CN103157815A - Surface wrapping cutting tool having good abrasive resistance during high speed heavy cut - Google Patents
Surface wrapping cutting tool having good abrasive resistance during high speed heavy cut Download PDFInfo
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- CN103157815A CN103157815A CN201210528346XA CN201210528346A CN103157815A CN 103157815 A CN103157815 A CN 103157815A CN 201210528346X A CN201210528346X A CN 201210528346XA CN 201210528346 A CN201210528346 A CN 201210528346A CN 103157815 A CN103157815 A CN 103157815A
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Abstract
The invention provides a surface wrapping cutting tool having good abrasive resistance during high speed heavy cut. A hard wrapping layer has a good lubricating performance and a good abrasive resistance during the high speed heavy cut processing of the cast iron and carbon steel. The surface of the tool is wrapped by a cutting tool, and a base body of the tool is provided with an alumina layer having an average layer thickness in a range from 0.2 to 5(mu)m and good smoothness on the outermost surface. The alumina layer is constituted by matrix and ball-shaped units dispersed in the matrix. The matrix is constituted by an alumina crystalline phase and non-crystalline phase. The ball-shaped units are constituted by one or two of the acicular crystalline phase and non-crystalline phase aggregates, and the area occupied by the ball-shaped units in the vertical cross section of the alumina layer is in a range of 20 to 60%, and the radius of the approximate circle is in a range from 0.02 to 0.5(mu)m.
Description
Technical field
The present invention relates to a kind of surface-coated cutting tool, its hard coating layer possesses excellent surface smoothness, lubricity, chip discharge, deposit resistance property, even thereby add man-hour at the high speed heavy cut for cast iron, carbon steel etc., also bring into play excellent wearability through long-time use.
Background technology
As everyone knows, the hard film all the time formed by carbide, nitride, the carbonitride that coats the element more than at least one of the 4a, the 5a that form in being selected from periodic table, 6a family on tool base surface, realize the raising of the wearability of cutting element.
And, in hard film, especially the Heat stability is good of alpha-type aluminum oxide layer, reactivity is low and hardness is high, the top layer of the hard film therefore formed as carbide, nitride, the carbonitride of the element more than at least one of 4a, 5a in being selected from above-mentioned periodic table, 6a family, usually coat and form the alpha-type aluminum oxide layer.
As coating the method that forms alumina layer, usually adopt chemical vapor deposition (CVD) method, in addition, also by physical vapor deposition (PVD) method, sol-gel process, form alumina layer as everyone knows.
For example, as Patent Document 1, for fear of tool base, the deterioration in characteristics of hard film/distortion, method as (below 1000 ℃) formation alpha-type aluminum oxide layer under cryogenic conditions, proposition has following content, by physical vapor deposition (PVD), on tool base surface, form by by A1, with be selected from 4a family, 5a family, the nitride that at least one element in 6a family and Si forms as necessity, carbide, carbonitride, boride, nitrogen oxide, after the hard film that carbon nitrogen oxide forms, form the oxycompound layer by this hard film of oxidation, and by physical vapor deposition (PVD), come evaporation to form the alumina layer as main body as the alpha type crystal structure of the wearability on top layer and excellent heat resistance on this oxycompound layer.
And, as shown in patent documentation 2, proposition has in by physical vapor deposition (PVD) method evaporation, forming the surface-coated cutting tool of hard coating layer, forms the 1st layer with (Ti, Al) N layer, and forms the 2nd layer with alumina layer (being preferably γ type alumina layer).
In addition, as shown in patent documentation 3, manufacture method as the alumina-coated structure with mechanical property, durability, it is after the 1st alumina layer that non crystalline structure or γ type aluminium oxide or their mixture form is coated on mother metal by crystal structure that proposition has by sol-gel process, coats to form by sputter and take the method for the 2nd alumina layer that the γ type is main body.
Patent documentation 1: TOHKEMY 2004-124246 communique
Patent documentation 2: TOHKEMY 2007-75990 communique
Patent documentation 3: TOHKEMY 2006-205558 communique
Coat and form the surface-coated cutting tool of alumina layer as hard coating layer by the CVD method, when cast iron, steel etc. is carried out to machining, can obtain the raising of the wearability of coating tool rake face, this is especially because heat endurance, non-reacted higher the obtaining of alpha-type aluminum oxide.
In above-mentioned patent documentation 1, proposition has by physical vapor deposition (PVD) method form the alpha-type aluminum oxide layer under cryogenic conditions, but when evaporation forms alumina layer, at first need the oxidation hard film to come to form the oxycompound layer on its surface, but because the adhesiveness of oxycompound layer and alumina layer is insufficient, and not only exist alpha-type aluminum oxide also to have γ type aluminium oxide as aluminium oxide, can't obtain sufficient heat resistance, there is the problem that can't bring into play gratifying cutting ability through long-term use in its result.
And, in above-mentioned patent documentation 2,3, formed aluminium oxide is γ type aluminium oxide, therefore lack the stability under high temperature, and, in high-speed cutting processing, existence can't be brought into play the problem of gratifying cutting ability.
