layer is carried out
Evaluate, it goes without saying that utilize drill bit, slotting cutter also to be able to obtain same result.
Industrial applicability
According to the surface-coated cutting tool of invention, form aluminium oxide by sol-gel process in most surface cladding,
This alumina layer possesses the surface smoothness of excellence, lubricity, chip discharge, deposit resistance property, even if so
The high speed heavy cut being used in cast iron, carbon steel etc. adds man-hour, also will not produce and collapse the abnormal damage such as cutter, stripping,
Excellent wearability is played, it is possible to the long lifetime in implementation tool life-span, practical function is bigger through long-time use.
Claims (5)
1. a surface-coated cutting tool, it is being made up of tungsten carbide base carbide alloy or base titanium carbonitride
Tool base Surface coating formed hard coating layer form, it is characterised in that
A () possesses the alumina layer surface layer as above-mentioned hard coating layer of the average thickness with 0.2～5 μm,
B () above-mentioned alumina layer is made up of substrate and the spheroidal structure that is dispersed in substrate,
C () above-mentioned substrate is made up of alumina crystalline phase and amorphous phase, and above-mentioned spheroidal structure is by needle-like crystalline phase and tabular
The aggregation of one or both and amorphous phase in crystalline phase is constituted.
2. surface-coated cutting tool as claimed in claim 1, it is characterised in that
Spheroidal structure is 20～60 area % at the area ratio shared by the longitudinal section of above-mentioned alumina layer.
3. surface-coated cutting tool as claimed in claim 2, it is characterised in that
The radius of the approximate circle of above-mentioned spheroidal structure is 0.02～0.5 μm.
4. the surface-coated cutting tool as described in any one in claims 1 to 3, it is being closed by tungsten carbide-base hard
The Surface coating of the tool base that gold is constituted forms hard coating layer and forms, it is characterised in that
Define the matrix table of the average thickness with 0.5～3.0 μm towards depth direction from the surface of above-mentioned tool base
Face hardened layer, the average content as the Co of the combination phase metal being contained in this matrix surface hardened layer is less than 2.0 mass
%.
5. the surface-coated cutting tool as described in any one in claims 1 to 3, it is by titanium carbide nitride based metal
The Surface coating of the tool base that pottery is constituted forms hard coating layer and forms, it is characterised in that
Define the matrix table of the average thickness with 0.5～3.0 μm towards depth direction from the surface of above-mentioned tool base
Face hardened layer, the grand mean content as Co and Ni of the combination phase metal being contained in this matrix surface hardened layer is less than
2.0 mass %.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2011-268562 | 2011-12-08 | ||
| JP2011268562 | 2011-12-08 | ||
| JP2012-264891 | 2012-12-04 | ||
| JP2012264891A JP2013139076A (en) | 2011-12-08 | 2012-12-04 | Surface coated cutting tool exhibiting superior wear resistance in high-speed heavy cutting |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103157815A CN103157815A (en) | 2013-06-19 |
| CN103157815B true CN103157815B (en) | 2016-10-19 |
Family
ID=48581637
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201210528346.XA Active CN103157815B (en) | 2011-12-08 | 2012-12-10 | The surface-coated cutting tool of the wearability of excellence is played in high speed heavy cut |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103157815B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2021020365A1 (en) * | 2019-07-29 | 2021-02-04 | 京セラ株式会社 | Coated tool, and cutting tool comprising same |
| US20220250161A1 (en) * | 2019-07-29 | 2022-08-11 | Kyocera Corporation | Coated tool and cutting tool including the same |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4643620A (en) * | 1983-05-27 | 1987-02-17 | Sumitomo Electric Industries, Ltd. | Coated hard metal tool |
| CN1104263A (en) * | 1992-11-21 | 1995-06-28 | 克鲁伯·韦狄亚有限公司 | Tool and method for forming coated layer of body of same |
| CN1203636A (en) * | 1995-11-30 | 1998-12-30 | 桑德维克公司 | Coated cutting insert and method of making it |
| CN1203638A (en) * | 1995-11-30 | 1998-12-30 | 桑德维克公司 | Coated milling insert and method of making it |
| CN1396029A (en) * | 2001-03-26 | 2003-02-12 | 三菱综合材料株式会社 | Cutting tool coated with hard alloy on surface for high-speed heavy cutting |
-
2012
- 2012-12-10 CN CN201210528346.XA patent/CN103157815B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4643620A (en) * | 1983-05-27 | 1987-02-17 | Sumitomo Electric Industries, Ltd. | Coated hard metal tool |
| CN1104263A (en) * | 1992-11-21 | 1995-06-28 | 克鲁伯·韦狄亚有限公司 | Tool and method for forming coated layer of body of same |
| CN1203636A (en) * | 1995-11-30 | 1998-12-30 | 桑德维克公司 | Coated cutting insert and method of making it |
| CN1203638A (en) * | 1995-11-30 | 1998-12-30 | 桑德维克公司 | Coated milling insert and method of making it |
| CN1396029A (en) * | 2001-03-26 | 2003-02-12 | 三菱综合材料株式会社 | Cutting tool coated with hard alloy on surface for high-speed heavy cutting |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103157815A (en) | 2013-06-19 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103764323B (en) | Surface-coated cutting tool | |
| JP5328653B2 (en) | Ti-based cermet, coated cermet and cutting tool | |
| CN103302326B (en) | Hard coating layer plays the excellent resistance to surface-coated cutting tool collapsing knife | |
| CN107073591A (en) | Surface coated cutting tool with excellent chip resistance | |
| CN102355968A (en) | Surface-coated cutting tool | |
| KR20120128595A (en) | Surface-coated cutting tool and manufacturing method thereof | |
| CN100448576C (en) | Coated cement cutting tool with a chipping resistant, hard coating layer | |
| JPWO2008078592A1 (en) | Surface coating tool and method for machining workpiece | |
| CN107405695A (en) | Hard coating layer plays the excellent resistance to surface-coated cutting tool for collapsing knife | |
| JP4330859B2 (en) | Coated cemented carbide and method for producing the same | |
| CN103962588A (en) | Surface coated cutting tool | |
| CN109641286A (en) | Hard coating layer plays the surface-coated cutting tool of excellent chipping resistance and peel resistance | |
| CN103157815B (en) | The surface-coated cutting tool of the wearability of excellence is played in high speed heavy cut | |
| CN103317157B (en) | Surface-coated cutting tool | |
| CN104884200B (en) | Surface is coated component and its manufacturing method | |
| CN102407352B (en) | Cutting tool having rigid surface covering layer having excellent toughness and cutter fracturing resisting capacity | |
| WO2018124108A1 (en) | Ceramic member and cutting tool | |
| US20180154463A1 (en) | Surface-coated cutting tool in which hard coating layer exhibits excellent chipping resistance | |
| JPH11197936A (en) | Milling tool excellent in wear resistance | |
| CN102380629B (en) | Hard coating layer plays resistance to the cutting property of excellence, the surface-coated cutting tool of wearability | |
| CN103537720A (en) | Surface-wrapped cutting tool | |
| CN103831466A (en) | Surface-wrapped cutting tool | |
| JP2009034766A (en) | Surface coated cutting tool with hard coat layer having improved chipping resistance and wear resistance | |
| CN103182536A (en) | Surface-coated cutting tool with excellent chipping resistance, peeling resistance, and wear resistance | |
| JP2006289546A (en) | Surface-coated cermet cutting tool having hard coating layer for exhibiting superior chipping resistance in high speed intermittent cutting work |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |