CN101031525A - Cubic boron nitride sintered material and cutting tool using the same - Google Patents
Cubic boron nitride sintered material and cutting tool using the same Download PDFInfo
- Publication number
- CN101031525A CN101031525A CN 200580033358 CN200580033358A CN101031525A CN 101031525 A CN101031525 A CN 101031525A CN 200580033358 CN200580033358 CN 200580033358 CN 200580033358 A CN200580033358 A CN 200580033358A CN 101031525 A CN101031525 A CN 101031525A
- Authority
- CN
- China
- Prior art keywords
- boron nitride
- cubic boron
- cbn
- sintered material
- carbide
- 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.)
- Granted
Links
Images
Abstract
A cubic boron nitride sintered material where wear resistance is suppressed from decreasing having excellent chipping resistance and a cutting tool made thereof are provided. The sintered material is constituted from cubic boron nitride particles that are bound by a binder phase, while the binder phase contains a carbide of at least one kind of metal element selected from among metals of groups 4, 5 and 6 of the periodic table and a nitride of at least one kind of metal element selected from among metals of groups 4, 5 and 6 of the periodic table coexisting therein, and therefore the particles can be suppressed from coming off and the binder phase can be suppressed from wearing and coming off at the same time, thereby making the sintered material having high wear resistance and particularly excellent chipping resistance.
Description
Technical field
The present invention relates to cubic boron nitride sintered material that constitutes by bonded bonding cubic boron nitride particles and the cutting tool that uses it.
Background technology
Cubic boron nitride (cBN) is celebrated with the high rigidity characteristic that is only second to diamond, and can react with ferrous metal unlike diamond.Based on this, cubic boron nitride sintered material (cBN agglomerated material) is used for making the steel and the cast iron of cutting tool, the especially high rigidity of cutting iron-bearing materials.
When a cutting instrument is made by the cBN agglomerated material, for example according to patent documentation 1, the cBN agglomerated material of under uht conditions, making by sintering cBN with a kind of its volumetric concentration as tackiness agent the metal of 10%-60% for example cobalt (Co) and pottery for example titanium carbide (TiC) use.Patent documentation 1 is also advised to avoid making the wear-resisting and temperature capacity of cBN agglomerated material impaired, should keep bonding in minimum, forms the structure that all the other cBN directly are bonded to each other.
In recent years, in the metal cutting field, the efficient of cutting operation in urgent need to be improved and give cutting machines to being difficult to the cutting power of cutting material.And the cBN agglomerated material yet needs to improve wear-resistant and the chip resistance ability as basic need.The cBN agglomerated material proposed a kind of by patent documentation 2, for improving its above performance, its cBN particle by a large amount of by the pottery for example intermetallic compound of titanium carbonitride (TiCN), a kind of titanium and aluminium and the adhesives that wolfram varbide (WC) is formed.
[patent documentation 1] Japanese unexamined patent (Kokoku) No.52-43846
[patent documentation 2] Japanese unexamined patent (Kokai) No.2003-175407
Summary of the invention
[problem that the present invention is to be solved]
But, when hard steel or cast iron are used the cutting tool cutting that the cBN agglomerated material introduced in the document 1 makes, produced such problem: the cBN particle comes off in sintered compact in cutting operation, so caused the wearing and tearing of cutting tool significantly to be quickened.
When the method for introducing in using document 2 adds a large amount of tackiness agents, following problem is also arranged: though may limit running out of and the quick generation of cutting tool wearing and tearing of cBN particle, the bonding of being made up of the intermetallic compound and the wolfram varbide (WC) of titanium carbonitride (TiCN), a kind of titanium and aluminium has low mechanical property and low thermal characteristics mutually.Wearing and tearing of tackiness agent phase as a result and the coming off wearing and tearing that significantly caused cutting tool and cracked that become make the life-span of prolongation cutting tool become unlikely like this.
One of the object of the invention be to provide a kind of can the wear-resistant ability drop of restriction and have the cBN agglomerated material of outstanding chip resistance ability and with its cutting tool of making.
[method of dealing with problems]
Inventors of the present invention study wearing and tearing and the cracked problem that successfully solves cutting tool simultaneously.By discovering, the cBN agglomerated material of forming by bonded bonding cBN particle, when bonding contains the carbide of special metal element mutually and is present in the nitride of special metal element wherein simultaneously, can show and use by carbide, nitride or the incomparable excellent properties of forming as their carbonitride of sosoloid of bonding phase time, find that also the cBN agglomerated material with this composition can suppress coming off of cBN particle, can suppress simultaneously bonding weares and teares mutually and comes off, thereby show high wear-resistant ability and, especially, outstanding chip resistance ability has been finished the present invention like this.
Specifically, cBN agglomerated material among the present invention is made up of bonded bonding cBN particle, wherein bonding contain mutually be selected from the periodic table of elements in the 4th, 5,6 family's elements the carbide of at least a metallic element and therein coexistence ground contain and be selected from the periodic table of elements nitride of at least a metallic element in the 4th, 5,6 family's elements.
Another kind of cBN agglomerated material among the present invention has a monfil shape structure, because this structure, the mould component that the cBN agglomerated material that is made of bonded bonding cBN particle is made is covered with the circumferential surface of the fibrous core member that the cBN agglomerated material that is made of bonded bonding cBN particle makes, the bonding that is used for mould component is by being selected from the periodic table of elements the 4th, 5, the nitride of at least a metallic element in the group of 6 group compositions is formed, and the bonding that is used for core component is by being selected from the periodic table of elements the 4th, 5, the carbide of at least a metallic element in the group of 6 group compositions is formed.
And, another kind of cBN agglomerated material among the present invention has a monfil shape structure, this structure makes, the mould component that the cBN agglomerated material that is made of bonded bonding cBN particle is made is covered with the circumferential surface of the fibrous core member that the cBN agglomerated material that is made of bonded bonding cBN particle makes, the bonding that is used for mould component is by being selected from the periodic table of elements the 4th, 5, the carbide of at least a metallic element is formed in 6 families, and the bonding that is used for core component is selected from the periodic table of elements the 4th mutually, 5, the nitride of at least a metallic element is formed in 6 families.
Cutting tool among the present invention is made by above-described cBN agglomerated material among the present invention, and the blade that utilizes the crestal line that meets along the side and the rake of cutting tool to form uses in the metal cutting operation.
[effect of invention]
The main characteristic of the cBN agglomerated material among the present invention is: the nitride of the carbide of special metal element and special metal element exists simultaneously.This has given the intensity of bonding phase certain level and bonding mutually and the bonding force of the certain level between the cBN particle simultaneously, the advantage that these are to use the conventional sintering material of the bonding phase that the carbonitride by carbide, nitride or their sosoloid constitutes not obtain.Coming off and suppressing the wearing and tearing of bonding phase simultaneously and come off of the so just feasible cBN of prevention particle becomes possibility, so just gives the cBN agglomerated material and has high abrasion resistance properties and greatly improve its chip resistance ability.
As a result, cBN agglomerated material and cutting tool among the present invention in cutting operation under the normal condition, can intermittently cut for example steel of high rigidity of the material that is difficult to cut, and show excellent wear-resistant and chip resistance ability.
Description of drawings
Fig. 1 (a) is a cBN agglomerated material structural representation among the present invention, and Fig. 1 (b) is the cBN agglomerated material structural representation with bonding phase of homogeneous composition.
Fig. 2 is the X-ray diffraction analysis chart of cBN agglomerated material among the present invention, has shown diffraction peak.
Fig. 3 is the cBN agglomerated material schematic cross-section of the 5th embodiment.
Fig. 4 (a) is the schematic cross-section that has the cBN agglomerated material of monfil shape structure among the present invention, and Fig. 4 (b) is the skeleton view of Fig. 4 (a).
Fig. 5 (a) is the schematic cross-section that has the cBN agglomerated material of multifilament shape structure among the present invention, and Fig. 5 (b) is the skeleton view of Fig. 5 (a).
Fig. 6 (a) is the perspective diagram that shows the arrangement example of the cBN agglomerated material that has filamentary structure among the present invention to Fig. 6 (d).
Fig. 7 (a) and Fig. 7 (b) are that demonstration prepares compound living pressed compact (green compact) method synoptic diagram according to the method that preparation of the present invention has the cBN agglomerated material of monfil shape structure.
Fig. 8 is that demonstration prepares the method synoptic diagram of giving birth to pressed compact according to the method that preparation of the present invention has the cBN agglomerated material of monfil shape structure.
Fig. 9 shows that method that preparation of the present invention has a cBN agglomerated material of monfil shape structure prepares the method synoptic diagram of the living pressed compact of another form.
Figure 10 is the skeleton view that the embodiment of cutting tool among the present invention is shown.
Figure 11 (a) is the schematic cross-section of example that shows the structure at the blade tip angle (tool tip corner) among the present invention, and Figure 11 (b) is the schematic cross-section that shows the structure at the blade tip angle in the another one example.
[reference number explanation among the figure]
1 cBN agglomerated material
2 cBN particles
3 bonding phases
4 intermediate phase
5 carbide
6 nitride
7 carbonitrides
The fibrous core member that 8 cBN agglomerated materials are made
(bonding is made of carbide the fibrous core member that 8a cBN agglomerated material is made.)
(bonding is made of nitride the fibrous core member that 8b cBN agglomerated material is made.)
The mould component that 9 cBN agglomerated materials are made
(bonding is made of nitride the mould component that 9a cBN agglomerated material is made.)
(bonding is made of carbide the mould component that 9b cBN agglomerated material is made.)
10 have the cBN agglomerated material of monfil shape structure
The elementary cBN agglomerated material of 10 a
10b level cBN agglomerated material
11 have the cBN agglomerated material of multifilament shape structure
12 points of a knife
13 blades
14 blades
15 strut members
16 sheet structures
The compound cBN agglomerated material of 16A sheet structure
The sheet arrangement architecture is according to the parallel mode storehouse of fiber among the 16B 16A
The sheet arrangement architecture is according to the orthogonal mode storehouse of fiber among the 16C 16A
The sheet arrangement architecture is according to the mode storehouse of fiber perpendicular to the sheet surface among the 16D 16A
The living pressed compact of 17 core components
The living pressed compact of 18 mould components
19 compound living pressed compacts
20 have the compound living pressed compact of monfil shape structure
21 have the compound living pressed compact of multifilament shape structure
22 have the compound living pressed compact of plate shape
23 rollers
30 make cutting tool cBN agglomerated material
31 rakes
32 sides
40 hard coat films
I
CBNClimax during the X-ray diffraction of cBN particle is analyzed
I
NPlace, (200) plane peak intensity during the X-ray diffraction of nitride is analyzed
I
CPlace, (200) plane peak intensity during the X-ray diffraction of carbide is analyzed
d
CThe diameter of core component
d
SThe thickness of mould component
Embodiment
＜cBN agglomerated material 〉
According to the present invention, the embodiment of preferred cBN agglomerated material will attachedly describe in detail with the reference legend.
(embodiment one)
Fig. 1 (a) shows is the cBN agglomerated material structural representation of the embodiment one in according to the present invention.Shown in Fig. 1 (a), cBN agglomerated material 13 is made of with bonding mutually cBN particle 2 (Fig. 1 (a) black part).Specifically cBN agglomerated material 1 by constitute by around bonding mutually the cBN particle 2 of the 3 hard phases that combine constitute.The cBN agglomerated material also has an intermediate phase 4, its between cBN particle 2 and bonding mutually between 3 with in conjunction with cBN particle 2 with bond mutually 3.
In this embodiment bonding is mutually in 3, is selected from the periodic table of elements in the 4th, 5,6 family's elements the carbide 5 of at least a metallic element and is selected from the periodic table of elements that the nitride 6 of at least a metallic element exists simultaneously in the 4th, 5,6 family's elements.When bonding mutually 3 when being grouped into by this one-tenth, the feasible bonding force that improves the intensity of bonding phase 3 simultaneously and bond between phase and the cBN particle 2 becomes possibility, and produced the unrelieved stress that bonds between phase 3 and the cBN particle 2, also just guaranteed combining closely between the cBN particle 2.As a result, this makes that suppressing coming off of cBN particle 2 becomes possibility with the wearing and tearing that bond mutually, has also just given abrasion resistance properties, the especially You Yi chip resistance characteristic of cBN agglomerated material 1 height.The state of matter that carbide 5 and the nitride 6 simultaneous meaning of one's words are carbide 5 and nitride 6 is in bonding existence independently of one another in 3 mutually.
Under the situation that the 3 solid solution that is made of carbide and nitride (shown in Fig. 1 (the b)) carbonitrides 7 with homogeneous are formed mutually that bonds, can not improve the intensity of bonding phase 3 and the bonding force between bonding phase and the cBN particle 2 simultaneously.On the other hand, when bonding phase 3 only was made up of carbide 5, the bonding force between bonding phase and the cBN particle 2 can descend, so can cause coming off of fritted failure or cBN particle 2, the fracture when having caused like this being hit or cracked.On the other hand, when bonding phase 3 only is made up of nitride 6, can make that then wear-resistant ability significantly descends.
As later on the situation of the cBN agglomerated material 10,11 of the filamentary structure that makes referrals to, under the situation that structure is constituted by core component and mould component, by make in core component and the mould component bonding mutually one for carbide another can make the performance of core component and mould component play a role in well balanced mode for nitride, so make cBN agglomerated material 10,11 show optimum performance.
" coexistence " can be by being confirmed the proximate analysis collection of illustrative platesization in 3 mutually in bonding for carbide 5 and nitride 6, using WDS (wavelength dispersion type X-x ray spectrometer x) to carry out under EPMA (electron probe microanalysis (EPMA)) situation, for example, carbide 5 can be confirmed by the atlas analysis of carbon, nitrogen, boron and metallic element with the coexistence of nitride 6.Different districts also can confirm that they still are that nitride 6 is formed by carbide 5 by X-ray photoelectric spectral method (ESCA).In addition, the X-ray diffraction analysis that below will introduce also can be used for confirming effectively the coexistence situation of carbide and nitride.
Though, form the metallic element of carbide 5 and preferentially select identical metallic element for use, can be different metallic elements with the metallic element of forming nitride 6 in order to obtain the strong keying action of 2 on high-intensity bonding phase 3 and cBN particle.Especially preferentially select metallic element titanium (Ti) for use, bonding phase 3 can be made up of titanium carbide (TiC) and titanium nitride (TiN) like this.In this case because titanium has and cBN particle 2 between high affinity, can make the high compressive residual stress of maintenance between the cBN particle 2, the keying action between the cBN particle 2 can be strengthened like this, makes material have excellent wear-resistant and shatter-resistant ability.
In order to reach cBN particle 2 come off and bond mutually 3 wearing and tearing and the abundant inhibition that comes off the content ratio P of carbide 5 in the cBN agglomerated material 1
CWith nitride 6 content ratio P
NBetween ratio (P
C/ P
N) preferably in 0.2～3.0 scope, preferably between 0.5～2.0.When using cBN agglomerated material 1 to make cutting tool, the decline of wear-resistant ability can be controlled in the cutting operation, can stop coming off of cBN particle 2, thereby stops over worn phenomenon to take place.
Be preferably in cBN particle 2 in the cBN agglomerated material 1 around have intermediate phase 4, intermediate phase 4 contains the compound of the component that is not bonding phase 3, it is to be selected from the 4th, 5,6 family's metals in the periodic table of elements, a kind of in iron family metal and the aluminium in the carbide of at least a metallic element, nitride, carbonitride, boride, boron-carbide, boron nitride and the oxide compound.This composition makes it cBN particle 2 can be closely linked.Intermediate phase 4 compositions can be by for example TiB
2, AlN or similar substance form.
As the carbonitride that is made of carbide 5 and nitride 6 sosoloid weight percent in whole cBN agglomerated material 1 also is being preferred below 5%.This has improved the ratio of cBN particle 2 and has reduced bonding 3 ratio mutually, just can suppress coming off and the wearing and tearing of the phase 3 that bonds and coming off of cBN particle 2.The content of carbonitride can compare calculating by respective peaks intensity in measured X-x ray diffraction analysis x and with the working curve of the standard model of other preparation.
Preferred 0.2～5.0 μ m of the median size of cBN particle 2 considers that wear-resistant ability and intensity are preferably between 0.5～3.0 μ m.
It is as follows that preparation has the example of method of cBN agglomerated material of this spline structure.Prepare raw material powder at first, as follows: taking by weighing median size is the cBN material powder of 0.2～3 μ m; Taking by weighing median size is 0.2～3 μ m, and preferred 0.5～3 μ m, the powder of best 1～3 μ m carbide, its metallic element are selected from the periodic table of elements the 4th, 5,6 family's metallic elements at least a; Take by weighing that to have median size be the powder that is preferably in nitride between 1～3 μ m between 0.2～3 μ m between preferred 0.5～3 μ m, metallic element is selected from the periodic table of elements the 4th, 5,6 family's metallic elements at least a in the nitride; In addition if desired according to special composition require to take by weighing median size between 0.5～5 μ m aluminium or the powder of at least a iron family metal.These powder rolled in ball mill and grind 16～72 hours.
Then the powder moulding that rolls is become predetermined shape.Can adopt many known moulding processs, for example pressing mold, injection molding, casting or extrusion molding.
Give birth to pressed compact and place the hyperpressure agglomerating plant together, handled 10～30 minutes down for 1200～1400 ℃ in pressure 5GPa, temperature, so obtained the described cBN agglomerated material of the present embodiment with the strut member of making by sintered carbide for preparing in addition.For carbide that wherein is selected from least a metal in the periodic table of elements the 4th, 5,6 family's metallic elements and the self-existent structure of nitride that is selected from a kind of metal in the periodic table of elements the 4th, 5,6 family's metallic elements, preferred heat up and cooling rate 30～50 ℃ of per minutes and soaking time (firing time) in 10～15 minutes scopes.When firing temperature, firing constant voltage time, intensification and cooling rate and above-mentioned scope to some extent during deviation, control texture will be difficult to so that contain the carbide and the nitride of coexistence therein.
[embodiment two]
Below will introduce the embodiment two of cBN agglomerated material among the present invention.In this embodiment, with embodiment one in same or similar components will use same reference number to represent and its relevant introduction will be omitted.
Shown in Fig. 1 (a), the cBN agglomerated material in this embodiment demonstrates the diffraction peak that the carbide 5 of diffraction peak that nitride 6 produces and coexistence produces in the X-ray diffraction analysis.Specifically as shown in Figure 2, the feature of cBN agglomerated material is the diffraction peak I that has nitride 6 generations that are selected from least a metal in the periodic table of elements the 4th, 5,6 family's metallic elements in the X-ray diffraction analysis simultaneously
N(nitride peak) and be selected from the diffraction peak I that the carbide 5 of at least a metal in the periodic table of elements the 4th, 5,6 family's metallic elements produces
C(carbide peak).
Specifically, nitride 6 and carbide 5 exist simultaneously with such level in the X-ray diffraction analysis: the diffraction peak that the plane (200) of diffraction peak that the plane of nitride 6 (200) are located to produce and carbide 5 is located to produce.Make like this bonding mutually 3 and cBN particle 2 between produce unrelieved stress shown in Fig. 1 (a), make that knot and stronger and the coming off of prevention cBN particle 2 between the cBN particle 2 becomes possibility.Among the present invention peak intensity I when peak in the diffracting spectrum is too crowded can be when overlapping each other by diffraction peak is estimated with the isolating method of described collection of illustrative plates.
In this embodiment, the nitride 6 and the carbide 5 simultaneous meanings are the diffraction peak intensity I that the plane (200) of carbide 5 is located
CThe diffraction peak intensity I that locates with the plane (200) of nitride 6
NBetween ratio (I
C/ I
N) in 0.5～20 scope.
When using the X-ray diffraction analysis to measure, the diffraction peak intensity I that the plane of carbide 5 (200) are located
CThe diffraction peak intensity I that locates with the plane (200) of nitride 6
NBetween ratio (I
C/ I
N) preferably in 0.5～1.2 scope, be preferably between the 0.3-0.9.Can stop coming off of cBN particle 2 to stop the decline of abrasion resistance properties in the cutting operation with over worn generation like this.
When using X-ray diffraction mentioned above to analyze, the diffraction peak intensity I of nitride 6
NThe diffraction peak intensity I that locates to produce with the plane (111) of cBN particle 2
CBNBetween ratio (I
N/ I
CBN) also want preferred in 0.3～1 scope, can under the high rigidity situation that keeps cBN agglomerated material 1, improve cBN particle 2 and bonding coming off of the bonding force between 3 and prevention cBN particle 2 mutually like this, thereby improve cBN agglomerated material 1 shock resistance.
When using X-ray diffraction to analyze, the diffraction peak intensity I of carbide 5
CThe diffraction peak intensity I that locates to produce with the plane (111) of cBN particle 2
CBNBetween ratio (I
C/ I
CBN) also want preferred in 0.5～0.9 scope.Can ensure wear-resistant like this and the chip resistance performance.Each unimodal intensity can be by determining each peak isolating method from the X-ray diffraction analysis chart.
The diffraction peak intensity I that the plane (200) of the sosoloid carbonitride 7 that is made of carbide 5 and nitride 6 is located to produce
CNValue, i.e. the peak that occurs between the peak that the plane (200) of peak of locating to produce between the plane (200) of carbide 5 and nitride 6 is located to produce, and the above each peak intensity I
CAnd I
N, also can preferably satisfy following relation: I between each peak intensity
CN＜0.3I
CAnd I
CN＜0.3I
NBe ideal when in other words, the peak of carbonitride 7 is difficult to measure.Can stop the decline of the bonding force between the cBN particle 2 like this and guarantee to prevent coming off of cBN particle 2.
Also preferably control the diffraction peak intensity I of place, (101) plane generation of intermediate phase 4
ILThe diffraction peak intensity I that produces with place, (111) plane of cBN particle 2
CBNBetween ratio (I
IL/ I
CBN) between 0.1 and 0.8, be preferably between 0.4 and 0.7, when using X-ray diffraction to analyze.Can keep cBN particle 2 so securely and obtain cBN particle 2 guaranteeing high hardness and toughness with boning mutually the rational proportion between 3 content.
(embodiment three)
The embodiment three of the cBN agglomerated material among the present invention now is described.In this embodiment with embodiment one and embodiment two in the same or similarly component will use same reference number to represent, and its explanation will be omitted.
In the cBN agglomerated material in the present embodiment, nitride 6 and carbide 5 coexist in 3 mutually simultaneously in bonding shown in Fig. 1 (a).Be equivalent to the median size d that the median size of equivalence circle of each particle area occupied of the carbide 5 between cBN particle 2 obtains by calculating
C, measure by the cross section of observing the cBN agglomerated material; And the median size d that obtains of the median size of equivalence circle that is equivalent to each particle area occupied of the nitride 6 between cBN particle 2 by calculating
N, satisfy such proportionlity: (d
N/ d
C) between 0.4 and 1.2.Such composition can be more effective the coming off of prevention cBN particle 2, this by carbide, is impossible in bonding under nitride or the situation of carbonitride formation of sosoloid as them.The result makes like this and suppresses coming off and stoping 3 the wearing and tearing and come off and become possibility of boning mutually simultaneously of cBN particle, so given the high wear resisting property of cBN agglomerated material and greatly improved its chip resistance ability.
Median size in this embodiment is to determine like this.The position of compound such as nitride 6 and carbide 5 is determined by microscopic examination cBN agglomerated material, the average area of nitride 6 and carbide 5 determines to have the median size that just becomes nitride 6 or carbide 5 with the circular diameter of average area equal areas so by Luzex or other similar approach.Microscopic examination can be undertaken by using metaloscope, laser microscope, digital microscope, scanning electronic microscope, transmission electron microscope or other microscopes according to the selected any appropriate of the composition of cBN agglomerated material.
The median size d of cBN particle 2
CBNPreferably at 5 μ m or littler, the median size d of carbide 5
CBe preferable between 1 μ m and the 3 μ m and the median size d of nitride 6
NBe preferable between 0.5 μ m and the 2 μ m.Improved the hardness of cBN agglomerated material like this and made that the bonding force between the cBN particle 2 is more tight, so improved abrasion resistance properties.
(embodiment four)
The embodiment four of the cBN agglomerated material among the present invention now is described.In this embodiment with embodiment one to three in the same or similarly component will use same reference number to represent, and its explanation will be omitted.
In the cBN of this embodiment agglomerated material, the compressive residual stress σ that possesses between the cBN particle 2 shown in Fig. 1 (a)
CBNAt 300MPa or more, preferably 300 and 1000MPa between, 500 and 700MPa between better.Can more effectively stop coming off of cBN particle 2 like this, improve abrasion resistance properties and greatly improve the chip resistance performance.
Selecting preferably is that compressive residual stress all exists in cBN particle 2 and bonding phase 3, and the compressive residual stress σ in the cBN particle 2
CBNWith the bonding compressive residual stress σ in 3 mutually
bBetween ratio (σ
CBN/ σ
b) between 2 to 5, be more preferably between 2 to 3.Like this can the more effective intensity that comes off and improve the cBN agglomerated material that stops cBN particle 2.As ratio (σ
CBN/ σ
b) also can be improved at 2 abrasion resistance properties between 3 time.
Compressive residual stress can be by for example using X-ray residual stress measuring method (2 θ-sin of X-ray diffraction analysis (XRD) to cBN agglomerated material 1
2) determine.Contain two kinds or more kinds of material as carbide 5 and nitride 6 as bonding 3 o'clock mutually at cBN agglomerated material 1, the bonding unrelieved stress in 3 is mutually determined by considering the carbide 5 and the method for the content ratio of nitride 6.The unrelieved stress of every kind of material can be determined particularly.The content ratio of these materials can be proportional to content by the maximum peak intensity in the analysis of supposition X-ray diffraction and calculate.So the unrelieved stress of every kind of material multiply by their content ratio (ratio between the amount of this material and mutually total amount of bonding), and so the adding altogether of all material is 3 the unrelieved stress mutually that obtains boning.
The compressive residual stress σ that possesses in the bonding phase 3
bPreferably between 60 to 300MPa, be more preferably 100 and 300MPa between.Can more effectively stop coming off of cBN particle 2 like this, improve abrasion resistance properties and greatly improve the chip resistance performance.
In bonding phase 3, act on the compressive residual stress σ on the carbide 5
CWith the compressive residual stress σ that acts on the nitride 6
NBetween ratio (σ
C/ σ
N) preferably between 1.5 to 5.Can make the unrelieved stress in the cBN agglomerated material 1 be optimized and improve the wear-resistant of cBN agglomerated material 1 and chip resistance performance like this.
Be used for the compressive residual stress σ on the nitride 6
NAlso can act on the compressive residual stress σ on the carbide 5 preferably at 30～200MPa
CAlso can be preferably at 100～700MPa, ratio (σ between them
C/ σ
N) preferably in the above scope.
(embodiment 5)
The embodiment five of the cBN agglomerated material among the present invention now is described.In this embodiment with embodiment one to four in the same or similarly component will use same identifying code to represent, and its explanation will be omitted.
Fig. 3 is the schematic cross-section of cBN agglomerated material in this embodiment.As shown in Figure 3, the cBN agglomerated material A in this embodiment has been coated with a kind of cBN agglomerated material 1 that is formed at its lip-deep specific dura mater 40.In other words, cBN agglomerated material A has such composition: by cBN particle 2 with contain carbide 5 and be coated with a kind of specific dura mater of above being mentioned 40 in 3 cBN agglomerated material 1 surfaces of forming mutually with the bonding of nitride 6.
Under this composition, mutually exist carbide 5 and nitride 6 to have such effect simultaneously in 3 in bonding: compressive residual stress will be because of carbide 5 and nitride 6 between the difference of thermal expansion and contraction in cBN agglomerated material 1, exist and finish up to sintering, thereby improve the intensity of cBN agglomerated material 1.Among the cBN agglomerated material A in this embodiment, because the surface of cBN agglomerated material 1 scribbles a kind of specific dura mater 40, cBN agglomerated material 1 further is subjected to the unrelieved stress effect, makes because the synergy of the compressive residual stress of carbide 5 and nitride 6 will produce a kind of high compressive residual stress at the near interface of 1 of dura mater 40 and cBN agglomerated material.The unrelieved stress on dura mater 40 surfaces will reduce as a result, makes cBN agglomerated material A can have very high toughness.And because dura mater 40 has high hardness, abrasion resistance properties can further be improved.Also because dura mater 40 at high temperature has the superiority of hardness, resistance of oxidation and lubricity aspect, it shows excellent abrasion resistance properties and chip resistance ability under the severe condition when using cutting tool and high-abrasive material.
The example of preferred dura mater 40 comprises the unitary film that is selected from one group of film, and this group film comprises film, the Al that is made up of the compound of Ti
2O
3Film, polycrystalline diamond film, class diamond carbon (DLC) film, cubic boron nitride (cBN) film are perhaps by two layers or three layers of film that constitutes.
The dura mater 40 preferred physical vapor deposition methods (PVD) that adopt form.Make that like this improve film becomes possibility with the unrelieved stress that the bond strength and the optimization of cBN agglomerated material 1 is present in cBN agglomerated material A surface, so improved abrasion resistance properties and the chip resistance ability of cBN agglomerated material A.
The total thickness of dura mater 40 is preferable over the scope of 0.01～15 μ m, better at 0.1～10 mu m range.Improve dura mater 40 like this with the bond strength of cBN agglomerated material 1 and make it incrust, thereby when keeping abrasion resistance properties, suppressed peeling off of film.More clear and definite is that for forming dura mater, every kind of differing materials has an optimal thickness.For example, for example DLC film or cBN film preferably have the unitary film of 0.01～0.3 μ m thickness to a kind of dura mater with ultrahigh hardness.As described later the dura mater of forming by the Ti compound preferably thickness be the unitary film of 0.5～8 μ m.Can obtain suitable unrelieved stress at above-described thickness range endosclerite 40.
The compressive residual stress that exists in the dura mater 40 is preferably in 0.1～30GPa scope.Improved dura mater 40 like this with the bond strength of cBN agglomerated material 1 and optimized the unrelieved stress that is present in cBN agglomerated material A surface, so improved the intensity of cBN agglomerated material A.
The compressive residual stress of cBN agglomerated material A that scribbles dura mater 40 is more preferably in 300～1000MPa scope preferably at 200MPa or higher, is preferably in 500～1000MPa scope.Improved the bond strength of dura mater 40 like this and optimized the unrelieved stress that is present in cBN agglomerated material A surface, so improved the intensity of cBN agglomerated material A.
At least one tunic of dura mater 40 preferably adopts the compound of expressing with following general molecular formula (1).This has improved the hardness of dura mater 40 and toughness and it bond strength with cBN agglomerated material 1.
[chemical molecular formula]
[Ti
a，M
1-a][B
xC
yN
zO
1-(x+y+z)]…(1)
Here at least a periodic table of elements the 4th, 5 and 6 families metallic element, Al and the Si element except that the Ti element that be selected from of M representative.0＜a≤1,0≤x≤1,0≤y≤1 and 0≤z≤1.
And at least one tunic of dura mater 40 preferably adopts the compound of expressing with following general molecular formula (2).This make improve dura mater 40 become possibility such as characteristic aspects such as hardness and intensity, and make cBN agglomerated material A have high toughness and high hardness.
[chemical molecular formula 2]
[Ti
a，M
1-a][B
xC
yN
zO
1-(x+y+z)]…(2)
Here at least a periodic table of elements the 4th, 5 and 6 families metallic element, Al and the Si element except that the Ti element that be selected from of M representative.0.3≤a≤0.7,0≤x≤0.5,0≤y≤0.5,0.5≤z≤1 and x+y+z≤1.
During X-ray diffraction is analyzed, the diffraction peak intensity I at place, (111) plane of one deck at least of dura mater 40
(111)With the diffraction peak intensity I of place, (200) plane
(200)Ratio I
(111)/ I
(200)Preferred 0.7 or higher.Make to form like this dura mater 40 compound crystal particle diameter more I so that the hardness of dura mater 40 becomes is higher, so improve its abrasion resistance properties.When the particle of dura mater 40 more hour, the grain defect of dura mater 40 descends, dura mater 40 strengthens with the bond strength of cBN agglomerated material 1, can suppress peeling off of film like this under the condition of greatly improving chip resistance ability and heat-resistant impact ability.
In order to improve dura mater 40 with the bond strength between the cBN agglomerated material 1, a middle layer (not shown) can be provided between dura mater 40 is with cBN agglomerated material 1, the middle layer can be by a kind of metal such as titanium, perhaps be selected from nitride, carbide or the carbonitride of at least a metallic element in the 4th, 5,6 family's elements in the periodic table of elements, compositions such as boron, aluminium and silicon.
Before forming dura mater 40, the surface of cBN agglomerated material 1 can use shot peening, sandblast, electrolytic etching, chemical milling, mechanical mill, polishing, ion implantation or additive method to handle.By such surface treatment, the bond strength of dura mater 40 also can be improved.
Executing the cBN agglomerated material with filamentary structure that scheme one to five belongs to another cBN agglomerated material 1 factually and will use referenced in schematic to be described in detail, is example with embodiment one.Fig. 4 (a) has shown the schematic cross-section of other cBN agglomerated materials in the present embodiment, and Fig. 4 (b) is its skeleton view.Shown in Fig. 4 (a) and (b), cBN agglomerated material 10 has such monfil shape structure: a mould component 9 of being made by specific cBN agglomerated material is covered with the circumferential surface of the fibrous core member of being made by specific cBN agglomerated material 8.
Monfil shape structure can be made by in the following dual mode any one.First kind of cBN agglomerated material 10a has such monfil shape structure: the crust member 9a that is made by the cBN agglomerated material, this material is made of bonded bonding cBN particle 2, and bonding is formed by being selected from the periodic table of elements in the metal in the 4th, 5,6 family's elements the nitride 6 of at least a metallic element; Crust member 9a is covered with the circumferential surface of fibrous core member 8a, core component 8a is made by the cBN agglomerated material, this material is made of bonded bonding cBN particle, and bonding is made up of the carbide 5 that is selected from least a metallic element of the 4th, 5,6 family's elements in the periodic table of elements.
Second kind of cBN agglomerated material 10b has such monfil shape structure: the mould component 9b that is made by the cBN agglomerated material, this material is made of bonded bonding cBN particle 2, and bonding is formed by being selected from the periodic table of elements in the 4th, 5,6 family's elements the carbide 5 of at least a metallic element; Mould component 9b is covered with the circumferential surface of fibrous core member 8b, core component 8b is made by the cBN agglomerated material, this material is made of bonded bonding cBN particle, and bonding is made up of the nitride 6 that is selected from least a metallic element of the 4th, 5,6 family's elements in the periodic table of elements.
Even the cBN agglomerated material has aforesaid monfil shape structure, cBN agglomerated material 10 has such composition on the whole: carbide 5 and nitride 6 are present in bonding mutually in 3 simultaneously, so cBN agglomerated material 10 can obtain cBN agglomerated material 1 similar effects introduced with former.And, mutually one of them of bonding that has monfil shape structure and its core component and a mould component when the cBN agglomerated material is made up of carbide 5 and another is when being made up of nitride 6, core component 8 can play a role with the performance of mould component 9 well balancedly, so cause the cBN agglomerated material to show optimal effectiveness on the whole.As a result, the abrasion resistance properties of cBN agglomerated material and chip resistance ability all more effectively are improved.Also make and preferentially improve abrasion resistance properties by the trend of controlling fiber or the chip resistance performance becomes possibility.
Except the above monfil shape structure of introducing, cBN agglomerated material with filamentary structure also can be the cBN agglomerated material 11 with multifilament shape structure, and a plurality of cBN agglomerated materials 10 with monfil shape structure become pencil shown in Fig. 5 (a), Fig. 5 (b) in the multifilament shape structure.This composition has further improved abrasion resistance properties and chip resistance performance.
When Bao Shu has the cBN agglomerated material 10 of monfil shape structure, can be only first kind of cBN agglomerated material 10a bunchy, perhaps only second kind of cBN agglomerated material 10b bunchy, perhaps first kind of cBN agglomerated material 10a is with second kind of cBN agglomerated material 10b bunchy, and this depends on application.
In order to improve chip resistance performance, the such situation of gravel size decision of the cBN agglomerated material 10,11 of filamentary structure: the median size d of core component 8 shown in Fig. 4 (a) with the cutting tool of its preparation
CIn 10～200 mu m ranges, the thickness d of mould component 9
SIn 1～20 mu m range.The median size d of core component 8
CThickness d with mould component 9
SCan determine by the cross-sectional area of observing cBN agglomerated material 10,11 under or the metaloscope following with filamentary structure in scanning electronic microscope (SEM).
Except the fascircular texture shown in Fig. 5 (a), Fig. 5 (b), the structure that multifilament shape structure also can be shown in Fig. 6 (a) to (d).Fig. 6 (a) has shown a kind of cBN agglomerated material 16A, and the cBN agglomerated material 10 (or 11) with filamentary structure is wherein arranged with the lamella structure; Fig. 6 (b) has shown cBN agglomerated material 16B, and wherein a plurality of sheet cBN agglomerated material 16A are with same direction storehouse; Fig. 6 (c) has shown cBN agglomerated material 16C, and wherein a plurality of sheet cBN agglomerated material 16A are with different direction storehouses; Fig. 6 (d) has shown cBN agglomerated material 16D, and the cBN agglomerated material 10 (or 11) that wherein has filamentary structure is arranged along the direction perpendicular to the sheet surface.As the cBN agglomerated material 10 (or 11) with filamentary structure at random the structure the lack of alignment also can adopt.
The embodiment 2 that the front is introduced is such situations: the cBN agglomerated material 1 that its bonding contains mutually carbide 5 and nitride 6 in 3 simultaneously shows the diffraction peak that demonstrates nitride 6 simultaneously and the diffraction peak of carbide 5 in the X-ray diffraction analysis.But the present invention is not limited thereto, and the cBN agglomerated material 10,11 with monfil shape structure also can demonstrate the diffraction peak of nitride 6 and the diffraction peak of carbide 5 simultaneously in the X-ray diffraction analysis.
Under the situation that the cBN agglomerated material of the cutting tool 30 that will introduce after being used for preparing is made by the cBN agglomerated material of embodiment two, especially, when using X-ray diffraction to analyze the cross section of fibrous texture of the cBN agglomerated material 10,11 with fibrous texture noted earlier, the diffraction peak intensity I that the plane of carbide 5 (200) are located
CThe diffraction peak intensity I that locates with the plane (200) of nitride 6
NBetween ratio (I
C/ I
N) also be controlled in 0.2～1.2 the scope, be preferably between the 0.3-0.9.Under not making the condition that abrasion resistance properties descends in the cutting operation, stoped coming off and over worn generation of cBN particle 2 like this.To the ratio I in the embodiment two
N/ I
CBN, ratio I
C/ I
CBN, peak intensity I
CN, peak intensity I
CWith peak intensity I
NAlso satisfy the above condition.
Embodiment three is handled is to contain ratio (d in the cBN agglomerated material 1 of simultaneous carbide 5 and nitride 6 mutually in 3 in its bonding
N/ d
C) have a situation of preset value.But the present invention is not confined to this, preferably in cBN agglomerated material 10,11 with monfil shape structure, and ratio (d
N/ d
C) also have a preset value.
Under the situation that the cBN agglomerated material of the cutting tool 30 that will introduce after being used for preparing is made by the cBN agglomerated material of embodiment three, when the cBN agglomerated material is taken as an integral body and treats, cBN agglomerated material with filamentary structure also has the bonding mutually 3 that contains simultaneous carbide 5 and nitride 6, and nitride 6 and the median size d of carbide 5 with nitride 6
NMedian size d with carbide 5
CRatio (d
N/ d
C) between 0.4～1.2 scope feature.The median size d of cBN particle 2
CBNAlso preferred 5 μ m or littler, the median size d of carbide 5
CAlso preferably between 1～3 μ m, the median size d of nitride 6
NAlso preferably between 0.5～2 μ m.Can stop coming off of cBN particle 2 like this, this is impossible using traditional bonding phase time.The result make to stop coming off of cBN particle and stops the wearing and tearing that bond mutually simultaneously and come off becomes possibility, then given the cBN agglomerated material high abrasion resistance properties, You Yi chip resistance performance especially.
In cBN agglomerated material 10,11, also want preferred 300MPa or the higher compressive residual stress σ of in cBN particle 2, keeping with filamentary structure
CBNCan suppress coming off of cBN particle 2 like this.To the situation of cBN agglomerated material 10,11, the compressive residual stress σ of cBN particle 2 with filamentary structure
CBNAnd the compressive residual stress σ of bonding phase 3
bAll tend to be higher than foregoing traditional situation with homogeneous ceramic structure.
The situation of dura mater 40 that has been its bonding surface coverage of containing simultaneous carbide 5 and the cBN agglomerated material 1 of nitride 6 mutually in 3 that embodiment five is handled.But the present invention is not confined to this, and dura mater 40 also can cover on the surface of mould component 9 of the cBN agglomerated material 10,11 with monfil shape or multifilament shape structure.
Referenced in schematic be will be aided with below and the example of method that a preparation has the cBN agglomerated material of filamentary structure, i.e. another cBN agglomerated material in the present embodiment introduced in detail.Fig. 7 (a) and Fig. 7 (b) show the synoptic diagram of the method for preparing the compound living pressed compact of being made by the cBN agglomerated material with monfil shape structure.
At first, the wherein a kind of conduct bonding phase component in only adding carbide and nitride, the starting material of core component prepare through crushing and mixing material by the preparation method's of the similar cBN agglomerated material of introducing previously technology.Then organic binder bond is added in the starting material of core component and mix.Mixture by pressing mold, be squeezed into mould, casting or similarly method form a cylindrical shape, make the living pressed compact of a core component 17 then, shown in Fig. 7 (a).
For organic binder bond, can use for example paraffin, polystyrene, polyethylene, ethylene-ethyl acrylate, vinyl-vinyl acetic ester, poly-n-butyl methacrylate, polyoxyethylene glycol or dibutyl phthalate.
Next, the starting material of mould component are by being prepared with the similar method technology of introducing previously, combine the phase component except adding with a kind of conduct in the two of the different carbide and nitride of core component use.So above-mentioned tackiness agent adds in the starting material that prepare mould component and mixes.Use the method for introducing previously, shown in Fig. 7 (a), the living pressed compact of the mould component 18 of two semi-cylindrical form forms from mixture.The living pressed compact of mould component 18 places the living pressed compact of core component 17 on every side to surround its circumference, so prepare compound living pressed compact 19.
Shown in Fig. 7 (b), compound living pressed compact 19 is prepared from by the method for extrusion molding (co-extrusion modling method) simultaneously.It is the living pressed compact extrusion molding at the same time of the living pressed compact and the mould component 18 of core component 17.This preparation technology makes compound living pressed compact 20 with monfil shape structure stretch with minor diameter, and wherein the living pressed compact of mould component 18 places on the living pressed compact of core component 17 to cover its periphery.
Living pressed compact 21 with multifilament shape structure can be by a plurality of 20 bag Shu Ercheng of the compound living pressed compacts with monfil shape structure that use extrusion molding simultaneously to form, again to the method for this Shu Caiyong extrusion molding simultaneously.Make in this way, can make further raising give birth to that the bond strength between matrix material becomes possibility in the pressed compact 20.
At the same time in the extruding shaping technique, the cross section of the fibrous living pressed compact that forms as front institute introduction method can be made required as shapes such as circle, trilateral, rectangle and sexangles by changing extrusion mould.
In order to prepare the composite structure that is formed by the matrix material of arranging with schistose structure as shown in Figure 6, Zhi Bei compound living pressed compact 20 is arranged according to the mode that forms the living pressed compact 22 of sheet as previously described.The compound living pressed compact 20 that sheet is given birth in the pressed compact 22 can be arranged with the mode storehouse that is parallel to each other or to be crossed as 90 ° or 45 degree mode mutually.In this case, as required, sheet is given birth to pressed compact 22 and also can be used cold isotactic compaction (CIP) or similar method to compress together with the jointing material tackiness agent as previously described between the compound living pressed compact 20.Perhaps, the living pressed compact 22 of sheet also can carry out roll forming by using a pair of roller 23 (as shown in Figure 9).Sheet is given birth to pressed compact 22 and also can be adopted for example forming method preparation of known fast prototype method when using matrix material (cBN agglomerated material 16A to 16D as shown in Figure 6).Giving birth to pressed compact 21 also can be used for replacing compound living pressed compact 20 to use.
So as the living pressed compact 20 to 22 of previous methods preparation at vacuum tightness 2Pa or more under 600～1000 ℃ of high temperature, handle under the low pressure and carried out degreasing thermal treatment in 1～72 hour.The living pressed compact of handling like this places ultra-high voltage firing device together with the other ready strut member of being made by sintered carbide, the cBN agglomerated material that calcining obtains to have filamentary structure under the described in front condition.
Calcining also can be burnt the state that is combined into one to its strut member made from sintered carbide to the living pressed compact of skimming treatment by placing the ultra-high pressure sintering device to carry out together with the other ready strut member of being made by sintered carbide.Sintered compact uses diamond disc sharpener, electropolishing, brush or similar method to mill or is polished to pre-determined thickness.
When cutting tool used the cBN agglomerated material to prepare, high strength and sharp blade can form the edge of processing of C face or R face processing accomplishing cBN agglomerated material by using a kind of elasticity grinding stone, brush or other analogues.
＜cutting tool 〉
Be aided with referenced in schematic, now introduce the cutting tool of the cBN agglomerated material preparation of using among the present invention in each embodiment of front.Figure 10 is the skeleton view that shows a kind of embodiment of cutting tool among the present invention.As shown in figure 10, point of a knife 12 has such structure: the cBN agglomerated material used of preparation cutting tool is whittled into predetermined shape, is welded on the tip bearing (tip mounting seat) on 13 1 jiaos on the blade by strut member 15.The cBN agglomerated material that is used for cutting tool 30 has along the cut edge 14 of end face and the formation of joint, side.
Figure 11 is the schematic cross-section of structure that shows the angle of point of a knife 12, and point of a knife 12 has adopted the cBN agglomerated material with dimension shape structure as previously described.Figure 11 (a) is the schematic cross-section of an example and Figure 11 (b) is the schematic cross-section of another one example.In the point of a knife 12 shown in Figure 11 (a), the cBN agglomerated material that is used for cutting tool 30 is made up of sheet cBN agglomerated material 16C, and the cBN agglomerated material 10 (or 11) that wherein has filamentary structure is placed in such a manner: the trend of fiber and rake 31 (cross section of fiber aims at side 32) parallel to each other.
In the point of a knife 12 shown in Figure 11 (b), the cBN agglomerated material of preparation cutting tool 30 is made up of cBN agglomerated material 16D, and the cBN agglomerated material 10 (or 11) that wherein has filamentary structure is placed in such a manner: the trend of fiber and side 32 (cross section of fiber aims at rake 31) parallel to each other.
Except structure above-mentioned, such structure is also arranged, fiber and rake 31 with cBN agglomerated material 10 (or 11) of filamentary structure move towards to place at a predetermined angle, and the fiber 10 (or 11) that perhaps has the cBN agglomerated material of filamentary structure is placed according to random fashion.In all these structures, it is ideal that being configured in shown in Figure 11 (b) improved chip resistance performance aspect.Except having the cBN agglomerated material 10 (or 11) of filamentary structure, point of a knife 12 also can advantageously be made by simple cBN agglomerated material 1 as mentioned previously.
The cBN agglomerated material shows excellent abrasion resistance properties and chip resistance ability, can be preferably used as the instrument such as the drill bit of excavator and the structured material for preparing the anti-abrasive material of punching block or slide plate composition that require to have wear-resistant and chip resistance ability.The cBN agglomerated material can be used to prepare the cutting tool with long life, in the metal cutting operation, use along the cutting edge of side and the formation of rake joint crestal line and show outstanding performance, cutting tool is pressing the workpiece that will cut, especially for example metals such as iron, aluminium or refractory alloy.The cBN agglomerated material is showing excellent cutting ability aspect the processing of metal that is difficult to cut such as hardened steel.
When being used for cutting tool, cutting tool preferably has such structure: comprise blade and be welded in point of a knife on the bearing of blade, here, point of a knife is made by the cBN agglomerated material in this embodiment.In this case, though the unrelieved stress of holding in the cBN agglomerated material is tended to discharge in the welding point of a knife, the unrelieved stress in the cBN agglomerated material of point of a knife is controlled in the suitable scope so that obtain high wear-resistant ability and high chip resistance ability.
Will the present invention is described in detail in the mode of example, but it will be appreciated that the present invention only only limits to following listed embodiment.
[routine I]
CBN material powder with median size 2 μ m, TiC material powder with median size 1 μ m, TiN material powder with median size 1 μ m, TiCN material powder with median size 1 μ m, HfC material powder with median size 1 μ m has the NbC material powder of median size 1 μ m, has the metallic aluminium powder of median size 1.2 μ m and the metal cobalt powder with median size 0.8 μ m, according to the preparation of table 1 ratio, mix 16 hours in the grinding in ball grinder of using alumina balls.
Mixed powder is pressed into mould under pressure 98Mpa then.This living pressed compact is calcined under the condition as shown in table 1 in hyperpressure, high temperature service, promptly according to keeping 5.0Gp pressure certain hour under the calcining temperature shown in heat-up rate, the table 1 shown in the table 1, then just according to table 1 cooling rate cooling, so obtain cBN agglomerated material (shown in the table 1 among the No.I-1 to No.I-10 sample).
(content)
The cBN agglomerated material sample that top technology obtains carries out grinding and buffing and reaches the minute surface modification, under metaloscope its structure is observed then.Show as the cBN agglomerated material of black, the carbide sharp outline that shows as the nitride of brown and show as white, and use WDS (wavelength scatter-type X-ray photometer) also to be distinguished by EPMA (electron probe microanalysis (EPMA)) intermediate phase and carbonitride.20 or the more area use image analysis measurement of multiparticle of every kind of compound, the mean value of area is used for representing the content of cBN particle, carbide, nitride, intermediate phase and carbonitride.The result is as shown in table 1.The existence of carbonitride is determined by the peak of observing in the X-ray diffraction analysis.When observing corresponding peak, the sort of components contents ratio by with standard model relatively come to determine (the living pressed compact that is prepared from by the mixture of cBN particle and carbonitride powder constituent).
Table 1
| Sample number into spectrum 1) | Ratio (% volume) | Calcination condition | Content ratio in the agglomerated material 2) | ||||||||||||
| cBN | Carbide | Nitride | Metal | Other | Heat-up rate (℃/minute) | Calcining temperature (℃) | Calcination time (branch) | Cooling rate (℃/minute) | cBN | Carbide | Nitride | Intermediate phase | Carbonitride | P C/P N | |
| I-1 | All the other | TiC：15 | TiN：25 | Al：10 | - | 50 | 1400 | 15 | 50 | 47 | 13 | 22 | 16 | 2 | 0.6 |
| I-2 | All the other | TiC：10 WC：5 | TiN：15 | Al：5 Co：3 | - | 50 | 1400 | 15 | 50 | 58 | 15 | 13 | 13 | 1 | 1.2 |
| I-3 | All the other | HfC：20 | TiN：10 | Al：10 | - | 50 | 1400 | 15 | 50 | 56 | 16 | 7 | 21 | - | 2.3 |
| I-4 | All the other | TiC：3 | TiN：8 | Al：10 Co：5 | - | 50 | 1400 | 15 | 50 | 78 | 3 | 7 | 12 | - | 0.4 |
| *I-5 | All the other | TiC：45 | - | Al：15 | - | 50 | 1400 | 15 | 50 | 42 | 43 | - | 15 | - | - |
| *I-6 | All the other | - | TiN：35 | Al：15 | - | 50 | 1400 | 15 | 50 | 50 | - | 32 | 18 | - | - |
| *I-7 | All the other | - | - | Al：8 | TiCN：37 | 50 | 1400 | 15 | 50 | 54 | - | - | 11 | 35 | - |
| *I-8 | All the other | TiC：21 NbC：10 | TiN：3 | Al：3 Co：3 | - | 50 | 1400 | 15 | 50 | 58 | 30 | - | 4 | 8 | - |
| *I-9 | All the other | TiC：25 | TiN：15 | Al：15 | - | 50 | 1500 | 15 | 50 | 53 | 8 | - | 10 | 27 | - |
| *I-10 | All the other | TiC：15 | TiN：15 | Al：10 | - | 50 | 1400 | 30 | 20 | 67 | - | - | 8 | 25 | - |
1) indicates
*Sample outside the scope of the invention.
2) content ratio: cBN particle, carbide, nitride are observed (% area) under metaloscope.The content of carbonitride calculates by the XRD peak and gets.
CBN agglomerated material sample uses wired discharge cutting method or similar method to cut into predetermined size, each is welded on the bearing of cemented carbide substrate, so made the disposal type cutting tool that has as the structure of defined among the JISCNGA120408, this cutting tool is accepted cutting test continuously or is interrupted under the following stated condition cutting test.The result is as shown in table 2.
(cutting test continuously)
Cutting mode: rotation
The case-hardened steel (HRC58-62) of workpiece: SCM415H with 70mm diameter circle post shapes
Cutting speed: 200m/min.
Infeed: 0.2mm
Delivery rate: 0.2mm/rev.
Cutting time: 25 minutes
Measure: terminal abrasion loss
(being interrupted the cutting test)
Cutting mode: rotation
The case-hardened steel (HRC58-62) of workpiece: SCM415H with the lotus rhizome shape in 8 holes
Cutting speed: 150m/min.
Infeed: 0.2mm
Delivery rate: 0.2mm/rev.
Measure: the impact number of times (upper limit 40000) before cracked
Table 2
| Sample number into spectrum 1) | Cutting test continuously | Be interrupted the cutting test |
| Abrasion loss (mm) | Impact number of times | |
| I-1 | 0.12 | 40000 |
| I-2 | 0.14 | 36000 |
| I-3 | 0.18 | 35000 |
| I-4 | 0.16 | 32000 |
| *I-5 | 0.25 | 10000 |
| *I-6 | 0.24 | 16000 |
| *I-7 | 0.20 | 13000 |
| *I-8 | 0.16 | 8000 |
| *I-9 | 0.18 | 13500 |
| *I-10 | 0.19 | 12000 |
1) indicates
*Sample outside research range of the present invention.
Table 1 and table 2 result show that the sample No.I-5,8 and 9 etc. of its cBN agglomerated material carbide-containing (TiC) has unfavorable chip resistance ability, because the interparticle cohesive action of cBN is insufficient.The sample No.I-6 of a nitrogenate (TiN) has unfavorable abrasion resistance properties in the cBN agglomerated material, shows as to have short work-ing life.The No.I-7 and 10 that bonding only is made up of carbonitride (TiCN) is mutually performing poor aspect wear-resistant and the chip resistance ability.
By cBN agglomerated material (No.I-1 to 4), the cutting tool of making on the contrary, all shows enough wear-resistant abilities among the present invention, has 0.20mm or abrasion loss still less in the case-hardened steel that cutting is difficult to cut continuously.In being interrupted the cutting test, these samples can both stand 30000 or more times impact before cracked.Especially, sample No.I-1 to 4 shows the cracked ability of excellent in resistance, does not still have crackedly after impacting for 40000 times, shows stable cutting ability in the time that prolongs.
[routine II]
The living pressed compact of core component has mixed the cBN of 45% volume, the TiN of 42% volume and the Al of 15% volume and the material extrusion molding that the adding organic binder bond prepares by handle and has been prepared from.The living pressed compact of skin members is by the Al of the TiC of the cBN, 35% volume that have mixed 55% volume and 10% volume and add a kind of material extrusion process that a kind of organic binder bond prepares and be prepared from.
As described above, core component and mould component the extrusion molding as shown in Figure 7 of living pressed compact, so be prepared into a compound living pressed compact.Mode as shown in Figure 8, this compound living pressed compact are bundled together and have made the compound living pressed compact with stringy texture.This compound living pressed compact with stringy texture further is arranged in schistose structure, and a plurality of layer stacks get up and compress then.The storehouse thing is calcined in a ultra-high voltage, high temperature service, 50 ℃ of per minutes of heat-up rate, keeps 15 minutes down for 1400 ℃ in pressure 5.0GPa and temperature, then with 50 ℃ of per minute speed coolings, so obtained compound cBN agglomerated material.
The compound cBN agglomerated material sample that top technology obtains carries out grinding and buffing and reaches the minute surface modification, under metaloscope its structure is observed then.Show as the cBN particle of black, carbide (TiC) sharp outline that shows as the nitride (TiN) of brown and show as white, and also sharp outline of carbonitride (TiCN).Use the ratio of the various component area occupied that image analysis measures to be: cBN is 50%, TiC is 10%, TiN be 25% and TiCN be 2%.
CBN agglomerated material sample uses wired discharge cutting process to cut into predetermined size, each is welded on the bearing on the cemented carbide substrate, so made the disposal type cutting tool that has as the configuration of defined among the JIS CNGA120408, this cutting tool accepts to be similar to the cutting test in the example 1.These samples cutting after 20 minutes its abrasion loss little of 0.15mm, do not show after in being interrupted the cutting test, having accepted to impact for 40000 times cracked, so show excellent cutting ability.
[routine III]
CBN material powder with median size 2 μ m, TiC material powder with median size 1 μ m, TiN material powder with median size 1 μ m, TiCN material powder with median size 1 μ m, HfC material powder with median size 1 μ m, TaC material powder with median size 1 μ m, have the metallic aluminium powder of median size 1.2 μ m and metal cobalt powder with median size 0.8 μ m, prepare according to table 3 ratio, in the ball mill that uses alumina balls, mix 16 hours, mixed powder compression moulding under pressure 98MPa.
Give birth to pressed compact and in a ultra-high voltage, pyritous device, calcine, just adopt calcination condition in the table 3 rather than the calcination condition in the table 1, so obtain cBN agglomerated material (sample No.III-1 to 10 as shown in table 3) according to the method that is similar to routine I.
Table 3
| Sample number into spectrum 1) | Ratio (% volume) | Calcination condition | |||||||
| cBN | Carbide | Nitride | Metal | Other | Heat-up rate (℃/minute) | Calcining temperature (℃) | Calcination time (branch) | Cooling rate (℃/minute) | |
| III-1 | All the other | TiC：20 | TiN：30 | Al：10 | - | 50 | 1400 | 15 | 50 |
| III-2 | All the other | TiC：13 WC：5 | TiN：16 | Al：5 Co：3 | - | 30 | 1300 | 30 | 45 |
| III-3 | All the other | HfC：20 | TiN：15 | Al：10 | - | 40 | 1400 | 20 | 30 |
| III-4 | All the other | TaC：3 | TiN：14 | Al：10 Ni：5 | - | 50 | 1250 | 25 | 50 |
| *III-5 | All the other | TiC：40 | - | Al：15 | - | 50 | 1400 | 10 | 100 |
| *III-6 | All the other | - | TiN：40 | Al：15 | - | 50 | 1400 | 10 | 100 |
| *III-7 | All the other | - | - | Al：8 | TiCN： 37 | 50 | 1400 | 10 | 100 |
| *III-8 | All the other | TiC：15 | TiN：15 | Al：15 | - | 50 | 1500 | 15 | 50 |
| *III-9 | All the other | TiC：20 | TiN：10 | Al：15 | - | 50 | 1400 | 30 | 20 |
| *III-10 | All the other | TiC：10 | TiN：25 | Al：8 | - | 100 | 1600 | 10 | 100 |
1) indicates
*Sample outside the scope of the invention.
(X-ray diffraction peak intensity)
CBN agglomerated material sample is with angle 2 θ=30 ° to 50 ° use Cu-K
αLine source (K
α 2Line is eliminated) carry out X-ray diffraction analysis (XRD), in diffracting diagram, determine the peak of carbide and nitride, calculate the intensity rate at the peak of carbide and nitride.The result is as shown in table 4.
(cutting test)
Similar with routine I, the disposal type cutting tool of the structure of stipulating among use cBN agglomerated material specimen preparation such as the JIS CNGA120408.Carry out successive cutting test and be interrupted the cutting test with routine I is similar, the upper limit of only being interrupted the impact number of times that stands before cracked in the cutting test is set at 60000, rather than 40000.
Table 4
| Sample number into spectrum 1) | The XRD analysis peak intensity 2) | Intermediate phase | Cut test wear amount (mm) continuously | Be interrupted the cutting test and impact number of times | ||||||
| cBN I cBN | Nitride I N | Carbide I C | Carbonitride I CN | I C /I N | I N /I cBN | I C/I cBN | ||||
| III-1 | 100 | 85 | 35 | 2 | 0.41 | 0.85 | 0.35 | TiB 2.AlN | 0.13 | 45000 |
| III-2 | 100 | 62 | 50 | 12 | 0.81 | 0.62 | 0.50 | TiB 2.WCoB | 0.14 | 39000 |
| III-3 | 100 | 57 | 60 | - | 1.05 | 0.57 | 0.60 | Do not exist | 0.18 | 38000 |
| III-4 | 100 | 88 | 20 | - | 0.23 | 0.88 | 0.20 | AlN | 0.16 | 33000 |
| *III-5 | 100 | - | 68 | - | - | - | 0.68 | TiB 2.AlN | 0.25 | 12000 |
| *III-6 | 100 | 70 | - | - | - | 0.70 | - | Do not exist | 0.24 | 16000 |
| *III-7 | 100 | - | - | 52 | - | - | - | Do not exist | 0.20 | 14000 |
| *III-8 | 100 | - | - | 45 | - | - | - | AlN.TiB 2 | 0.21 | 12000 |
| *III-9 | 100 | 2 | - | 40 | - | 0.02 | - | AlN | 0.20 | 8000 |
| *III-10 | 100 | - | 5 | 35 | - | - | 0.05 | AlN.TiB 2 | 0.26 | 15000 |
1) indicates
*Sample outside the scope of the invention.
2) "-" mark in cBN, nitride, carbide and carbonitride row represents that the peak can't measure.
So the result shows among the sample No.III-5 that the peak that has only carbide is observed because insufficient keying action chip resistance scarce capacity between the cBN particle in table 3 and the table 4.Have only among the sample No.III-6 that the peak of nitride is observed deficiency aspect wear-resistant ability, cause short cutting tool work-ing life.The sample No.III-7 that uses the TiCN powder to do the bonding phase is transformed into the sample No.III-8 of TiCN phase not enough aspect wear-resistant and the chip resistance ability mutually with make bonding by the calcining effect.Bonding by TiCN mutually and the sample No.III-9 of TiC phase composite with bond by the sample No.III-10 of TiCN phase and TiN phase composite in deficiency all aspect wear-resistant and the chip resistance ability.
Sample No.III-1 to 4 is by the blade of the cBN agglomerated material preparation at the XRD peak of XRD peak that demonstrates TiC and TiN, shows sufficient wear-resistant ability, and abrasion loss is no more than 0.20mm in to the continuous cutting test of the case-hardened steel that is difficult to cut.Especially, these blades cut in the test in interruption and reveal excellent chip resistance ability by tolerance 30000 times or more times collimeter before cracked, demonstrate interior for a long time stable cutting ability.
[routine IV]
Living pressed compact with the similar preparation core component of routine II.Then with the living pressed compact of the similar preparation mould component of routine II, only with the content of TiC from 35% stereomutation to 30% volume.Be used for preparing compound living pressed compact with the living pressed compact of the similar core component of routine II and the living pressed compact of mould component, calcine compound living pressed compact with preparation cBN agglomerated material with multifibres structure.
On compound cBN agglomerated material cross section, carry out X-ray diffraction analysis (XRD), the peak of the nitride of the peak of the carbide of mould component and core component in the affirmation diffracting diagram.The peak intensity I of carbide
CPeak intensity I with nitride
NRatio (I
C/ I
N) be 0.42.The observation of microcosmic and compositional analysis show the existence of TiN in core component and the existence of TiC in mould component.
CBN agglomerated material sample uses wired discharge cutting process to cut into predetermined size, each is welded on the bearing on the cemented carbide substrate, so made the disposal type cutting tool that has as the structure of defined among the JIS CNGA120408, this cutting tool accepts to be similar to the cutting test among the routine I.These samples cutting after 20 minutes its abrasion loss little of 0.15mm, do not show after in being interrupted the cutting test, having accepted to impact for 60000 times cracked, so show excellent cutting ability.
[routine V]
CBN material powder with median size 2.5 μ m, TiC material powder with median size 1.5 μ m, TiN material powder with median size 1.2 μ m, TiCN material powder with median size 1 μ m, NbC material powder with median size 1 μ m, TaC material powder with median size 1.1 μ m, NbN material powder with median size 0.9 μ m, have the metallic aluminium powder of median size 1.2 μ m and metal cobalt powder with median size 0.8 μ m, according to the preparation of table 5 ratio, in the ball mill that uses alumina balls, mix 16 hours.
Mixed powder compression moulding under pressure 98MPa.Give birth to pressed compact and in a ultra-high voltage, pyritous device, calcine, just adopt calcination condition in the table 5 rather than the calcination condition in the table 1, so obtain cBN agglomerated material (sample No.V-1 to 10 as shown in table 5) according to the method that is similar to routine I.
Table 5
| Sample number into spectrum 1) | Ratio (% volume) | Calcination condition | Remarks | |||||||
| cBN | Carbide | Nitride | Metal | Other | Heat-up rate (℃/minute) | Calcining temperature (℃) | Calcination time (branch) | Cooling rate (℃/minute) | ||
| V-1 | All the other | TiC：25 | TiN：25 | Al：12 | - | 50 | 1400 | 15 | 50 | The blade of welding |
| V-2 | All the other | TiC：12 WC：8 | TiN：15 | Al：6 Co：4 | - | 30 | 1300 | 30 | 45 | The blade of welding |
| V-3 | All the other | NbC：15 | NbN：20 | Al：10 | - | 40 | 1400 | 20 | 30 | The blade of welding |
| V-4 | All the other | TaC：10 | TiN：12 | Al：15 Ni：3 | - | 50 | 1250 | 25 | 50 | The blade of welding |
| *V-5 | All the other | TiC：36 | - | Al：14 | - | 50 | 1400 | 10 | 100 | The blade of welding |
| *V-6 | All the other | - | TiN：40 | Al：10 | - | 50 | 1400 | 10 | 100 | The blade of welding |
| *V-7 | All the other | - | - | Al：7 | TiCN：28 | 50 | 1400 | 10 | 100 | The blade of welding |
| *V-8 | All the other | TiC：15 | TiN：15 | Al：10 | - | 50 | 1500 | 15 | 50 | The blade of welding |
| *V-9 | All the other | TiC：20 | TiN：10 | Al：15 | - | 50 | 1400 | 30 | 20 | The blade of welding |
| *V-10 | All the other | TiC：10 | TiN：20 | Al：8 | - | 100 | 1600 | 10 | 100 | The blade of welding |
1) indicates
*Sample outside the scope of the invention.
(X-ray diffraction peak intensity)
Similar with routine III, sample carries out the X-ray diffraction analysis, determines the peak of carbide, nitride and other components in diffracting diagram, calculates the intensity rate at peak as shown in table 6.
(median size)
Use the microtexture of metallography microscope sem observation different colours, and inspect middle mutually nitride of bonding and carbide existence.Median size d
N, d
CAnd d
CBNUse the Luzex image analyzer to measure.d
N, d
CAnd d
CBNValue by use each in mutually 50 of showing in the microtexture photo or more the more number particle determine.
In a certain haplopia open country under the situation of 50 of a certain less thaies mutually, the population of this phase in other visuals field is taken into account.To 50 of every phase or more a series of measurements of the particle of more number on every three or more points, carry out, average as d then
N, d
CAnd d
CBNValue.Measuring result is summarized in the table 6.
(cutting test)
Similar with routine I, the disposal type cutting tool of the configuration of stipulating among use cBN agglomerated material specimen preparation such as the JIS CNGA120408.Carry out successive cutting test and be interrupted the cutting test with routine I is similar, the ultimate value of only being interrupted the impact number of times that cutting stands before cracked in testing is set to 60000 to replace 40000.The result is as shown in table 6.
Table 6
| Sample number into spectrum 1) | d cBN (μm) | d C (μm) | d N (μm) | d N/d C | The XRD analysis peak intensity | Intermediate phase | Cut test wear amount (mm) continuously | Be interrupted the cutting test and impact number of times | ||||||
| cBN I cBN | Nitride I N | Carbide I C | Carbonitride I CN | I C /I N | I N /I cBN | I C /I cBN | ||||||||
| V-1 | 2.2 | 1.2 | 0.7 | 0.6 | 100 | 70 | 40 | 2 | 0.57 | 0.70 | 0.40 | TiB 2.AlN | 0.15 | 43200 |
| V-2 | 0.8 | 1.0 | 0.4 | 0.4 | 100 | 60 | 45 | 12 | 0.75 | 0.60 | 0.45 | TiB 2.WCoB | 0.14 | 38400 |
| V-3 | 2.8 | 1.5 | 1.8 | 1.2 | 100 | 40 | 28 | - | 0.70 | 0.40 | 0.28 | Do not exist | 0.18 | 31200 |
| V-4 | 3.8 | 3.2 | 2.4 | 0.8 | 100 | 64 | 20 | - | 0.31 | 0.64 | 0.20 | AlN | 0.20 | 36400 |
| *V-5 | 3.8 | 2.4 | - | - | 100 | - | 68 | - | - | - | 0.68 | TiB 2.AlN | 0.24 | 11600 |
| *V-6 | 1.2 | - | 0.8 | - | 100 | 70 | - | - | - | 0.70 | - | Do not exist | 0.28 | 18000 |
| *V-7 | 1.8 | - | - | - | 100 | - | - | 52 | - | - | - | Do not exist | 0.20 | 14000 |
| *V-8 | 2.0 | - | - | - | 100 | - | - | 45 | - | - | - | AlN.TiB 2 | 0.21 | 12000 |
| *V-9 | 2.0 | 1.5 | - | - | 100 | 2 | - | 40 | - | 0.02 | - | AlN | 0.20 | 8800 |
| *V-10 | 2.0 | - | 2.0 | - | 100 | - | 5 | 35 | - | - | 0.05 | AlN.TiB 2 | 0.26 | 15600 |
1) indicates
*Sample outside the scope of the invention.
The result shows among the sample No.V-5 to 10 that the interparticle keying action of cBN is all not enough, so the chip resistance scarce capacity causes the cutting tool work-ing life of lacking because bonding does not have the coexistence of carbide and nitride in mutually in table 5 and the table 6.
It exists carbide and nitride in boning mutually simultaneously, and the median size d of nitride
NMedian size d with carbide
CBetween ratio d
N/ d
CSample No.V-1 to 4 between 0.4～1.2, on the contrary, all have enough wear-resistant abilities, when cutting the case-hardened steel that is difficult to cut continuously, abrasion loss is no more than 0.20mm, and show excellent chip resistance ability, and especially in being interrupted the cutting test, before cracked, have 30000 times or more times impact, show stable cutting ability in the time period of prolongation.
[routine VI]
The living pressed compact of core component is by the Al of the TiN of the cBN, 39% volume that have mixed 47% volume and 14% volume and add a kind of powder body material extrusion process that a kind of organic binder bond prepares and be prepared from.The living pressed compact of mould component is by the Al of the TiC of the cBN, 30% volume that have mixed 60% volume and 10% volume and add the material extrusion process that a kind of organic binder bond prepares and be prepared from.
The living pressed compact of the core component of preparation as described above and mould component living pressed compact be used for preparing the compound living pressed compact that has with the similar multifibres structure of routine II, compound cBN agglomerated material is made in calcining then.
The median size d that the nitride in the cBN agglomerated material (TiN) and the image analysis of carbide (TiC) is shown carbide by microscopic examination
C=1.2 μ m, the median size d of nitride
N=0.7 μ m, their ratio d
N/ d
C=0.6.The X-ray diffraction analysis revealed of the core component of cBN agglomerated material preparation and mould component is existed the peak of carbide and nitride, the peak intensity I of carbide in the X-ray diffraction chart
CPeak intensity I with nitride
NBetween ratio I
C/ I
NBe defined as 0.42.
Agglomerated material uses wired discharge cutting process to cut into predetermined size, each is welded on the bearing of cemented carbide substrate, so made the disposal type cutting tool that has as the configuration of defined among the JIS CNGA120408, this cutting tool accepts to be similar to the cutting test in the example 1.These samples cutting after 20 minutes its abrasion loss little of 0.16mm, do not show after in being interrupted the cutting test, having accepted to impact for 60000 times cracked, so show excellent cutting ability.
[routine VII]
The cBN agglomerated material has median size 2 μ m, TiC material powder has median size 1 μ m, TiN material powder has median size 1 μ m, TiCN material powder has median size 1 μ m, TaC material powder has median size 1 μ m, ZrC material powder has median size 1.2 μ m, ZrN material powder has median size 1.1 μ m, WC material powder has median size 0.9 μ m, metallic aluminium powder has median size 1.2 μ m and metal cobalt powder has median size 0.8 μ m, they according to the preparation of table 7 ratio, are mixed 16 hours in the ball mill that uses alumina balls.
Mixed powder compression moulding under pressure 98MPa, giving birth to pressed compact calcines in a ultra-high voltage, pyritous device according to the method that is similar to routine I, just adopt calcination condition in the table 7 rather than the calcination condition in the table 1, so obtain cBN agglomerated material (sample No.VII-1 to 12 as shown in table 7).
Similar with routine I, the disposal type cutting tool of the structure of stipulating among use cBN agglomerated material specimen preparation such as the JIS CNGA120408.Sample No.VII-11 forms blade separately and need not weld the agglomerated material that a slice is used wired discharge cutting.Sample VII-12 scribbles one deck TiAlN film, and this film is to use the ion plating technology to be formed up to 1 μ m thickness under the bias voltage of 500 ℃ of temperature and 30V.
Table 7
| Sample number into spectrum 1) | Ratio (% volume) | Calcination condition | Remarks | |||||||
| cBN | Carbide | Nitride | Metal | Other | Heat-up rate (℃/minute) | Calcining temperature (℃) | Calcination time (branch) | Cooling rate (℃/minute) | ||
| VII-1 | All the other | TiC：20 | TiN：25 | Al：10 | - | 50 | 1400 | 15 | 50 | The blade of welding |
| VII-2 | All the other | TiC：10 WC：7 | TiN：13 | Al：3 Co：4 | - | 30 | 1350 | 30 | 45 | The blade of welding |
| VII-3 | All the other | ZrC：15 | ZrN：20 | Al：10 | - | 40 | 1400 | 20 | 30 | The blade of welding |
| VII-4 | All the other | TaC：5 | TiN：15 | Al：12 Co：3 | - | 50 | 1375 | 25 | 50 | The blade of welding |
| *VII-5 | All the other | TiC：35 | - | Al：15 | - | 50 | 1400 | 10 | 100 | The blade of welding |
| *VII-6 | All the other | - | TiN：40 | Al：15 | - | 50 | 1400 | 10 | 100 | The blade of welding |
| *VII-7 | All the other | - | - | Al：8 | TiCN： 37 | 50 | 1400 | 10 | 100 | The blade of welding |
| *VII-8 | All the other | TiC：15 | TiN：15 | Al：15 | - | 20 | 1500 | 15 | 50 | The blade of welding |
| *VII-9 | All the other | TiC：20 | TiN：10 | Al：15 | - | 50 | 1400 | 30 | 20 | The blade of welding |
| *VII-10 | All the other | TiC：10 | TiN：25 | Al：8 | - | 100 | 1600 | 10 | 100 | The blade of welding |
| VII-11 | All the other | TiC：20 | TiN：25 | Al：10 | - | 50 | 1400 | 15 | 50 | Independent blade |
| VII-12 | All the other | TiC：20 | TiN：25 | Al：10 | - | 50 | 1400 | 15 | 50 | The TiAlN coating |
1) indicates
*Sample outside the scope of the invention.
(X-ray diffraction peak intensity)
Similar with routine III, cBN agglomerated material sample is carried out X-ray diffraction analysis (XRD), determine carbide peak, nitride peak and other peaks, calculate the intensity rate at peak as shown in table 8.
(unrelieved stress)
Act on the unrelieved stress cBN particle and that act on the bonding phase by X-ray residual stress measuring method (2 θ-sin
2) locate the observation at peak is calculated, cBN used Fe-K α line, the TiC and the TiN of bonding phase used Cu-K α line angle 2 θ 〉=100 °, for example, cBN on the plane (311) distinctive peak and bonding on the plane (422) distinctive peak.It is 712GPa that this calculating is adopted modulus of elasticity E to the cBN particle, and Poisson's ratio is 0.215, is 250GPa and TiN is adopted modulus of elasticity E, and Poisson's ratio is 0.19, and it is 400GPa that TiC is adopted modulus of elasticity E, and Poisson's ratio is 0.19.
The unrelieved stress of sample No.VII-11 is measured in an agglomerated material that is cut by wired discharge, measures under the state of the unrelieved stress of sample No.VII-12 after the TiAlN layer is removed by electropolishing.
(cutting test)
With routine I is similar the cBN agglomerated material is carried out successive cutting test and is interrupted the cutting test, the ultimate value of only being interrupted the impact number of times that cutting stands before cracked in testing is set to 60000 and replaces 40000.The result is as shown in table 8.
Table 8
| Sample number into spectrum 1) | Compressive residual stress | The XRD analysis peak intensity | Intermediate phase | Cut test wear amount (mm) continuously | Be interrupted the cutting test and impact number of times | |||||||||||
| σ cBN (MP a) | σ C (MP a) | σ N (MP a) | σ C /σ N | σ b (MP a) | σ cBN /σ b | cBN I cBN | Carbide I C | Nitride I N | Carbonitride I CN | I C /I N | I N /I cBN | I C /I cBN | ||||
| VII-1 | 600 | 340 | 220 | 1.5 | 250 | 2.4 | 100 | 35 | 80 | 2 | 0.41 | 0.85 | 0.35 | TiB 2.AlN | 0.14 | 45500 |
| VII-2 | 550 | 180 | 95 | 1.9 | 120 | 4.6 | 100 | 48 | 60 | 10 | 0.80 | 0.60 | 0.48 | TiB 2.WCoB | 0.13 | 39000 |
| VII-3 | 450 | 285 | 80 | 3.6 | 175 | 2.6 | 100 | 55 | 42 | - | 1.31 | 0.42 | 0.55 | Do not exist | 0.20 | 35500 |
| VII-4 | 500 | 155 | 65 | 2.4 | 100 | 5.0 | 100 | 20 | 66 | - | 0.30 | 0.66 | 0.20 | AlN | 0.15 | 30500 |
| *VII-5 | 200 | 85 | - | - | 85 | 2.4 | 100 | 68 | - | - | - | - | 0.68 | TiB 2.AlN | 0.25 | 12000 |
| *VII-6 | 110 | - | 120 | - | 120 | 0.9 | 100 | - | 70 | - | - | 0.70 | - | Do not exist | 0.28 | 16000 |
| *VII-7 | 280 | - | - | - | 120 | 2.3 | 100 | - | - | 52 | - | - | - | Do not exist | 0.20 | 14000 |
| *VII-8 | 95 | - | - | - | 48 | 2.0 | 100 | - | - | 45 | - | - | - | AlN.TiB 2 | 0.21 | 12000 |
| *VII-9 | 180 | - | 100 | - | 100 | 1.8 | 100 | - | 2 | 40 | - | 0.02 | - | AIN | 0.26 | 14000 |
| *VII-10 | 130 | 25 | - | - | 25 | 5.2 | 100 | 5 | - | 35 | - | - | 0.05 | AlN.TiB 2 | 0.18 | 8000 |
| VII-11 | 660 | 470 | 95 | 4.9 | 220 | 3.0 | 100 | 35 | 80 | 2 | 0.44 | 0.80 | 0.35 | TiB 2.AlN | 0.14 | 53500 |
| VII-12 | 530 | 234 | 130 | 1.8 | 185 | 2.9 | 100 | 35 | 80 | 2 | 0.41 | 0.85 | 0.35 | TiB 2.AlN | 0.09 | 40000 |
1) indicates
*Sample outside the scope of the invention.
The compressive residual stress that the result of table 7 and table 8 shows cBN particle among the sample No.VII-5 to 10 has keying action weak between the cBN particle less than 300MPa, so cause short work-ing life in deficiency aspect the chip resistance ability.
Sample No.VII-1 to 4,11 and 12, the compressive residual stress of its cBN particle is more than or equal to 300MPa, all have enough wear-resistant abilities, when cutting the case-hardened steel that is difficult to cut continuously, abrasion loss is no more than 0.20mm, and shows excellent chip resistance ability, especially in being interrupted the cutting test, before cracked, have 30000 times or more times impact, show stable cutting effect in the time period of prolongation.
[routine VIII]
The living pressed compact of core component is by the Al of the TiN of the cBN, 37% volume that have mixed 50% volume and 13% volume and add a kind of powder body material extrusion process that a kind of organic binder bond prepares and be prepared from.The living pressed compact of mould component is by the Al of the TiC of the cBN, 30% volume that have mixed 60% volume and 10% volume and add a kind of material extrusion process that a kind of organic binder bond prepares and be prepared from.
The living pressed compact of the core component of preparation as described above and the living pressed compact of mould component are used for preparing the compound living pressed compact that has with the similar multifibres structure of routine II, and compound cBN agglomerated material is made in calcining then.
The analysis revealed compressive residual stress σ of the diffracted intensity that obtains from X-ray diffraction analysis to the core component of compound cBN agglomerated material and mould component
CBN=717MPa and σ
b=281MPa.The peak of carbide and nitride is observed, and the peak intensity I of carbide
CPeak intensity I with nitride
NRatio I
C/ I
NBe 0.42.
Agglomerated material uses wired discharge cutting process to cut into predetermined size, and each is welded on the bearing of agglomerating carbide substrate, so made the disposal type cutting tool that has as the structure of defined among the JIS CNGA120408.
The measurement of unrelieved stress of the blade of preparation is as previously mentioned shown compressive residual stress σ
CBN=535MPa, σ
TiC=120MPa and σ
TiN=220MPa.This cutting tool accepts to be similar to the cutting test in the example 1.These samples cutting after 20 minutes its abrasion loss little of 0.16mm, do not show after in being interrupted the cutting test, having accepted to impact for 60000 times cracked, so show excellent cutting ability.
[routine IX]
CBN material powder has median size 1.5 μ m, TiC material powder has median size 1 μ m, TiN material powder has median size 1 μ m, TiCN material powder has median size 1 μ m, HfC material powder has median size 1 μ m, and NbC material powder has median size 1 μ m, and metallic aluminium powder has median size 1.2 μ m and metal cobalt powder has median size 0.8 μ m, they according to the preparation of table 9 ratio, are mixed 16 hours in the ball mill that uses alumina balls.
Mixed powder is pressed into mould under pressure 98Mpa.This living pressed compact is calcined in a ultra-high voltage, pyritous device, and 1400 ℃ of 5GPa and temperature of keep-uping pressure 15 minutes are so obtained cBN agglomerated material (sample No.IX-1 to 9 as shown in table 9).
Table 9
| Sample number into spectrum 1) | Ratio (% volume) | Calcination condition | |||||||
| cBN | Carbide | Nitride | Metal | Other | Heat-up rate (℃/minute) | Calcining temperature (℃) | Calcination time (branch) | Cooling rate (℃/minute) | |
| IX-1 | All the other | TiC：20 | TiN：25 | Al：10 | - | 50 | 1400 | 15 | 50 |
| IX-2 | All the other | TiC：8 WC：4 | TiN：18 | Al：5 Co：3 | - | 35 | 1400 | 15 | 35 |
| IX-3 | All the other | HfC：23 | TiN：8 | Al：13 | - | 40 | 1400 | 15 | 40 |
| IX-4 | All the other | TiC：5 | TiN：10 | Al：10 Co：5 | - | 45 | 1400 | 15 | 45 |
| IX-5 | All the other | TiC：8 | TiN：10 | Al：14 | - | 50 | 1420 | 15 | 50 |
| *IX-6 | All the other | TiC：45 | - | Al：15 | - | 35 | 1375 | 15 | 35 |
| *IX-7 | All the other | - | TiN：35 | Al：15 | - | 45 | 1300 | 30 | 45 |
| *IX-8 | All the other | - | - | Al：8 | TiCN：30 | 50 | 1400 | 15 | 50 |
| *IX-9 | All the other | TiC：21 NbC：10 | TiN：3 | Al：3 Co：3 | - | 40 | 1500 | 15 | 40 |
1) indicates
*Sample outside the scope of the invention.