Summary of the invention
Therefore, the inventor etc. conduct in-depth research for the alumina layer that forms excellent in abrasion resistance on the tool base surface by sol-gel process, find: in the aluminium oxide forming the matrix formed with sol-gel process, the spheroidal structure of the excellent in abrasion resistance that the aggregation of one or both and the amorphous phase in needle-like crystalline phase and tabular crystalline phase of disperse distributing forms, hot for generation of height, 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.
; find that there is following content: while preparing alumina sol; process and carry out than the stirring under common more low temperature and keep for a long time as ripening at low temperature; suppress thus the reaction speed of hydrolysis and polycondensation; and dense while forming the alumina precursor formed by the Al-O key, can form the more how close octahedra AlO that is similar to corundum type structure
6if so the superficial layer using this alumina sol as tool base is coated with and drying is burnt till, can form the superficial layer of the hard film formed by alumina layer as follows, the alumina layer of the spheroidal structure of the excellent in abrasion resistance that above-mentioned alumina layer forms for the aggregation that is distributed with one or both and amorphous phase in needle-like crystalline phase and tabular crystalline phase in and lubricity higher in flatness, matrix to the aluminium oxide of the deposit resistance property excellence of smear metal.
In addition, it is shared containing proportional while being nitride epithelium more than 40 atom % in forming that hard film that will be adjacent with the alumina layer of superficial layer forms the metal of Al in this hard film, because the adhesion strength of the alumina layer with superficial layer uprises, the peeling off of the alumina layer that the impact when suppressing because of machining etc. causes, damaged etc. generation viewpoint are seen more satisfactory.
; find following content: in surface-coated cutting tool of the present invention; the superficial layer of hard coating layer consists of alumina layer; and this alumina layer consists of with the spheroidal structure that is distributed in the excellent in abrasion resistance in this matrix the alumina host of flatness, lubricity, deposit resistance property excellence; therefore the surface-coated cutting tool that possesses this hard coating layer adds man-hour at the high speed heavy cut for cast iron, carbon steel etc., through long-time use, also brings into play excellent wearability.
The present invention is what based on above-mentioned opinion, complete, it is characterized in that,
(1) a kind of surface-coated cutting tool, its coating of surface in the tool base consisted of tungsten carbide base carbide alloy, base titanium carbonitride forms hard coating layer and forms, it is characterized in that,
(a) possess the superficial layer of the alumina layer of the average bed thickness with 0.2～5 μ m as above-mentioned hard coating layer,
(b) above-mentioned alumina layer consists of matrix and the spheroidal structure that is dispersed in matrix,
(c) above-mentioned matrix consists of aluminium oxide crystalline phase and amorphous phase, and the aggregation of one or both and the amorphous phase of above-mentioned spheroidal structure in needle-like crystalline phase and tabular crystalline phase forms.
(2) as described in (1) described surface-coated cutting tool, it is characterized in that, spheroidal structure shared Area Ratio in above-mentioned alumina layer is 20～60 area %.
(3) as described in (2) described surface-coated cutting tool, it is characterized in that, the approximate radius of a circle of above-mentioned spheroidal structure is 0.02～0.5 μ m.
(4) as described in the described surface-coated cutting tool of any one in (1) ~ (3), its surface in the tool base consisted of tungsten carbide base carbide alloy coats and forms hard coating layer and form, it is characterized in that,
Surface from above-mentioned tool base has formed the matrix surface hardened layer of the average bed thickness with 0.5 ~ 3.0 μ m towards depth direction, as the average content that is contained in the Co in conjunction with the phase metal in this matrix surface hardened layer, be less than 2.0 quality %.
(5), as the described surface-coated cutting tool of any one in claim (1) ~ (3), its coating of surface in the tool base consisted of base titanium carbonitride forms hard coating layer and forms, it is characterized in that,
Surface from above-mentioned tool base has formed the matrix surface hardened layer of the average bed thickness with 0.5 ~ 3.0 μ m towards depth direction, as being contained in the Co in conjunction with the phase metal in this matrix surface hardened layer and the overall average content of Ni, be less than 2.0 quality %.
Below the present invention is described in detail.
Surface-coated cutting tool of the present invention possesses the alumina layer that passes through the sol-gel process film forming of 0.2～5.0 μ m as the superficial layer of hard coating layer, if but the bed thickness of alumina layer is less than 0.2 μ m, the generation negligible amounts of spheroidal structure described later, so can't bring into play sufficient wearability, on the other hand, if bed thickness surpasses 5.0 μ m, easy peeling off of genetic horizon, so be decided to be 0.2～5.0 μ m by the bed thickness of alumina layer.
And, above-mentioned alumina layer can be brought into play its performance by direct formation of film at surface on tool base, but at the tungsten carbide base carbide alloy that will contain titanium carbonitride during as matrix, by burnt till the high carbonitride of at least one wearability made in Ti, Ta, Nb, Zr in blanket of nitrogen, more contain at the tool base near surface, form thus the matrix surface hardened layer, can improve the adhesion strength of alumina layer and tool base, extend life tools.In addition, the hardness that forms the hard alloy substrate after this matrix surface hardened layer is preferably more than 2200 in Vickers hardness (Hv) and below 2800.Now, by more containing carbonitride, can make near the Co of matrix surface relatively reduce, for example utilize scanning electron microscope (SEM) to be observed towards the cross section of depth direction 0.5 ~ 3.0 μ m from surface, and carry out quantitative analysis based on the Wavelength dispersion type x ray spectroscopic methodology in analyzing field of view 1 * 1 μ m scope, thereby while detecting as the content in conjunction with the Co of phase metal, if the content of Co is less than 2.0 quality %, fully become the carbonitride of the main cause of matrix surface sclerosis, further improve wearability.
If the average bed thickness of matrix surface hardened layer is below 0.5 μ m, wearing and tearing earlier under the state that can't give full play to wearability, if more than 3.0 μ m, easily collapse cutter.
In addition, using base titanium carbonitride as matrix the time, atmosphere when heating up in sintering circuit and while remaining on maximum temperature is made as the blanket of nitrogen of regulation, and keep midway in or reduced pressure during cooling, thereby compare with the situation that whole sintering circuit is implemented in the blanket of nitrogen of certain pressure, can make the surface sclerosis.If this is because during by the operation till implementing under certain nitrogen pressure to keep with maximum temperature, disperse equably to form the carbonitride that hardness is high in collective inside, if but will heat up or keep midway till under higher nitrogen pressure, process, and keep midway in or while being processed in the blanket of nitrogen that starts further to reduce pressure while certainly lowering the temperature, due to only in the most surface denitrogenation of matrix, therefore the diffusion to matrix surface comes to life to the melting of Ni and Co metal bound phase with from inside for Ti and Nb etc., promote the formation of the carbonitride of Ti and Nb etc. on surface, thereby form the matrix surface hardened layer.In addition, the hardness of the cermet matrix after forming this matrix surface hardened layer is preferably more than 2000 in Vickers hardness (Hv) and below 2600.And, now with above-mentioned tool base similarly, near reduce relative with Co of Ni matrix surface, if be less than 2.0 quality % as the content of the Ni in conjunction with the phase metal and Co, fully become the carbonitride of the main cause of matrix surface sclerosis, further improve wearability.
If the average bed thickness of matrix surface hardened layer is to be similarly below 0.5 μ m with above-mentioned hard alloy substrate, wearing and tearing earlier under the state that can't give full play to wearability, if more than 3.0 μ m, easily collapse cutter.
In addition, in surface-coated cutting tool of the present invention, can on the surface of tool base, directly not form above-mentioned aluminium oxide, but form hard film well known by persons skilled in the art by physical vapor deposition (PVD) method, chemical vapor deposition (CVD) method or sol-gel process, after the nitride of at least one element in containing 4a, 5a, 6a family and the Si be selected from periodic table or the hard film more than 1 layer that oxide forms, at the superficial layer of this hard film, coat and form above-mentioned alumina layer.
In addition, while by above-mentioned physical vapor deposition (PVD) method, forming hard film, for the hard film adjacent with alumina layer, from improving adhering viewpoint, be preferably formed as in this hard film and contain Al, and Al in the metal of this hard film forms shared containing proportional be nitride epithelium (such as TiAlN film, CrAlN film etc.) more than 40 atom %.
This be because, if the metal of Al in hard film in forming shared containing proportional be nitride epithelium more than 40 atom %, on the interface of nitride epithelium and aluminium oxide epithelium, form the higher oxide of aluminum concentration, this oxide becomes and has the effect of bond securely nitride epithelium and aluminium oxide epithelium.
Form the alumina layer of superficial layer of surface-coated cutting tool of the present invention by sol-gel process film forming described later, its matrix consists of aluminium oxide crystalline phase and amorphous phase thus, and the spheroidal structure formed at the aggregation that is formed with one or both and amorphous phase in needle-like crystalline phase and tabular crystalline phase in this matrix.
About above-mentioned spheroidal structure, while by SEM (SEM), observing alumina layer, as shown in Figure 1 and Figure 2, observing radius is the conglobulation soma of 0.02～0.5 μ m, if and further this spheroidal structure is observed the known aggregation tissue that forms amorphous phase and needle-like crystalline phase, tabular crystalline phase with transmission electron microscope (TEM).
And, for example, in the scope of field of view 5 * 7 μ m, by observing longitudinal section SEM, obtain this spheroidal structure shared area ratio in aluminium oxide, known is 20～60 area %.
In addition, can be observed according to Fig. 2 on the interface of the aluminium oxide in spheroidal structure and matrix and be formed with recess (in Fig. 2, the black annulus) in the mode of surrounding spheroidal structure.
Its shape of spheroidal structure is exactly that each is arranged in complex tissue on various directions originally, so isotropism is stronger, by its stress dispersion effect, even if also contribute to the wearability of playing stably in applying the heavy cut of high capacity.If above-mentioned spheroidal structure shared area ratio in aluminium oxide surpasses 60 area %, fixedly the ratio regular meeting of the matrix of spheroidal structure diminishes, so the embrittlement tendency occurs at alumina layer, and the ratio of surrounding the recess (with reference to figure 2) of spheroidal structure becomes large, load inhomogeneous while carrying out machining acts on layer, therefore likely produces and destroys.On the other hand, when area ratio is less than 20 area %, owing to contributing to the spheroidal structure that improves wearability to tail off, so the wearability of alumina layer descends.
Therefore, in the present invention, spheroidal structure shared area ratio in alumina layer is decided to be to 20～60 area %.
When the radius of a circle as having the area equated with the area of this spheroidal structure is obtained the radius of above-mentioned spheroidal structure, if radius is less than 0.02 μ m, the effect of the raising wearability in alumina layer diminishes, on the other hand, if radius surpasses 0.5 μ m, become thick tissue, easily become the former of be full of cracks thereby cause anti-reduction of collapsing cutter.
Therefore, the size of above-mentioned spheroidal structure is decided to be to radius 0.02～0.5 μ m.
The alumina layer that forms the superficial layer of surface-coated cutting tool of the present invention can form by sol-gel process shown below.
The preparation of alumina sol:
At first, for example, add alcohol (for example ethanol, n-butyl alcohol) in the alkoxide (aluminium secondary butylate, aluminium propoxide) of aluminium, further add (also can simultaneously add the alpha alumina particles that average grain diameter is 10～300nm) acid (for example hydrochloric acid, nitric acid) afterwards, in the temperature range below 15～30 ℃, stir, and, by carrying out for example maturation process more than 12 hours, form alumina sol.
In addition, when adding alcohol, the promotion when forming alumina layer generates film formation at low temp and the crystalline raising of nucleus, contains in advance the alcohol of the alpha alumina particles that average grain diameter is 10～300nm from the preferred interpolation of the viewpoint of making uniform colloidal sol.And, this be because, when coating, alpha alumina particles becomes the core of the starting point that becomes the crystal growth, the effect that there is as center the conglobulation tissue of favorable dispersibility ground formation homogeneous diameter in alumina layer, but add while containing alpha alumina particles pure, if the average grain diameter of alpha alumina particles is less than 10nm, do not reach the critical nucleus size of the starting point that can become the crystal growth, so not from the growth of the alumina sol generation crystal around alpha alumina particles, and it is isolated from matrix, burn till the rear position weak with the adhesion of crystal grain on every side that easily become.On the other hand, if average grain diameter surpasses 300nm, the alpha alumina particles of usining can grow into excessive big particle as the nucleus of starting point, brings out defect in the reduction of film hardness and film, therefore the mean radius of added alpha alumina particles is decided to be to 10～300nm.
In addition, if the content of alpha alumina particles in alcohol is less than 0.5 quality % with respect to the alkoxide of aluminium, can't meet the required karyogenesis quantity of nucleus distributed equably more than certain density in film, crystallinity in film is different and inhomogeneous according to position, easily brings out inordinate wear while therefore cutting.If the alkoxide with respect to aluminium surpasses 5 quality %, in alumina sol, easily produce the cohesion of alpha alumina particles, while forming alumina layer, this cohesion section forms the big particle in film, therefore bring out defect in film, preferably the addition of alpha alumina particles is made as to the scope that the alkoxide with respect to aluminium is 0.5～5 quality % from this reason.
And the concentration of preferred added acid is 0.01～4.0N, and preferred acid is 0.5～5 times (capacity) with respect to pure addition.
In the preparation of the alumina sol usually carried out, carry out stirring under 40～80 ℃ and the maturation process of about several hours under this whipping temp, but the ripening at low temperature of carrying out for a long time the stirring in the low temperature range of 15～30 ℃ for example spent more than 12 hours in the present invention, is processed.
Wherein, if temperature when stirring and maintenance is over 30 ℃, hydrolysis and polycondensation reaction meeting are carried out fast, so precursor can't form densely, do not form alpha-aluminium oxide in the operation firing process as follow-up, so be defined as 30 ℃ on the temperature in the time of will stirring and keep, on the other hand, if temperature when stirring and maintenance is lower than 15 ℃, in alumina sol, be formed uniformly a plurality of dense Al-O joint portions of constructing, but form the spheroidal structure with size of the present invention, the joint portion that in alumina sol, forms partly a small amount of Al-O closely is for well, so the temperature in the time of will stirring and keep is decided to be hydrolysis, the cryogenic temperature scope of 15～30 ℃ that polycondensation reaction is easily carried out partly.
In addition, will be decided to be long-time more than 12 hours the curing time, be because impel gradually hydrolysis at low temperatures, and alumina precursor is generated densely.
Dry/as to burn till:
To be coated directly onto at the alumina sol of above-mentioned middle preparation the surface of tool base or be applied to the most surface that is formed at the hard film on tool base surface by physical vapor deposition (PVD) method, then, repeatedly carry out 100～400 ℃, the more preferably processing of the drying under 250～350 ℃ more than 1 time, then in the temperature range of 750～1000 ℃, burnt till processing and coat the formation alumina layer.
By the above-mentioned dry dry colloidal sol that forms aluminium oxide of processing, by the processing of burning till of then carrying out, form on hard film surface and take the alumina layer that aluminium oxide crystalline phase and amorphous phase be matrix, meanwhile, in matrix, the spheroidal structure that the aggregation of one or both in needle-like crystalline phase and tabular crystalline phase and amorphous phase forms is distributed in matrix and forms.
The thickness of above-mentioned alumina layer depends on coating thickness and the coating number of times of alumina sol, be less than 0.2 μ m if coat the thickness of the above-mentioned oxide layer formed, as through the long-term surface-coated cutting tool used, bringing into play excellent wearability, on the other hand, if thickness surpasses 5.0 μ m, alumina layer easily produces and peels off, so the thickness of above-mentioned alumina layer is decided to be to 0.2～5.0 μ m.
And, the temperature range that drying is processed is decided to be 100～400 ℃, more preferably 250～350 ℃, and the temperature range that will burn till processing is decided to be the reason of 750～1000 ℃ and is, for baking temperature, if can't be fully dry lower than 100 ℃, if surpass 400 ℃ sol volume shrink and sharply carry out, and generation be full of cracks etc., easily produce peeling off of film etc., for firing temperature, if lower than 750 ℃, can't form and there is the crystalline alumina layer that fully meets heavy cut, therefore wearability is insufficient, on the other hand, if burn till with the temperature over 1000 ℃, can form because of the poor be full of cracks caused of the coefficient of expansion of alumina layer and substrate, and produce the oxidation of carbide alloy or cermet matrix etc., the advantage that can not show film formation at low temp.
According to surface-coated cutting tool of the present invention, most surface in tool base coats formation by the aluminium oxide of sol-gel process film forming, but formed above-mentioned alumina layer possesses excellent surface smoothness, lubricity, wearability, therefore it is hot for generation of height, and the high speed heavy cut that high capacity acts on cast iron, carbon steel of cutting edge etc. adds man-hour, the abnormal damage such as also do not collapse cutter, peel off, through the long-time excellent wearability of performance of using.
The accompanying drawing explanation
Fig. 1 mean for instrument 1 use SEM of the present invention observe its alumina layer longitudinal section organize photo.
Fig. 2 means in instrument 1 of the present invention to be distributed in the surperficial SEM photo of the spheroidal structure in its alumina layer.
The specific embodiment
Then according to embodiment, the present invention is carried out to more specific description.
[embodiment 1]
As material powder, prepare the particulate WC powder of average grain diameter 0.8 μ m, the middle grain WC powder of average grain diameter 2 ~ 3 μ m and TiCN powder, ZrC powder, TaC powder, NbC powder, the Cr that all there is the average grain diameter of 1～3 μ m
3c
2powder and Co powder, coordinate these material powders with the predetermined mix proportion shown in table 1, further add paraffin and mix 24 hours with ball mill in acetone, become the pressed compact of reservation shape after drying under reduced pressure with the pressure punch forming of 98MPa, in the vacuum of 5Pa, this pressed compact of vacuum-sintering under the maintenance of the temperature with the 1400 ℃ condition of 1 hour, after sintering, by the cutting blade being implemented to the cutting edge reconditioning processing of R:0.05mm, manufacture has the WC base cemented carbide tool base A processed of the blade shapes of stipulating in ISOCNMG120408, B, a, b, C1, C2, C3, C4 and C5(are called tool base A, B, a, b, C1, C2, C3, C4 and C5).
But, about 1400 ℃ of maintenances, after 1 hour, being cooled to the process of 1320 ℃, for tool base C2, be in the blanket of nitrogen of 3.3kPa, to carry out 40 minutes, for tool base C3, be in the blanket of nitrogen of 1kPa, to carry out 40 minutes, for tool base C4, be in the blanket of nitrogen of 2kPa, to carry out 10 minutes, for tool base C5 be in the blanket of nitrogen of 3.3kPa, carry out carrying out in 120 minutes cooling, thereby matrix surface has been carried out to cure process.
Then, formed lower floor for above-mentioned tool base A ~ C5.
And, when forming lower floor, above-mentioned tool base a and b are encased in chemical evaporation plating device, by the membrance casting condition shown in table 2, the Ti compound layer that will consist of the TiCN layer of the TiN layer with granular crystal tissue, TiCN layer, TiCO layer, TiCNO layer, longitudinal growth crystalline structure (below, be expressed as 1-TiCN) forms and has been pre-formed basalis with the epithelium shown in table 4.On the other hand, for above-mentioned tool base A, being encased in one of physical vapor deposition device is in arc ion plating apparatus, be pre-formed the thickness shown in table 4 by Ti
0.5al
0.5the basalis that the N layer forms.
And, by above-mentioned tool base B, the arc ion plating apparatus of packing into equally, be pre-formed the thickness shown in table 4 by Al
0.7cr
0.3the basalis that the N layer forms.
On the other hand, for the not special basalis that forms of above-mentioned tool base C1, C2, C3, C4 and C5.
