CN103787662B - Cubic boron nitride base ultra-high pressure sintered material cutting tool and surface-coated cutting tool - Google Patents
Cubic boron nitride base ultra-high pressure sintered material cutting tool and surface-coated cutting tool Download PDFInfo
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Abstract
The present invention provides a kind of cBN base ultra-high pressure sintered body using tenacity excellent as the excellent cutting element of the fracture resistance of tool base and surface-coated cutting tool.The cutting element of the present invention and surface-coated cutting tool will be containing cBN granules, with reference to phase, TiB2The cBN base ultra-high pressure sintered body of phase and WB phase is as tool base, for this cubic boron nitride base ultra-high pressure sintered body, the mean diameter of cBN granule is 0.5～3.5 μm, and content is 40～75 capacity %, has, in conjunction with dispersed and distributed in phase, the fine TiB that mean diameter is 50～500nm2Mutually with WB phase, and, the TiB in sintered body2The growing amount that amounts to of phase and WB phase is with reference to 5～15 capacity % in phase, this 15～35 capacity % combining in phase is the nitride of Al, more than at least one in oxide, in addition at least one above and inevitable impurity in the nitride for Ti, carbide, boride or carbonitride, and, meet 0.5≤（The growing amount of WB phase）/(TiB2The growing amount of phase)≤1.0 relation.
Description
Technical field
The present invention relates to a kind of cubic boron nitride by tenacity excellent（Represented with " cBN " below）Base ultra-high pressure sintered body
（Hereinafter referred to as cBN sintered body）The cutting element constituting（Hereinafter referred to as cBN instrument）.
Background technology
From known cBN sintered body in the past, there is excellent durability, heat stability and heat conductivity, and resistance to impact and rubbing
Wipe coefficient also excellent and, relatively low with the affinity of ferrous material, therefore play these characteristics and be used as the ferrum such as steel, cast iron
It is the cutting tool material of workpiece.
For example, as Patent Document 1, proposition has the method by cBN sintered body is obtained as below：To be contained using ball mill
The material powder having Ti based compound pulverizes, mix after, with the cooperation of cBN powder, mix and make molded body, and it is carried out
Sintering, thus obtain using one of the carbide of Ti, nitride and carbonitride or two or more as matrix and in this base
Be uniformly dispersed in body less than 10 capacity % less than 50 capacity % mean diameter be 4～20 μm cBN, 0.1～1.0 appearance
The Al that the mean diameter measuring % is less than 0.2 μm of WC, the mean diameter of 3～10 capacity % is less than 0.2 μm2O3, 3～7 capacity %
Mean diameter be less than 0.5 μm of the mean diameter of AlN and 1～5 capacity % be less than 0.5 μm of TiB2CBN sintered body come
As for by the mar proof of the high speed continuous cutting such as glass hard steel, chilled cast iron, fracture resistance and resistance to collapse knife excellent
CBN sintered body.
And, for example propose there is following cBN sintered body shown in patent documentation 2：By the material powder containing Ti based compound
Make molded body, and after being crushed, pulverizing, by predetermined particle diameter and the cBN mixture of powders of scheduled volume is added in slurry,
And the slurry that this contains cBN is carried out being pulverized and mixed, is dried and molding pressed compact, and it is sintered, so that sintered body
Contained TiB in matrix phase2's（101）The XRD peak height of peak value is less than cBN's（111）The 12% of the peak heights at peak, and resistance to
Defect, breakage resistance are improved.
In addition, for example proposing there is following technology shown in patent documentation 3：Comprising the average grain of volume of about 60～80 volumes %
In the cBN sintered body of the tungsten of cBN, the vitrified bonding phase of about 40～20 volumes % and about 3～15 weight % of about 3～6 μm of degree, pottery
About 20～60 volumes % in porcelain binding agent by the 4th race or the 6th race's metal carbide, nitride or boride more than one
Constitute, and about 40～80 volumes % of surplus by the carbide of aluminum, nitride, boride or oxide more than one constitute, and
And the generation suppression TiB of the WB phase in sintered body2Generation and make fracture resistance reduce, therefore by WB/ in terms of XRD intensity ratio
TiB2Suppress to the fracture resistance to improve cBN sintered body less than 0.4.
Patent documentation 1：Japanese Patent Publication 8-81270 publication
Patent documentation 2：Japan Patent public affairs table 2008-528413 publication
Patent documentation 3：Japanese Patent Publication 2004-160637 publication
CBN sintered body shown in above-mentioned patent documentation 1,2 is all by making the Ti boride of high rigidity（TiB2）Mutually it is scattered in
Realize the raising of the mar proof of cBN sintered body in conjunction with phase, but in the past, because uncontrollable dispersed and distributed is in reference in phase
The generation size of Ti boride phase, generate form, therefore exist in cBN sintered body, at cBN granule and the interface with reference to phase
Generate banding, membranaceous Ti boride phase, or the situation forming bulk Ti boride phase in reference to phase.
And, in this case, because of decline and the coefficient of thermal expansion of cBN granule and the adhesion of the interface with reference to phase
Difference, these reasons become starting point and are easily caused the generation/progress of cracking, and become that the toughness of cBN sintered body reduces is former
Cause.
Especially, when cBN sintered body being used as cutting element, because in machining, high load capacity, impact etc. act on cBN
Sintered body, the defect therefore causing because toughness reduces, breakage become serious problem.
And, the cBN sintered body shown in above-mentioned patent documentation 3, contains W in sintered body, therefore give birth in sintering simultaneously
Become Ti boride phase and W boride phase, but the generation of W boride phase suppresses the Ti boride phase of cBN granule-combine boundary
Generate, therefore, cBN granule-combine boundary adhesion reduce, this become cracking produce starting point and exist fracture resistance fall
Low problem.
Content of the invention
The present invention completes to solve above-mentioned problem, its object is to provide one kind by making microgranule Ti boride
Mutually and W boride is mutually scattered in the high tenacity to realize in Ceramic bond phase with reference to phase, the toughness of raising sintered body, therefore by
Even if the cBN instrument that this cBN sintered body is constituted acts under the Cutting and machining conditions of cBN instrument in high load capacity, impact etc., also can
Play excellent fracture resistance through long-term.
The present inventor etc. are to solve above-mentioned problem, to the cBN instrument being made up of cBN sintered body, are conceived to reference to institute in phase
The Ti boride containing（Below with " TiB2" represent）Phase and W boride（Represented with " WB " below）The growing amount of phase, growing amount ratio
Rate and dispersed and distributed form, the result furtherd investigate has obtained following opinion.
In the past, when manufacturing cBN sintered body, to the Ti based compound containing the mesophase constituting sintered body, W based compound etc.
Material powder pulverized after, add cBN powder and mixed, pulverized and made molded body, and this molded body is carried out
Sinter and to obtain cBN sintered body.
But, the present inventor waits and finds in the manufacturing process of above-mentioned cBN sintered body, to containing the centre constituting sintered body
After the material powder of the Ti based compound of layer etc. is mixed, add hexagonal boron before adding cBN powder（Below
Represented with " hBN "）Powder and W based compound powder simultaneously carry out mixing, pulverize, then, the material powder that obtain here and cBN
Powder is mixed and is carried out molding-sintering, and result gained cBN sintered body has adamant by being formed with reference to dispersed and distributed in phase
Matter is fine TiB2Phase, WB phase are without forming the TiB of bulk in reference to phase2Phase, the sintering structure of WB phase are improving cBN
The toughness of sintered body, when the cBN sintered body with this tissue is used as cBN instrument, is not susceptible to defect, breakage, is growing
Time plays excellent fracture resistance in using.
The reason this toughness is improved, the result studied further, the present inventor etc. finds as follows：Containing
Constitute before adding cBN powder in the mixed material powder of the Ti based compound of mesophase of sintered body etc., add hexagonal crystal nitrogen
Change boron（Represented with " hBN " below）Powder and W based compound powder simultaneously carry out mixing, pulverize, thus fine hBN granule and micro-
Thin W based compound granule is uniformly distributed in reference to phase, and, this is mixed with cBN powder and is sintered, thus fine
HBN granule and Ti metal ingredient and fine W based compound particle reaction and become fine TiB2Phase, WB phase, as a result,
In the combination phase of cBN sintered body after sintering, form fine TiB2Mutually and WB phase is uniformly dispersed the sintering structure that is distributed.
And find, when the cBN sintered body with this sintering structure is used as cBN instrument, even if in machining
When high load capacity, impact etc. act on cBN instrument, by with reference to phase high tenacityization suppression cracking generation, progress, therefore resistance to lack
Damage property is improved.
The present invention is completed based on above-mentioned opinion, has following feature：
（1）A kind of cubic boron nitride base ultra-high pressure sintered material cutting tool, will be containing cubic boron nitride granule, combination
The cubic boron nitride base ultra-high pressure sintered body of phase, Ti boride phase and W boride phase as tool base, wherein,
For cubic boron nitride base ultra-high pressure sintered body, the mean diameter of cubic boron nitride granule is 0.5～3.5
μm and content is 40～75 capacity %, and, have, with reference to dispersed and distributed in phase, the fine Ti boron that mean diameter is 50～500nm
Compound phase and the fine W boride phase that mean diameter is 50～500nm, the growing amount of Ti boride phase and W boride phase it
With at least for reference to 5～15 capacity % in phase, this 15～35 capacity % combining in phase is the nitride of Al, in oxide
More than kind, in addition at least one above and inevitable in the nitride for Ti, carbide, boride or carbonitride
Impurity, and,
Meet 0.5≤（The growing amount of W boride phase）The relation of/(growing amount of Ti boride phase)≤1.0.
（2）A kind of Surface coating cubic boron nitride base ultra-high pressure sintered material cutting tool, wherein,
As（1）In described cubic boron nitride base ultra-high pressure sintered material cutting tool, in the surface of tool base evaporation
It is formed with hard coating layer.
Hereinafter, the present invention will be described.
＜ cBN granule ＞
In this invention, the mean diameter of the cBN granule in cBN sintered body is 0.5～3.5 μm, its content is set to 40～
75 capacity %.
If the mean diameter of cBN granule is less than 0.5 μm, be for example used for glass hard steel etc. high-speed cutting processing when, no
Method plays sufficient fracture resistance by long-term use, on the other hand, if the mean diameter of cBN granule more than 3.5 μm it is likely that
Lead to polished surface precision to reduce, therefore the mean diameter of cBN granule is set to 0.5～3.5 μm.
And, if the content ratio of cBN is less than 40 capacity %, the hardness as cBN instrument is insufficient, in glass hard steel
Deng high-speed cutting processing in abrasion progress aggravation, on the other hand, if the content ratio of cBN is more than 75 capacity %, in conjunction with phase
Content ratio reduces relatively, and dispersed and distributed is in reference to the TiB in phase simultaneously2Phase, the amount of WB phase also reduce, and cBN sintered body
Toughness improves effect and reduces, and therefore the content ratio of shared cBN granule in cBN sintered body is set to 40～75 capacity %.
<The nitride of Al, oxide>
In this invention, by AlN, Al contained in cBN sintered body2O3One or more of be set to reference to 15～35 in phase
Capacity %.The capacity % in combination phase now represents and is set to the total capacity of the composition in addition to cBN granule in cBN sintered body
When 100, with AlN, Al2O3The Capacity Ratio of sum.
If AlN, Al2O3More than one be less than with reference to 15 capacity % in phase, then caking property reduces, thus combine mutually cannot
Keep cBN granule, the intensity of cBN sintered body declines.On the other hand, if AlN, Al2O3One or more of exceed with reference in phase
35 capacity %, then at cBN granule and the interface with reference to phase or combine AlN, the Al generating in phase2O3Increase, therefore cBN sintered body
Toughness reduces, in the high-speed cutting processing of glass hard steel by relatively low for hardness AlN, Al2O3Produce cracking as starting point early stage,
Therefore by AlN, Al2O3One or more of be set to 15～35 capacity % with reference to the content ratio in phase.
<TiB2Phase, WB phase>
TiB in the combination phase of cBN sintered body for the dispersed and distributed2Phase, WB phase, the such as manufacture of the cBN sintered body of the present invention
Method（Aftermentioned）Described, by for forming the Ti compound in the material powder combining phase（Such as TiAl, TiAl3、Ti3Al、
TiN and TiCN etc.）Powder, W compound（Such as WC etc.）The reaction of powder and microgranule hBN powder and formed, therefore in order to improve
Its reactivity, preferably Ti compound powder, W compound powder and hBN powder all by mix, pulverize and by fine-powdered.
But, in fine-powdered to reference to the TiB in phase2When phase, the mean diameter of WB phase are respectively lower than the degree of 50nm, come
Increase from being mixed into of impurity such as the oxygen of hBN powder, moisture, the probability that therefore flexible reduces on the contrary, on the other hand, in non-mistake
Degree fine-powdered, and combine the TiB in phase2During size respectively more than 500nm of phase, the mean diameter of WB phase, can be formed thick
TiB2Phase, thick WB phase, in addition, in TiB2The hBN of the core remained unreacted of phase, and WB phase central part remain not
The W compound of reaction, therefore causes toughness to reduce and also become cracking Producing reason, therefore dispersed and distributed sinters in cBN
TiB in the combination phase of body2Phase, the mean diameter of WB phase need to be set to 50～500nm.
In this invention, TiB2The ratio of the growing amount of phase and the growing amount of WB phase（=（The growing amount of WB phase）/（TiB2Phase
Growing amount））Preferred ratio be 0.5～1.0, preferred ratio be 0.8～1.0.This is because, work as TiB2The growing amount of phase
When being less than 0.5 with the ratio of the growing amount of WB phase, TiB2The growing amount of phase increases, and therefore can generate the TiB of bulk2Phase, is made
Easily produce cracking for starting point, thus expected life tools sometimes cannot be obtained, on the other hand, work as TiB2The growing amount of phase
During with the ratio of the growing amount of WB phase more than 1.0, because the WB phase with reference to hard in phase increases, the fragility with reference to phase increases, because
This reduces as the toughness of cBN sintered body, thus by TiB2The ratio of the growing amount of phase and the growing amount of WB phase is set to 0.5～
1.0.
TiB in conventional cBN sintered body shown in Fig. 12Phase, the dispersed and distributed situation of WB phase.
Fig. 1's（a）For secondary electron image,（b）Mapping graph picture for B,（c）Mapping graph picture for Ti,（d）Reflecting for W
Penetrate image, Fig. 1's（b）、（c）Lap become TiB2The formation zone of phase, and,（b）、（d）Lap become
The formation zone of WB phase.
TiB in the cBN sintered body of the present invention shown in Fig. 22Phase, the dispersed and distributed situation of WB phase.
Identical with Fig. 1, Fig. 2's（a）For secondary electron image,（b）Mapping graph picture for B,（c）Mapping graph picture for Ti,
（d）Mapping graph picture for W, from Fig. 2's（b）、（c）Lap be TiB2The formation zone of phase and（b）、（d）Overlapping portion
The formation zone dividing i.e. WB phase understands, in the cBN sintered body of the present invention of Fig. 2, TiB2Mutually and WB phase dispersed and distributed is in combining phase
In.
Fig. 3 is the figure representing the sintering structure of cBN sintered body of the present invention with schematic diagram.
In Fig. 3, TiB2Phase, WB phase are as micro organization（Mean diameter is 50～500nm）Dispersed and distributed is in cBN sintered body
Combination phase in.
And, in the present invention, by specifying this TiB2Phase, the dispersity of WB phase, are capable of based on hard TiB2
Phase, the dispersion of WB phase improve the toughness combining phase additionally it is possible to realize being based on fine dispersion phase（TiB2Phase）Presence and be based on its
He combines phase constituent（Such as TiN, TiC and TiCN etc.）Crystal grain-growth suppress improving toughness.
And, in this invention, TiB2Growing amount sum with WB phase need to be with reference to 5～15 capacity % in phase.Now
Represent in conjunction with the capacity % in phase when the total capacity of the composition in addition to cBN granule in cBN sintered body is set to 100, with
TiB2Phase, the Capacity Ratio of the growing amount sum of WB phase.
Work as TiB2Mutually and when the growing amount sum of WB phase is less than with reference to 5 capacity % in phase, dispersed and distributed is in reference in phase
TiB2Mutually less with the amount of WB phase, therefore cannot play the effect that suppression combines the grain growth of phase constituent, on the other hand, when
TiB2Mutually and when the growing amount sum of WB phase exceedes with reference to 15 capacity % in phase, in conjunction with the TiB of hard in phase2Mutually increase with WB phase
And the fragility with reference to phase increases, therefore the toughness as cBN sintered body reduces.
Therefore, in this invention, TiB2The growing amount sum of phase and WB phase need to be with reference to 5～15 capacity % in phase, this
In the case of, the toughness of cBN sintered body can be improved, when this cBN sintered body is used as cBN instrument, using the teaching of the invention it is possible to provide resistance to defect
Property cBN instrument that is excellent and playing excellent cutting ability by long-term use.
Manufacture method ＞ of ＜ cBN sintered body
One of the step of cBN sintered body of the tenacity excellent for making this invention described below.
（a）First, composition of preparation combines the material powder of the composition of phase.
As material powder, prepare Ti compound powder（For example TiN powder, TiC powder, TiCN powder, TiAl powder,
TiAl3Powder, Ti2AlN powder, Ti3Al powder and Ti4Al2C2Powder etc.）, or add in the past known on this basis further
Combination phase formation material powder（Al powder, Al2O3Powder, AlN powder etc.）.
（b）These material powders are filled into for example with hard alloy liner in the lump with WC sintered carbide ball and acetone
In ball mill, pulverized by rotating ball mill after closeing the lid and mixed.
（c）Then, by mean diameter be 1～5 μm hBN powder integrally to become about 0.8～about 7.0 weight with respect to powder
The mode of amount % is added, and, by mean diameter be 0.5～3 μm WC powder integrally becoming about 1.5 with respect to powder～about
The mode of 18.0 weight % is added, and similarly carries out pulverizing and the mixing of 24～72 hours in ball mill, and hBN powder is pulverized
Become 500nm particles below hBN, and, WC powder is ground into 500nm particles below WC powder, and so that it is equably divided
Dissipate in reference in phase.
（d）Then, carried out pulverizing, the hBN powder of mixing and combined mutually formation material powder to above-mentioned, added average
Particle diameter is 0.5～3.5 μm of cBN powder, and, carries out the mixing of 24 hours in ball mill.
（e）Then, gained sintered body material powder is made molded body with predetermined pressure molding, and in pressure：10-4Pa
In following vacuum atmosphere, after presintering being carried out to this sintered body with 900～1300 DEG C, load in ultra-high pressure sintering device,
By with pressure：5GPa, temperature：The cBN that predetermined temperature in the range of 1200～1400 DEG C is sintered making the present invention burns
Knot body.
The present invention is especially with above-mentioned operation（c）It is characterized, by setting this operation（c）And make cBN sintered body, can make
Fine TiB2, in reference in phase, the toughness thereby, it is possible to realize cBN sintered body improves for phase, WB phase dispersed and distributed.
In addition, TiB2Phase, the mean diameter of WB phase（50～500nm）、TiB2Total growing amount with WB phase（Capacity %）
And TiB2The ratio of the growing amount of phase and the growing amount of WB phase（=（The growing amount of WB phase）/（TiB2The growing amount of phase））Mainly can
By above-mentioned operation（c）The addition of hBN, the addition of W based compound powder, pulverizing/mixing condition is being adjusted.
<CBN instrument>
Using the cBN sintered body of tenacity excellent as this invention of tool base cBN base ultra-high pressure sintered material cutting tool
For example in the high-speed cutting processing of glass hard steel, still there is excellent fracture resistance, and play excellent cutting by long-term use
Cut performance.
And, the cBN sintered body inventing this is as tool base, passes through the evaporation such as physical vapor deposition thereon and form hard
The Surface coating cBN base ultra-high pressure sintered material cutting tool of clad, even if for example in the high-speed cutting processing of glass hard steel
Also play excellent fracture resistance, wherein, this hard coating layer is for example by the composite nitride nitride layer of TiN layer and Ti and Al
Layer or two-layer and these layer of alternately laminated multilamellar is constituted.
As above-mentioned, in the cBN instrument of the present invention, particularly by the TiB in the combination phase of regulation cBN sintered body2Phase, WB phase
Mean diameter, growing amount and generate ratio, the cBN sintered body of tenacity excellent can be obtained, this cBN instrument（CBN base ultra-high pressure
Sintered material cutting tool, Surface coating cBN base ultra-high pressure sintered material cutting tool）In the high-speed cutting processing of glass hard steel still
Show excellent fracture resistance, and play excellent cutting ability by long-term use.
Brief description
Fig. 1 represents the TiB in conventional cBN sintered body2The dispersed and distributed situation of phase,（a）For secondary electron image,（b）
It is the mapping graph picture of the B element being obtained by auger electron spectroscopic analysis,（c）It is the Ti being obtained by auger electron spectroscopic analysis
The mapping graph picture of element,（d）It is the mapping graph picture of the W element being obtained by auger electron spectroscopic analysis.
Fig. 2 represents the TiB in the cBN sintered body of the present invention2The dispersed and distributed situation of phase,（a）For secondary electron image,
（b）It is the mapping graph picture of the B element being obtained by auger electron spectroscopic analysis,（c）It is to be obtained by auger electron spectroscopic analysis
Ti element mapping graph picture,（d）It is the mapping graph picture of the W element being obtained by auger electron spectroscopic analysis.
Fig. 3 is the figure representing the sintering structure of cBN sintered body of the present invention with schematic diagram.
Specific embodiment
Hereinafter, according to embodiment, the present invention will be described.
[embodiment]
（a）First, as shown in table 1, prepare to be made up of the predetermined composition of the combination phase constituting sintered body and mixing ratio
Material powder.
（b）Then, above-mentioned raw materials powder is filled into sintered carbide ball and acetone in the lump with the ball of hard alloy liner
In grinding machine, pulverized by rotating ball mill after closeing the lid and mixed.
（c）Then, by the hBN powder of the mean diameter shown in table 2 and WC powder, respectively with same with respect to powder gross weight
The mode that sample becomes the adding proportion shown in table 2 is added, and similarly carries out the pulverizing of the time shown in table 2 in ball mill and mixes
Close.
（d）Then, to above-mentioned carried out pulverizing, the hBN powder of mixing and combine mutually formation material powder, with respect to
Powder gross weight similarly becomes the cBN powder of the mean diameter shown in mode interpolation table 2 of the adding proportion shown in table 2, with
Carry out mixing in 24 hours in ball mill sample.
（e）Then, by gained sintered body material powder, diameter is become with molding pressure 100MPa punch forming：50mm × thickness：
The size of 1.5mm, then, by this molded body in pressure：10-4In the vacuum atmosphere of below Pa, in the range of 900～1300 DEG C
Predetermined temperature keeps and carries out presintering, afterwards, loads ultra-high pressure sintering device, with pressure：5GPa, temperature：1200～1400
Predetermined temperature in the range of DEG C is sintered making cBN sintered body 1～12 of the present invention（Referred to as part 1～12 of the present invention）.
[table 1]
[table 2]
In order to compare, by with part 1～12 identical method of the present invention, or in above-mentioned operation（c）In without allocating in advance
The all hBN powder of particle diameter or methods of WC powder, the cBN sintered body 1～12 of comparison example（Referred to as compare part 1～12）.
To by part of the present invention 1～12 obtained above with compare part 1～12, obtain with reference to the TiB in phase2Phase average
Particle diameter, growing amount or combine the mean diameter of WB phase in phase, growing amount, and (the WB phase growing amount in conjunction with phase)/（In conjunction with
TiB in phase2Phase growing amount）Ratio.
CBN granule is also measured with mean diameter and its content ratio.And, it is also measured to the nitride of Al, oxide
Content ratio.
TiB described below2The assay method of the mean diameter of phase.
In order to measure TiB2The mean diameter of phase, by the observation only to the combination phase of cBN sintered body for the auger electron spectroscopy
Visual field is analyzed.Afterwards, the mapping graph picture of the Ti element being obtained based on auger electron spectroscopic analysis is become to specific strength
It is changed to the Blue of RGB, and the contrast intensity transformation of the mapping graph picture of B element is the Red of RGB, closed by image procossing
Become.By graphical analyses, the threshold value of the RGB of composograph is set as R：30～255, G：0、B：30～255（Threshold range：0
～255）And binaryzation, thus draw out the whole TiB in picture2Phase.The TiB that will extract out2The major diameter of the granule of phase is as this
The particle diameter of grain, using their meansigma methodss as TiB2The mean diameter of phase.
TiB described below2The assay method of the growing amount of phase.
Extract described TiB out2After phase, by its gross area of image analysis calculation, it is calculated divided by total image area
This area ratio is thus considered as capacity % by area ratio, measures the TiB combining in phase2The growing amount of phase.
To above-mentioned 2, by each 5 visual fields of 100,000 times of image to auger electron spectroscopic analysis by said method
The meansigma methodss of value obtained from being processed are as measurement result.
Mensure to the mensure of the mean diameter of WB phase, growing amount, also by with above-mentioned with regard to TiB2Molybdenum determination is same
Method carry out.
That is, only the observation visual field of the combination phase of cBN sintered body is analyzed by auger electron spectroscopy, and by W element
The contrast intensity transformation of mapping graph picture be the Blue of RGB, and the contrast intensity transformation of the mapping graph picture of B element is RGB
Red, is synthesized by image procossing.By graphical analyses, the threshold value of the RGB of composograph is set as R：30～255, G：
0、B：30～255（Threshold range：0～255）And binaryzation, thus draw out the whole WB phase in picture.By the WB phase extracted out
The major diameter of granule as the particle diameter of this granule, using their meansigma methodss as WB phase mean diameter.
The mensure of the growing amount of WB phase measures by the following method, that is, after extracting described WB phase out, by graphical analyses meter
Calculate its gross area, by its divided by total image area reference area ratio, thus this area ratio is considered as capacity %, measures knot
Close the growing amount of the WB phase in phase.
To above-mentioned 2, by each 5 visual fields of 100,000 times of image to auger electron spectroscopic analysis by said method
The meansigma methodss of value obtained from being processed are as measurement result.
In addition,（In conjunction with the WB phase growing amount in phase）/（In conjunction with the TiB in phase2Phase growing amount）Value asked by by above-mentioned
TiB in the combination phase going out2The growing amount of phase and the growing amount with reference to the WB phase in phase are calculated.
Then, the assay method of the mean diameter of cBN granule described below.
For by the secondary electron image of sem observation, cBN granule is extracted out by image procossing, should
The major diameter of cBN granule as the particle diameter of this granule, using their meansigma methodss as cBN granule mean diameter.
The assay method of the content ratio of cBN granule described below.
After extracting described cBN granule out, will be counted divided by total image area by the value of its gross area of image analysis calculation
Calculate area ratio, thus this area ratio is considered as capacity %, measure the content ratio of cBN granule.
To above-mentioned 2, will be passed through by each 3 visual fields of the 5 of scanning electron microscope, 000 times, 10,000 times of image
The meansigma methodss of the value that said method is processed are as measurement result.
Respective measurement result is shown in table 3.
The nitride of Al described below, the assay method of the content ratio of oxide.
First, using X-ray diffraction device, cBN sintered body is analyzed.Employ the ripple of X-ray as x-ray source
A length ofCuK alpha ray source.X-ray analyses result, confirms only have AlN, Al as the compound of Al2O3Peak value, connect
, in order to measure the nitride of Al, the content ratio of oxide, by the combination phase only to cBN sintered body for the auger electron spectroscopy
Carry out observing blinding analysis, based on the mapping graph picture of Al element, detected by image analysis calculation Al element part total
Area, by the value of this gross area divided by total image area reference area ratio, thus this area ratio is considered as volume %, survey
Determine the nitride of Al, the content ratio of oxide.
Each 5 visual fields of 20,000 times of images to above-mentioned auger electron spectroscopic analysis by said method are processed
Obtained from value meansigma methodss as measurement result.
[table 3]
Then, with spark coil cutting processor by by the part of the present invention 1～12 of above-mentioned making, compare part 1～12 and cut
Be broken into preliminary dimension, using have with quality % count Cu be 26%, Ti be 5%, the solder of the Ag alloy of the composition as remainder for the Ag
Be brazed in have Co be 5 mass %, TaC be 5 mass %, WC be the composition of remainder and the blade of iso standard CNGA120408
The brazed portion of the WC base cemented carbide vane body of shape（Corner）, and implement upper and lower surface and periphery grinding, cutting edge reconditioning
Process, thus producing the cBN base ultra-high pressure sintered body cutting of the present invention of the blade shapes with iso standard CNGA120408
Instrument（Referred to as blade of the present invention）1～12, the cBN base ultra-high pressure sintered material cutting tool of comparative example（Referred to as compare blade）1～
12.
In addition, for blade 1,5,7,9 of the present invention and comparing blade 1,5,7,9, also by physical vapor deposition equally with table 4 institute
The thickness shown coats the hard coating layer shown in formation table 4, thus produces the Surface coating cBN base ultra-high pressure sintering of the present invention
Body cutting element（Referred to as present invention cladding blade）1st, 5,7,9, the Surface coating cBN base ultra-high pressure sintered body skiver of comparative example
Tool（Referred to as compare cladding blade）1、5、7、9.
[table 4]
Then, to above-mentioned blade of the present invention 1～6, the present invention coats blade 1,5, compares blade 1～6 and compares cladding
Blade 1,5, implements machining test with following machining condition, and measures the life tools till defect（sec）.
Carry out the High Speed Dry Cutting processing experiment of glass hard steel with following condition.
" machining condition "
Workpiece：Carburizing and quenching steel（JIS SCM415, hardness：HRC62）Along its length at equal intervals with 1 pod
Pole,
Cutting speed：170m/min、
Cutting-in amount：0.2mm、
Feed speed：0.1mm/rev.
Time by the blade defect of each blade（sec）As life tools.
The measurement result of above-mentioned machining test shown in table 5.
[table 5]
Knowable to result shown in from table 5, compared with comparing blade and comparing cladding blade, blade of the present invention, bag of the present invention
Cover blade blade do not occur sudden collapse knife, life tools are extended, it can thus be appreciated that with compare blade and compare cladding knife
Piece is compared, and the toughness that blade of the present invention, the present invention coat blade is improved.
Then, to above-mentioned blade of the present invention 7～12, the present invention coats blade 7,9, compares blade 7～12 and compares bag
Cover blade 7,9, machining test is implemented with following machining condition, and measures the life tools till defect（sec）.
Carry out the High Speed Dry Cutting processing experiment of glass hard steel with following condition.
" machining condition "
Workpiece：Carburizing and quenching steel（JIS SCM415, hardness：HRC62）Along its length at equal intervals carry 8 pods
Pole,
Cutting speed：150m/min、
Cutting-in amount：0.2mm、
Feed speed：0.2mm/rev.
Time by the blade defect of each blade（sec）As life tools.
The measurement result of above-mentioned machining test shown in table 6.
[table 6]
Knowable to result shown in from table 6, compared with comparing blade and comparing cladding blade, blade of the present invention, bag of the present invention
Cover blade and defect does not occur, life tools are extended, it can thus be appreciated that compared with comparing blade and comparing cladding blade, the present invention
The toughness that blade, the present invention coat blade is improved.
Industrial applicability
Using the cBN sintered body of the tenacity excellent of the present invention as the cBN instrument of tool base, there is not defect, breakage, warp
The excellent fracture resistance of life-time service performance, and achieve the prolongation of life tools, therefore, it is possible to very satisfactorily reply cutting
The saving labourization of the high performance of processing unit (plant) and machining and energy-saving, cost degradation.
Claims (2)
1. a kind of cubic boron nitride base ultra-high pressure sintered material cutting tool, by containing cubic boron nitride granule and with reference to phase
Cubic boron nitride base ultra-high pressure sintered body as tool base, described cubic boron nitride base ultra-high pressure sintered material cutting tool
It is characterised by,
For cubic boron nitride base ultra-high pressure sintered body, the mean diameter of cubic boron nitride granule be 0.5～3.5 μm and
Content is 40～75 capacity %, and, has, with reference to dispersed and distributed in phase, the fine Ti boride that mean diameter is 50～500nm
It is mutually the fine W boride phase of 50～500nm with mean diameter, the growing amount of fine Ti boride phase and W boride phase
Sum is with reference to 5～15 capacity % in phase, this 15～35 capacity % combining in phase is the nitride of Al, in oxide extremely
Few more than one, in addition at least one above in the nitride for Ti, carbide, boride or carbonitride and can not
The impurity avoiding, and,
Meet the relation of growing amount≤1.0 of growing amount/Ti boride phase of 0.5≤W boride phase.
2. a kind of surface-coated cutting tool it is characterised in that
In cubic boron nitride base ultra-high pressure sintered material cutting tool described in claim 1, steam on the surface of tool base
Plating is formed with hard coating layer.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2012236527A JP6032409B2 (en) | 2012-10-26 | 2012-10-26 | Cutting tools and surface-coated cutting tools using a cubic boron nitride-based ultra-high pressure sintered body as a tool base |
| JP2012-236527 | 2012-10-26 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103787662A CN103787662A (en) | 2014-05-14 |
| CN103787662B true CN103787662B (en) | 2017-03-01 |
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| CN201310445743.5A Active CN103787662B (en) | 2012-10-26 | 2013-09-25 | Cubic boron nitride base ultra-high pressure sintered material cutting tool and surface-coated cutting tool |
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| JP (1) | JP6032409B2 (en) |
| CN (1) | CN103787662B (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105693253B (en) * | 2014-11-28 | 2020-12-11 | 三菱综合材料株式会社 | Cubic boron nitride sintered body cutting tool having excellent chipping resistance |
| JP6850980B2 (en) * | 2016-03-07 | 2021-03-31 | 三菱マテリアル株式会社 | Surface-coated cubic boron nitride sintered body tool |
| WO2017154730A1 (en) * | 2016-03-07 | 2017-09-14 | 三菱マテリアル株式会社 | Surface-coated cubic boron nitride sintered tool |
| WO2017204152A1 (en) * | 2016-05-23 | 2017-11-30 | 三菱マテリアル株式会社 | Cubic boron nitride sintered compact cutting tool |
| JP6853951B2 (en) | 2017-03-01 | 2021-04-07 | 三菱マテリアル株式会社 | cBN sintered body and cutting tool |
| GB201704133D0 (en) * | 2017-03-15 | 2017-04-26 | Element Six (Uk) Ltd | Sintered polycrystalline cubic boron nitride material |
| KR20210126568A (en) * | 2019-02-27 | 2021-10-20 | 미쓰비시 마테리알 가부시키가이샤 | cBN sintered compacts and cutting tools |
| EP4079708A4 (en) * | 2019-12-16 | 2023-03-22 | Sumitomo Electric Hardmetal Corp. | Cubic boron nitride sintered body and method for manufacturing same |
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| CN1242350A (en) * | 1998-07-22 | 2000-01-26 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
| CN101595075A (en) * | 2007-01-30 | 2009-12-02 | 住友电工硬质合金株式会社 | Composite sinter |
| CN102190497A (en) * | 2010-03-19 | 2011-09-21 | 三菱综合材料株式会社 | High-toughness crystalline cubic boron nitride-based ultrahigh pressure sintering material and cutting tool |
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| JPH03131573A (en) * | 1989-10-13 | 1991-06-05 | Toshiba Tungaloy Co Ltd | Sintered boron nitrode base having high-density phase and composite sintered material produced by using the same |
| JPH05117037A (en) * | 1991-10-24 | 1993-05-14 | Kobe Steel Ltd | High-hardness sintered compact |
| JPH0881270A (en) * | 1994-09-13 | 1996-03-26 | Mitsubishi Materials Corp | Ceramic sintered compact containing cubic boron nitride and cutting tool |
| US6814775B2 (en) * | 2002-06-26 | 2004-11-09 | Diamond Innovations, Inc. | Sintered compact for use in machining chemically reactive materials |
| KR100843994B1 (en) * | 2004-02-20 | 2008-07-07 | 다이아몬드 이노베이션즈, 인크. | Sintered compact |
| US8673435B2 (en) * | 2010-07-06 | 2014-03-18 | Tungaloy Corporation | Coated cBN sintered body tool |
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- 2012-10-26 JP JP2012236527A patent/JP6032409B2/en not_active Expired - Fee Related
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1242350A (en) * | 1998-07-22 | 2000-01-26 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
| CN101595075A (en) * | 2007-01-30 | 2009-12-02 | 住友电工硬质合金株式会社 | Composite sinter |
| CN102190497A (en) * | 2010-03-19 | 2011-09-21 | 三菱综合材料株式会社 | High-toughness crystalline cubic boron nitride-based ultrahigh pressure sintering material and cutting tool |
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| Publication number | Publication date |
|---|---|
| JP2014083664A (en) | 2014-05-12 |
| JP6032409B2 (en) | 2016-11-30 |
| CN103787662A (en) | 2014-05-14 |
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