CBN agglomerated material sample uses wired discharge cutting process or similar approach to cut into shape as defined among the JISCNGA120408, and each is welded on the bearing of agglomerating carbide substrate.The cBN agglomerated material blade of each welding is coated with the last layer dura mater according to composition shown in the table 11 and film, so made the disposal type cutting tool by the cBN agglomerated material that scribbles dura mater (the cBN agglomerated material of surface coatings) preparation.Dura mater uses the ion plating technology to form down and under the bias voltage 150V condition at 500 ℃.
Zhi Bei cutting tool makes and estimates its component concentration, diffraction peak intensity, film thickness, ratio [I in the following method as previously mentioned
(111)/ I
(200)], compressive residual stress, continuously the cutting test be interrupted the cutting test.Component concentration, and the measuring result of diffraction peak intensity as shown in table 10, film thickness, ratio [I
(111)/ I
(200)], compressive residual stress, continuously the cutting test is as shown in table 11 with the measuring result of being interrupted the cutting test.
(each component concentration)
Similar with routine I, the component concentration of each cutting tool is determined by observe its structure under metaloscope.
For carbonitride, its existence can be determined by the X-ray diffraction peak.When observing the peak, the peak of the peak of carbide, the peak of nitride and carbonitride can quantize by the isolating method in peak, and the content of carbonitride calculates by the ratio of peak intensity.
(diffraction peak intensity)
Similar with routine III, carry out the X-ray diffraction analysis.From diffracting diagram, normalized peak intensity I
C, I
N, I
ILAnd I
CNBy supposition I
CBNBe 100 to calculate.
(dura mater thickness)
The thickness of dura mater is measured by observe the surperficial fracture surface that scribbles the cBN agglomerated material of coating under scanning electron microscope.
(ratio [the I at the X-ray diffraction peak of dura mater
(111)/ I
(200)])
Dura mater on the plane (111) locate distinctive diffraction peak intensity I
(111)Locate distinctive diffraction peak intensity I with plane (200)
(200)By the X-ray diffraction analysis to measure, their ratio [I
(111)/ I
(200)] calculate.
(compressive residual stress of cBN agglomerated material)
Acting on cBN particle and epidural unrelieved stress uses the method that is similar to routine VII to determine.Under the situation that dura mater is made up of multilayer, measure the unrelieved stress of thick one deck.
(cutting test)
With routine I is similar the cBN agglomerated material is carried out successive cutting test and is interrupted the cutting test, the ultimate value of only being interrupted the impact number of times that cutting stands before cracked in testing is set to 60000 to replace 40000.
Table 10
| Sample number into spectrum 1) | Content ratio in the agglomerated material 2)(% area) | X-ray diffraction peak intensity ratio in the agglomerated material 3) | ||||||||||
| cBN | Carbide | Nitride | Intermediate phase | Carbonitride | I cBN | I C | I N | I IL | I CN | I C/I N | I IL/I cBN | |
| IX-1 | 44 | 18 | 25 | 11 | 2 | 100 | 44 | 79 | 63 | 2 | 0.56 | 0.63 |
| IX-2 | 51 | 17 | 15 | 16 | 1 | 100 | 53 | 67 | 77 | 12 | 0.79 | 0.77 |
| IX-3 | 71 | 18 | 6 | 5 | - | 100 | 33 | 51 | 10 | - | 0.65 | 0.10 |
| IX-4 | 77 | 3 | 7 | 13 | - | 100 | 19 | 86 | 42 | - | 0.22 | 0.42 |
| IX-5 | 65 | 10 | 19 | 4 | 2 | 100 | 26 | 65 | 27 | 5 | 0.40 | 0.27 |
| *IX-6 | 45 | 38 | - | 13 | 3 | 100 | 87 | - | 32 | 8 | - | 0.32 |
| *IX-7 | 52 | - | 35 | 17 | - | 100 | - | 70 | 56 | - | - | 0.56 |
| *IX-8 | 60 | - | - | 15 | 25 | 100 | - | - | 51 | 41 | - | 0.51 |
| *IX-9 | 62 | 22 | - | 2 | 14 | 100 | 27 | - | 9 | 38 | - | 0.09 |
1) indicates
*Sample outside the scope of the invention.
2) content ratio: cBN particle, carbide, nitride are observed under metaloscope and are got.The content of carbonitride calculates from the XRD peak and gets.
3) X-ray diffraction peak intensity ratio in the agglomerated material
I
CBN: cBN plane (111) locate diffraction peak, I
N: nitride plane (200) locate diffraction peak, I
C: carbide plane (200) locate diffraction peak, I
IL: intermediate phase plane (101) locate diffraction peak, I
CN: carbonitride plane (200) locate diffraction peak.
Table 11
| Sample number into spectrum 1) | Hard coat 2)3) | Compressive residual stress 4) | Cut test wear amount (mm) continuously | Be interrupted the cutting test and impact number of times | |||||
| The first layer | The second layer | The 3rd layer | The 4th layer | Coating method | cBN (MPa) | Coating (film) (GPa) | |||
| IX-1 | (Ti 0.5Al 0.5)N (1.7)[1.5] | - | - | - | Ion plating | 500 | 2.2 | 0.12 | 50000 |
| IX-2 | TiN (0.1)[3.1] | TiCN (6.0)[0.7] | Al 2O 3 (3.0)[-] | TiN (0.1)[2.2] | Hot CVD | 900 | -0.3 | 0.10 | 39000 |
| IX-3 | Ti (0.1)[-] | TiN (1.5)[2.0] | - | - | Ion plating | 600 | 1.2 | 0.13 | 40000 |
| IX-4 | TiN (0.1)[2.0] | (Ti 0.2Al 0.7Cr 0.1)N (1.0)[1.0] | - | - | Ion plating | 400 | 0.9 | 0.14 | 45000 |
| IX-5 | TiCN (1.8)[1.2] | - | - | - | Sputter | 250 | 1.4 | 0.18 | 40000 |
| *IX-6 | (Ti 0.5Al 0.5)N (2.0)[0.8] | TiN (0.2)[1.7] | - | - | Ion plating | 150 | 1.2 | 0.21 | 13000 |
| *IX-7 | TiN (1.0)[2.0] | - | - | - | Ion plating | 160 | 1.3 | 0.23 | 8500 |
| *IX-8 | TiCN (2.5)[0.9] | - | - | - | Ion plating | 200 | 2 | 0.20 | 12000 |
| *IX-9 | - | - | - | - | - | 150 | - | 0.31 | 28000 |
1) indicates
*Sample outside the scope of the invention.
2) thickness of the interior numeral dura mater of parenthesis () (unit: μ m)
3) the interior numeral XRD midplanes of square brackets [] (111) are located peak intensity and plane (200) locate peak intensity ratio [I
(111)/ I
(200)].
4) has the numeric representation stretching unrelieved stress of negative sign "-".
Table 9-11 result shows that the sample No.IX-6 and 9 of a carbide-containing (TiC) in its agglomerated material has weak keying action between the cBN particle, then aspect the chip resistance ability deficiency.The sample No.IX-7 of a nitrogenate (TiN) has inadequate abrasion resistance properties and short work-ing life in its agglomerated material.Carbonitride (TiCN) is all not enough aspect wear-resistant and chip resistance as the sample No.IX-8 of bonding phase.Do not provide the sample No.IX-9 of dura mater all not enough aspect wear-resistant and chip resistance.
Sample No.IX-1 to 5 within the scope of the present invention, all have enough wear-resistant abilities, when cutting the case-hardened steel that is difficult to cut continuously, abrasion loss is no more than 0.20mm, and can tolerate before cracked 35000 times or more times impact in being interrupted the cutting test.Especially sample No.IX-1 does not show crackedly after experience is impacted for 50000 times, so show excellent chip resistance ability, shows stable cutting effect in the time period that prolongs.
[routine X]
The living pressed compact of core component is by the Al of the TiN of the cBN, 35% volume that have mixed 50% volume and 15% volume and add a kind of powder body material extrusion molding that a kind of organic binder bond prepares and be prepared from.The living pressed compact of mould component is by the Al of the TiC of the cBN, 25% volume that have mixed 65% volume and 10% volume and add a kind of material extrusion molding that a kind of organic binder bond prepares and be prepared from.
The living pressed compact of the core component of preparation as described above and the living pressed compact of mould component are used for preparing the compound living pressed compact that has with the similar multifibres structure of routine II, and compound cBN agglomerated material is made in calcining then.
CBN agglomerated material sample uses wired discharge cutting process to cut into predetermined size (as the shape of defined among the JISCNGA120408), and each is welded on the bearing of agglomerating carbide substrate.Soldered cBN agglomerated material uses cathode arc ion plating technology to plate the (Ti of one deck 2.0 μ m on its surface
0.5, Al
0.5) the N film, so make a kind of cutting tool (sample No.X-1) by the preparation of the cBN agglomerated material of surface coatings.
The structure of the cutting tool of Huo Deing is observed under metaloscope like this.Show as the cBN particle of black, the TiN sharp outline that shows as the TiC of brown and show as white.Measure 30 particulate areas of every kind of component and be averaged by image analysis.The ratio of the area that is occupied by these components calculates by these mean values relatively, and the result is: cBN is 50%, TiC is 10%, TiN be 25% and TiCN be 2%.
By X-ray diffraction analysis (XRD) dura mater of cutting tool as mentioned above, similar with routine IX, measure on the plane (111) and locate distinctive diffraction peak intensity I
(111)Locate distinctive diffraction peak intensity I with plane (200)
(200), their ratio [I
(111)/ I
(200)] be defined as 1.8.
Sample accepts to be similar to the cutting test among the routine IX.These samples cutting after 20 minutes its abrasion loss little of 0.15mm, do not show after in being interrupted the cutting test, having accepted to impact for 60000 times cracked, so show excellent cutting ability.
[routine XI]
Use the method preparation that is similar to routine IX with the same cBN agglomerated material of the sample No.IX-1 shown in the table 9.The cBN agglomerated material uses wired discharge means to cut into predetermined shape, be welded on the bearing of the disposal type blade that is prepared from by sintered carbide of milling cutter, so make one and the similar cutting tool of routine IX, only use plasma CVD technology to form a class diamond carbon film (sample No.XI-1) that thickness is 0.2 μ m.
Preparation is with the same cBN agglomerated material of the sample No.IX-8 shown in the table 9.The cBN agglomerated material uses wired discharge means to cut into predetermined shape, be welded on the bearing of the disposal type blade that is prepared from by sintered carbide of milling cutter, so make one and the similar cutting tool of routine IX, only use plasma CVD technology to form a class diamond carbon film (sample No.XI-2) that thickness is 0.2 μ m.
Under the following stated condition, accept the cutting ability test according to the cutting tool of above method preparation.
Cutting mode: milling
Workpiece: Ti-16Al-4V alloy
Cutting speed: 500m/min.
Infeed: 1.0mm
Feeding speed: 0.3mm/ cutter
Measure: after length of cut reaches 1m, under scanning electron microscope, observe the incisxal edge situation.
In the cutting test, sample No.XI-2 is impaired, show coming off of cracked and film on incisxal edge, but the incisxal edge of sample No.XI-1 remains intact, and does not show coming off of cracked and film.
Claims (34)
1. cubic boron nitride sintered material, be made up of bonded bonding cubic boron nitride particles, wherein said bonding contains the simultaneous therein carbide and the nitride that is selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements that is selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements mutually.
2. cubic boron nitride sintered material, have such monfil shape structure: mould component is covered with the circumferential surface of fibrous core member, wherein said mould component is made by cubic boron nitride sintered material, this cubic boron nitride sintered material is by being formed by the bonding cubic boron nitride particles of nitride-bonded, and described nitride-bonded is made by the nitride that is selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements; Described fibrous core member is made by cubic boron nitride sintered material, this cubic boron nitride sintered material is formed by being carbonized the bonding cubic boron nitride particles of thing bonding, and described carbide bonding is made by the carbide that is selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements.
3. cubic boron nitride sintered material, have such monfil shape structure: mould component is covered with the circumferential surface of fibrous core member, wherein said mould component is made by cubic boron nitride sintered material, this cubic boron nitride sintered material is formed by being carbonized the bonding cubic boron nitride particles of thing bonding, and described carbide bonding is made by the carbide that is selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements; Described core component is made by cubic boron nitride sintered material, this cubic boron nitride sintered material is by being formed by the bonding cubic boron nitride particles of nitride-bonded, and described nitride-bonded is made by the nitride that is selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements.
4. according to the cubic boron nitride sintered material of claim 2 or 3, it has by a plurality of described monfil shape structures and ties together and the multifilament shape structure that constitutes.
5. according to each cubic boron nitride sintered material in the claim 1 to 3, the metallic element that wherein constitutes described carbide is a metallic element of the same race with the metallic element that constitutes described nitride.
6. according to the cubic boron nitride sintered material of claim 5, wherein said metallic element is a titanium.
7. according to each cubic boron nitride sintered material in the claim 1 to 3, wherein the content ratio p of carbide in whole cubic boron nitride sintered material
CContent ratio p with nitride
NRatio p
C/ p
NIn 0.2～3.0 scope.
8. according to each cubic boron nitride sintered material in the claim 1 to 3, provide such intermediate phase on wherein around described cubic boron nitride particles: it contains the compound of the component that is different from described bonding phase, and described compound is carbide, nitride, carbonitride, boride, boron-carbide, boron nitride and the oxide compound that is selected from least a metallic element in the 4th, 5,6 family's metals, iron family metal and the aluminium in the periodic table of elements.