On the other hand, be prepared as follows alumina sol, this alumina sol is for coating the alumina layer formed as the superficial layer of hard coating layer by sol-gel process.
(a) at first, take molar ratio computing as (aluminium secondary butylate) with the solution composition of each composition in reaction raw materials: (water): (ethanol): (hydrochloric acid)=1:(40～60): after the mode of 20:0.8 is added, stirred in thermostat under the conditions shown in Table 3, kept, prepared thus alumina sol.
(b) then, at the above-mentioned alumina sol of lower floor's surface-coated of above-mentioned tool base A ~ C5.
(c) then, alumina sol after above-mentioned dip coated is carried out to drying under the conditions shown in Table 3 in atmosphere to be processed, and carry out the processing of burning till of 800 ℃, 1 hour in atmosphere, thus by alumina layer of the present invention (, the alumina layer of the spheroidal structure that the aggregation of one or both and amorphous phase in needle-like crystalline phase and tabular crystalline phase of disperseing to distribute in the matrix that has aluminium oxide crystalline phase and amorphous phase to form forms) coat and be formed on most surface, produce the coating tool 1 ~ 12(of the present invention shown in table 4 and be called instrument 1 ~ 12 of the present invention).
For the invention described above instrument 1～12, the result of the longitudinal section of alumina layer being observed by SEM (SEM) confirms: its matrix consists of aluminium oxide crystalline phase and amorphous phase, on the other hand, the aggregation that is distributed in spheroidal structure in matrix one or both and the amorphous phase in needle-like crystalline phase and tabular crystalline phase forms.Utilize transmission electron microscope (TEM) to confirm aluminium oxide crystalline phase and amorphous phase, by the SEAD method, analyze respectively its matrix and spheroidal structure, all obtained clearly electron diffraction pattern and halation pattern.
In Fig. 1, the longitudinal section SEM photo of the alumina layer of instrument 1 of the present invention is shown as an example, and, in Fig. 2, equally for instrument 1 of the present invention, the surperficial SEM photo of the spheroidal structure be distributed in its alumina host is shown.Can determine that according to Fig. 2 spheroidal structure consists of the aggregation of amorphous phase and acicular crystal, plate crystal.
For the invention described above instrument 1～12, about spheroidal structure, the mean radius of the area ratio shared in the longitudinal section of alumina layer and spheroidal structure is by SEM (Carl zeiss society system, ultra55) with the visual field of 50,000 times, observed, for its result, be assumed to be plane and measure the area ratio of spheroidal structure, and measure the approximate radius of a circle when the area of a circle calculates using the area of this spheroidal structure of 5 points, and using its mean value as average-size.
And, utilize SEM to carry out cross-section determination to the average bed thickness of alumina layer simultaneously, result all demonstrates in fact identical with target bed thickness mean value (mean values at 5 places).
Measurement result is shown in to table 4.
And then, about in the invention described above instrument 1 ~ 12 basalis is not set and on hard substrate the instrument of direct formation of film at surface alumina layer, Co content to the tool base surface, by utilizing the Wavelength dispersion type x ray spectroscopic methodology of scanning electron microscope (SEM), in observation visual field, the longitudinal section of tool base from substrate surface in the scope towards depth direction 0.5 ~ 3.0 μ m 1 * 1 μ m carry out surface analysis, quantitative analysis is carried out in 5 visual fields, and adopt its mean value.
In table 4, illustrated in cementation zone bed thickness and cementation zone in conjunction with the phase amount of metal.
[comparative example 1]
For relatively, by following manufacture method, manufacture surface-coated cutting tool.
(a) similarly to Example 1, with the solution composition of each composition in reaction raw materials, take molar ratio computing as (aluminium secondary butylate): (water): (ethanol): (hydrochloric acid)=1:(40～60): the mode of 20:0.8 is added.
(b) then, with embodiment 1 differently, under the state kept with the thermostat temperature shown in table 3, continue to stir in 12 hours, and then slaking 24 hours, prepared alumina sol by such processing.
(c) then, will form respectively the above-mentioned tool base A of the Ti compound layer formed through above-mentioned chemical vapor deposition method and the TiAlN layer formed through physical vapor deposition, AlCrN layer ~ D and not implement the above-mentioned alumina sol of surface-coated of special surface-treated tool base C1 ~ C5.
(d) then, the above-mentioned alumina sol be coated with is processed to carry out drying under the condition shown in table 3 in atmosphere, and then repeatedly be coated with dry until reach predetermined bed thickness, then in atmosphere, with 800 ℃, carry out within 1 hour, burning till processing, the surface-coated cutting tool 1 ~ 9(that produces thus the comparative example shown in table 4 is called comparative example instrument 1 ~ 9).
For above-mentioned comparative example 1～9, the result of also utilizing SEM (SEM) and transmission electron microscope (TEM) to observe alumina layer confirms: spheroidal structure is not dispersed in film.
Then, with following condition, the invention described above instrument 1～12 and comparative example instrument 1～9 have been carried out to the high speed heavy cut processing experiment of spheroidal graphite cast-iron.
State of wear to the high cutting-in cutting test of high speed (common cutting speed and cutting-in amount are respectively 200m/min, 1.0mm) each instrument afterwards of carrying out spheroidal graphite cast-iron under following condition is observed, and the wear extent of knife face after measuring.
The pole of workpiece: JISFCD600
Cutting speed: 380/min
Cutting-in amount: 2.0mm
The amount of feeding: 0.3mm/rev.
Cutting time: 5 minutes
These be the results are shown in table 5.
Table 1
Table 2
Table 3
Table 4
Table 5
[embodiment 2]
(a), as material powder, preparation all has TiCN (TiC/TiN=50/50 by quality ratio) powder, the Mo of the average grain diameter of 0.5～2 μ m
2the C powder, the NbC powder, the TaC powder, WC powder, Co powder and Ni powder, and these raw materials are fitted in to the predetermined mix proportion shown in table 6, with after ball mill wet mixed 24 hours drying, pressure punch forming with 98MPa becomes pressed compact, by this pressed compact in the 1.3KPa nitrogen atmosphere, in the temperature with 1540 ℃, keep under the condition of 1 hour after sintering, by cutting edge partly being implemented to the reconditioning of R:0.07mm cutting edge, manufacture thus the TiCN based ceramic metal tool base D processed of the blade shapes with iso standard CNMG190612, E, d, e, F1, F2, F3, F4 and F5(are called 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 ℃/min from room temperature be warming up to 1540 ℃ and keep 30 minutes after, be made as the vacuum of 13Pa and further 1540 ℃ keep 30 minutes after cooling make its surface sclerosis.For tool base F3, be heat up in the vacuum of 13Pa always and keep 60 minutes at 1540 ℃, for tool base F4 be in the blanket of nitrogen of 1.3kPa from room temperature be warming up to 1540 ℃ and keep 30 minutes after, be made as the vacuum of 13Pa and further keep 5 minutes at 1540 ℃, for tool base F5 be in the blanket of nitrogen of 1.3kPa from room temperature be warming up to 1540 ℃ and keep 30 minutes after, be made as the vacuum of 13Pa and further 1540 ℃ keep 90 minutes after cooling and make its surface sclerosis.
Table 6
(b) then, for above-mentioned tool base D ~ F5, formed lower floor.
And, when forming lower floor, above-mentioned tool base d and e are encased in chemical evaporation plating device, utilize the membrance casting condition shown in table 2, the epithelium formed with the Ti compound of table 8 forms and has been pre-formed basalis.On the other 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 Ti
0.5al
0.5the basalis that the N layer forms.
And, by above-mentioned tool base E, the arc ion plating apparatus of packing into equally, be pre-formed the thickness shown in table 8 by Al
0.7cr
0.3the basalis that the N layer forms.
On the other hand, for the not special basalis that forms of above-mentioned tool base F1, F2, F3, F4 and F5.
Then, be formed with above-mentioned tool base D, the E of basalis, d, e and do not forming all sol-gel process of the preparation condition by table 7 and drying condition film forming alumina layers till bed thickness that makes it similarly to Example 1 of the above-mentioned tool base F1 of basalis ~ F5.
Then, carry out the processing of burning till of 1 hour under 800 ℃ in atmosphere, manufactured the coating tool 13 ~ 24(of the present invention shown in table 8 and be called instrument 13 ~ 24 of the present invention).
For the invention described above instrument 13 ~ 24, the result of the longitudinal section of alumina layer being observed by SEM (SEM) confirms: its matrix consists of aluminium oxide crystalline phase and amorphous phase, on the other hand, the aggregation that is distributed in spheroidal structure in matrix one or both and the amorphous phase in needle-like crystalline phase and tabular crystalline phase forms.
For the invention described above instrument 13 ~ 24, about spheroidal structure, the area ratio shared in the longitudinal section of alumina layer and the mean radius of spheroidal structure are observed with the visual field of 50,000 times by SEM, for its result, be assumed to be plane and measure the area ratio of spheroidal structure, and measure the approximate radius of a circle when the area of a circle calculates using the area of this spheroidal structure of 5 points, and using its mean value as average-size.
Measurement result is shown in to table 8.
[comparative example 2]
For relatively, by following manufacture method, manufactured coating tool.
Use above-mentioned tool base D, E, d, e, under the state kept with the thermostat temperature shown in the table 7 different from embodiment 2, continue to stir 12 hours, and then slaking 24 hours, by such processing, use alumina sol to reach film forming alumina layer till the predeterminated target bed thickness shown in table 8, then, by in atmosphere with 800 ℃ of processing of burning till of carrying out 1 hour, thereby the coating tool 10 ~ 18(that has manufactured the comparative example shown in table 8 is called comparative example instrument 10 ~ 18).
For comparative example instrument 10 ~ 18, the result of utilizing SEM (SEM) and transmission electron microscope (TEM) to observe alumina layer confirms: spheroidal structure is not dispersed in film.
Then, with following condition, the invention described above instrument 13～24 and comparative example instrument 10 ~ 18 have been carried out to the high speed heavy cut processing experiment of cast iron.
State of wear to the high feeding machining test of the high speed to carry out cast iron under following condition (common cutting speed and the amount of feeding are respectively 250m/min, 0.3mm/rev.) each instrument is afterwards observed, and measures the wear extent of rear knife face.
The pole of workpiece: JISFC350
Cutting speed: 400/min
Cutting-in amount: 1.5mm
The amount of feeding: 0.4mm/rev.
Cutting time: 20 minutes
These be the results are shown in table 9.
Table 7
Table 8
Table 9
From being shown in table 5,9 result, in surface-coated cutting tool 1～24 of the present invention, coat the formation aluminium oxide by sol-gel process in the most surface of tool base, this alumina layer possesses excellent surface smoothness, lubricity, chip discharge, deposit resistance property, so during by this processing such as high speed heavy cut for cast iron, carbon steel etc., can not produce the abnormal damage such as collapse cutter, peel off, through the long-time excellent wearability of performance of using yet.
On the other hand, in the surface-coated cutting tool 1～18 of the clearly known comparative example not containing spheroidal structure on the alumina layer of most surface and only being formed by matrix organization, bear the incessantly high capacity of heavy cut, especially because the abnormal damage in rake face produces crescent hollow abrasion more sharply, therefore wear no resistance and arrive at short notice service life.
In addition, in described embodiment, although utilize the instrument of blade shapes to estimate the performance of hard coating layer, in the nature of things, utilize drill bit, slotting cutter also can access same result.
Utilizability on industry
Surface-coated cutting tool according to invention, coat and form aluminium oxide in most surface by sol-gel process, this alumina layer possesses excellent surface smoothness, lubricity, chip discharge, deposit resistance property, even so the high speed heavy cut that it is used in to cast iron, carbon steel etc. adds man-hour, can not produce the abnormal damage such as collapse cutter, peel off yet, through the long-time excellent wearability of performance of using, long lifetime that can the implementation tool life-span, practical function is larger.
Claims (5)
1. a surface-coated cutting tool, its surface in the tool base consisted of tungsten carbide base carbide alloy, base titanium carbonitride coats and forms hard coating layer and form, it is characterized in that,
(a) possess the superficial layer of the alumina layer of the average bed thickness with 0.2～5 μ m as above-mentioned hard coating layer,
(b) above-mentioned alumina layer consists of matrix and the spheroidal structure that is dispersed in matrix,
(c) above-mentioned matrix consists of aluminium oxide crystalline phase and amorphous phase, and the aggregation of one or both and the amorphous phase of above-mentioned spheroidal structure in needle-like crystalline phase and tabular crystalline phase forms.
2. surface-coated cutting tool as claimed in claim 1, is characterized in that,
Spheroidal structure shared area ratio in above-mentioned alumina layer is 20～60 area %.
3. surface-coated cutting tool as claimed in claim 2, is characterized in that,
The approximate radius of a circle of above-mentioned spheroidal structure is 0.02～0.5 μ m.
4. surface-coated cutting tool as described as any one in claim 1 ~ 3, its surface in the tool base consisted of tungsten carbide base carbide alloy coats and forms hard coating layer and form, it is characterized in that,
Surface from above-mentioned tool base has formed the matrix surface hardened layer of the average bed thickness with 0.5 ~ 3.0 μ m towards depth direction, as the average content that is contained in the Co in conjunction with the phase metal in this matrix surface hardened layer, be less than 2.0 quality %.
5. surface-coated cutting tool as described as any one in claim 1 ~ 3, its surface in the tool base consisted of base titanium carbonitride coats and forms hard coating layer and form, it is characterized in that,
Surface from above-mentioned tool base has formed the matrix surface hardened layer of the average bed thickness with 0.5 ~ 3.0 μ m towards depth direction, as being contained in the Co in conjunction with the phase metal in this matrix surface hardened layer and the overall average content of Ni, be less than 2.0 quality %.
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| JP2011268562 | 2011-12-08 | ||
| JP2011-268562 | 2011-12-08 | ||
| JP2012264891A JP2013139076A (en) | 2011-12-08 | 2012-12-04 | Surface coated cutting tool exhibiting superior wear resistance in high-speed heavy cutting |
| JP2012-264891 | 2012-12-04 |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN114144273A (en) * | 2019-07-29 | 2022-03-04 | 京瓷株式会社 | Coated cutting tool and cutting tool provided with same |
| CN114144272A (en) * | 2019-07-29 | 2022-03-04 | 京瓷株式会社 | Coated cutting tool and cutting tool provided with same |
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| CN114144273A (en) * | 2019-07-29 | 2022-03-04 | 京瓷株式会社 | Coated cutting tool and cutting tool provided with same |
| CN114144272A (en) * | 2019-07-29 | 2022-03-04 | 京瓷株式会社 | Coated cutting tool and cutting tool provided with same |
| CN114144273B (en) * | 2019-07-29 | 2024-01-19 | 京瓷株式会社 | Coated cutting tool and cutting tool provided with same |
| CN114144272B (en) * | 2019-07-29 | 2024-02-20 | 京瓷株式会社 | Coated cutting tool and cutting tool provided with same |
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