9. cubic boron nitride sintered material according to Claim 8, the area content ratio p of the whole relatively cubic boron nitride sintered material of wherein said cubic boron nitride particles
CBNIn 45%～80% scope, the area content ratio p of described carbide
CIn 2%～45% scope, the area content ratio p of described nitride
NIn 3%～50% scope, the area content ratio p of described intermediate phase
mIn 0%～25% scope,
10. according to each cubic boron nitride sintered material in the claim 1 to 3, be 5% or still less wherein as the described carbide and the weight content ratio of the relative whole cubic boron nitride material of carbonitride of the sosoloid of described nitride.
11., wherein in X-ray diffraction is analyzed, exist simultaneously by the distinctive peak of described nitride with by the distinctive peak of described carbide according to each cubic boron nitride sintered material in the claim 1 to 3.
12. according to the cubic boron nitride sintered material of claim 11, wherein in described X-ray diffraction is analyzed, the described carbide diffraction peak intensity I that (200) are located on the plane
CWith the described nitride diffraction peak intensity I that (200) are located on the plane
NRatio I
C/ I
NIn 0.2～～1.2 scope.
13. according to the cubic boron nitride sintered material of claim 11, wherein in described X-ray diffraction is analyzed, the diffraction peak intensity I of described nitride
NWith the described cubic boron nitride particles diffraction peak intensity I that (111) are located on the plane
CBNRatio I
N/ I
CBNIn 0.3～1 scope.
14. according to the cubic boron nitride sintered material of claim 11, wherein in described X-ray diffraction is analyzed, the diffraction peak intensity I of described carbide
CWith the described cubic boron nitride particles diffraction peak intensity I that (111) are located on the plane
CBNRatio I
C/ I
CBNIn 0.1～0.9 scope.
15. according to the cubic boron nitride sintered material of claim 11, wherein in described X-ray diffraction is analyzed, as the carbonitride diffraction peak intensity I that (200) are located on the plane of the sosoloid of described carbide and described nitride
CN, and peak intensity I
CAnd I
NSatisfy such relational expression: I
CN＜0.3I
CAnd I
CN＜0.3I
N
16. according to the cubic boron nitride sintered material of claim 11, wherein in described X-ray diffraction is analyzed, described intermediate phase is the diffraction peak intensity I of (101) on the plane
ILWith the described cubic boron nitride particles diffraction peak intensity I that (111) are located on the plane
CBNRatio I
IL/ I
CBNIn 0.1～0.8 scope.
17. according to each cubic boron nitride sintered material in the claim 1 to 3, the median size d that calculates by the corresponding circle of equal value of area wherein with the individual particle of described nitride
NAnd by and the median size d that calculates of the corresponding circle of equal value of area of the individual particle of described carbide between cubic boron nitride particles
CRatio d
N/ d
CBetween 0.4～1.2, described area gets by the cross section of observing cubic boron nitride sintered material.
18. according to the cubic boron nitride sintered material of claim 17, wherein by justifying the median size d that calculates with the corresponding equivalence of the area of single cubic boron nitride particles
CBNBe 5 μ m or littler, the median size of described carbide in 1～3 mu m range, the median size d of described nitride
NIn 0.5～2 mu m range, above-mentioned median size is definite by the cross section of observing described cubic boron nitride sintered material.
19. according to each cubic boron nitride sintered material in the claim 1 to 3, the compressive residual stress σ that keeps on the wherein said cubic boron nitride particles
CBNBe 300MPa or bigger.
20. according to the cubic boron nitride sintered material of claim 19, compressive residual stress σ wherein
bRemain on described bonding mutually in, and compressive residual stress σ
CBNWith compressive residual stress σ
bRatio (σ
CBN/ σ
b) in 2～5 scopes.
21. according to the cubic boron nitride sintered material of claim 20, the middle mutually compressive residual stress σ that keeps of wherein said bonding
bBe 60～300MPa.
22., wherein act on compressive residual stress σ on the described carbide in mutually in described bonding according to the cubic boron nitride sintered material of claim 19
CWith the compressive residual stress σ that acts on the described nitride
NRatio σ
C/ σ
NIn 1.5～5 scopes.
23., wherein act on the compressive residual stress σ on the described nitride according to the cubic boron nitride sintered material of claim 22
NIn 30～200MPa scope, act on the compressive residual stress σ on the described carbide
CIn 100～700MPa scope.
24. according to each cubic boron nitride sintered material in the claim 1 to 3, wherein said cubic boron nitride material surface scribbles one deck dura mater at least, described dura mater is made of at least a following material: be selected from least a metallic element in the 4th, 5,6 family's metals in the periodic table of elements, Al and carbide Si, nitride, boride, oxide compound and carbonitride and their sosoloid, hard carbon and boron nitride.
25. according to the cubic boron nitride sintered material of claim 24, wherein said dura mater uses the physical vapor deposition (PVD) method to form.
26. according to the cubic boron nitride sintered material of claim 24, the total thickness of wherein said dura mater is 0.1-15 μ m.
27. according to the cubic boron nitride sintered material of claim 24, the compressive residual stress that keeps in the wherein said dura mater is in 0.1～30GPa scope.
28., be 200MPa or higher wherein with the residual compression pressure that scribbles the cubic boron nitride sintered material that described dura mater state exists according to the cubic boron nitride sintered material of claim 24.
29. according to the cubic boron nitride sintered material of claim 24, in the wherein said dura mater at least one deck by the compound formation of following general formula (1) expression:
[chemical molecular formula 3]
[Ti
a，M
1-a][B
xC
yN
zO
1-(x+y+z)] ...(1)
Wherein M represents to be selected from the periodic table of elements at least a metallic element except that Ti in the 4th, 5,6 family's elements, Al and Si, 0＜a≤1,0≤x≤1,0≤y≤1 and 0≤z≤1.
30. according to the cubic boron nitride sintered material of claim 29, in the wherein said dura mater at least one deck by the compound formation of following general formula (2) expression:
[chemical molecular formula 4]
[Ti
a，M
1-a][B
xC
yN
zO
1-(x+y+z)] ...(2)
Wherein M represents to be selected from the periodic table of elements at least a metallic element except that Ti in the 4th, 5,6 family's elements, Al and Si, 0.3≤a≤0.7,0≤x≤0.5,0≤y≤0.5,0.5≤z≤1 and x+y+z≤1.
31. according to the cubic boron nitride sintered material of claim 24, the diffraction peak intensity I that (111) are located on the plane that measures during the X-ray diffraction of one deck is analyzed at least in the wherein said dura mater
(111)The diffraction peak intensity I that locates with on the plane (200)
(200)Ratio I
(111)/ I
(200)Be 0.7 or higher.
32. by the cutting tool of making according to the cubic boron nitride sintered material in each in the claim 1 to 3, it is used in the cutting operation by blade is pressed on the workpiece that will cut, wherein blade forms along crestal line, and at the crestal line place, its side and rake are met.
33. according to the cutting tool of claim 32, comprise cutter hub and the brazing point of a knife on the bearing of described cutter hub, wherein said point of a knife is made by described cubic boron nitride sintered material.
34. make the method according to the cutting tool of claim 32, described cutting tool is used in the cutting operation by blade is pressed on the workpiece that will cut, wherein blade forms along crestal line, and at the crestal line place, its described side and described rake are met.
Applications Claiming Priority (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2004314592 | 2004-10-28 | ||
| JP314592/2004 | 2004-10-28 | ||
| JP049771/2005 | 2005-02-24 | ||
| JP096111/2005 | 2005-03-29 | ||
| JP095857/2005 | 2005-03-29 | ||
| JP095855/2005 | 2005-03-29 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101031525A true CN101031525A (en) | 2007-09-05 |
| CN100584797C CN100584797C (en) | 2010-01-27 |
Family
ID=38716226
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200580033358A Active CN100584797C (en) | 2004-10-28 | 2005-10-26 | Cubic boron nitride sintered material and cutting tool using the same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100584797C (en) |
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102152216A (en) * | 2010-12-27 | 2011-08-17 | 长沙岱勒新材料科技有限公司 | Cubic boron nitride cutting line |
| CN103741002A (en) * | 2013-06-28 | 2014-04-23 | 长春阿尔玛斯科技有限公司 | Preparation method of superhard composite material |
| WO2015079035A1 (en) * | 2013-11-29 | 2015-06-04 | Sandvik Intellectual Property Ab | A method of making a powder composition for production of a cubic boron nitride composite material |
| CN104858458A (en) * | 2014-02-26 | 2015-08-26 | 三菱综合材料株式会社 | Surface Coating Cutting Tool Having Excellent Abnormal Damage Resistance And Wear Resistance |
| CN105019026A (en) * | 2014-04-18 | 2015-11-04 | 住友电气工业株式会社 | Cubic boron nitride polycrystal, cutting tool, wear-resistant tool, grinding tool, and method of producing cubic boron nitride polycrystal |
| CN106414371A (en) * | 2014-06-27 | 2017-02-15 | 京瓷株式会社 | Sintered object of cubic boron nitride and cutting tool |
| CN107000068A (en) * | 2014-11-27 | 2017-08-01 | 三菱综合材料株式会社 | The resistance to surface-coated cutting tool for collapsing knife, excellent in abrasion resistance |
| CN107973606A (en) * | 2017-10-23 | 2018-05-01 | 富耐克超硬材料股份有限公司 | Polycrystalline cubic boron nitride, preparation method and applications, the cutter comprising the polycrystalline cubic boron nitride |
| CN108326353A (en) * | 2018-02-06 | 2018-07-27 | 江苏宏威重工机床制造有限公司 | A kind of machinery plate shearing machine |
| CN108349821A (en) * | 2016-10-06 | 2018-07-31 | 住友电气工业株式会社 | Manufacture method, boron nitride polycrystalline body, cutting element, wear resistant tools and the milling tool of boron nitride polycrystalline body |
| CN108655429A (en) * | 2017-03-28 | 2018-10-16 | 株式会社泰珂洛 | Coated cutting tool |
| CN108675813A (en) * | 2018-07-07 | 2018-10-19 | 郑州万创智造科技有限公司 | A kind of high intensity polycrystalline cubic boron nitride and its manufacturing method |
| CN113508101A (en) * | 2019-03-05 | 2021-10-15 | 三菱综合材料株式会社 | cBN sintered body and cutting tool |
| CN114144392A (en) * | 2019-07-18 | 2022-03-04 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
| CN114761371A (en) * | 2019-12-16 | 2022-07-15 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
-
2005
- 2005-10-26 CN CN200580033358A patent/CN100584797C/en active Active
Cited By (24)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102152216A (en) * | 2010-12-27 | 2011-08-17 | 长沙岱勒新材料科技有限公司 | Cubic boron nitride cutting line |
| CN103741002A (en) * | 2013-06-28 | 2014-04-23 | 长春阿尔玛斯科技有限公司 | Preparation method of superhard composite material |
| CN103741002B (en) * | 2013-06-28 | 2016-07-06 | 长春阿尔玛斯科技有限公司 | A kind of preparation method of super-hard compound material |
| WO2015079035A1 (en) * | 2013-11-29 | 2015-06-04 | Sandvik Intellectual Property Ab | A method of making a powder composition for production of a cubic boron nitride composite material |
| CN104858458B (en) * | 2014-02-26 | 2018-09-14 | 三菱综合材料株式会社 | The surface-coated cutting tool of abnormal damage resistance and excellent in wear resistance |
| CN104858458A (en) * | 2014-02-26 | 2015-08-26 | 三菱综合材料株式会社 | Surface Coating Cutting Tool Having Excellent Abnormal Damage Resistance And Wear Resistance |
| CN105019026A (en) * | 2014-04-18 | 2015-11-04 | 住友电气工业株式会社 | Cubic boron nitride polycrystal, cutting tool, wear-resistant tool, grinding tool, and method of producing cubic boron nitride polycrystal |
| CN106414371A (en) * | 2014-06-27 | 2017-02-15 | 京瓷株式会社 | Sintered object of cubic boron nitride and cutting tool |
| CN106414371B (en) * | 2014-06-27 | 2019-07-19 | 京瓷株式会社 | Cubic boron nitride sintered compact and cutting element |
| US10556273B2 (en) | 2014-11-27 | 2020-02-11 | Mitsubishi Materials Corporation | Surface-coated cutting tool having excellent chipping resistance and wear resistance |
| CN107000068A (en) * | 2014-11-27 | 2017-08-01 | 三菱综合材料株式会社 | The resistance to surface-coated cutting tool for collapsing knife, excellent in abrasion resistance |
| CN107000068B (en) * | 2014-11-27 | 2019-04-19 | 三菱综合材料株式会社 | The excellent surface-coated cutting tool of chipping resistance, wearability |
| CN108349821B (en) * | 2016-10-06 | 2021-11-02 | 住友电气工业株式会社 | Method for producing boron nitride polycrystal, cutting tool, wear-resistant tool, and grinding tool |
| CN108349821A (en) * | 2016-10-06 | 2018-07-31 | 住友电气工业株式会社 | Manufacture method, boron nitride polycrystalline body, cutting element, wear resistant tools and the milling tool of boron nitride polycrystalline body |
| CN108655429A (en) * | 2017-03-28 | 2018-10-16 | 株式会社泰珂洛 | Coated cutting tool |
| CN107973606B (en) * | 2017-10-23 | 2020-06-12 | 富耐克超硬材料股份有限公司 | Polycrystalline cubic boron nitride, preparation method and application thereof, and cutter containing polycrystalline cubic boron nitride |
| CN107973606A (en) * | 2017-10-23 | 2018-05-01 | 富耐克超硬材料股份有限公司 | Polycrystalline cubic boron nitride, preparation method and applications, the cutter comprising the polycrystalline cubic boron nitride |
| CN108326353A (en) * | 2018-02-06 | 2018-07-27 | 江苏宏威重工机床制造有限公司 | A kind of machinery plate shearing machine |
| CN108675813A (en) * | 2018-07-07 | 2018-10-19 | 郑州万创智造科技有限公司 | A kind of high intensity polycrystalline cubic boron nitride and its manufacturing method |
| CN113508101A (en) * | 2019-03-05 | 2021-10-15 | 三菱综合材料株式会社 | cBN sintered body and cutting tool |
| EP3936264A4 (en) * | 2019-03-05 | 2022-11-30 | Mitsubishi Materials Corporation | Cbn sintered compact and cutting tool |
| CN114144392A (en) * | 2019-07-18 | 2022-03-04 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
| CN114144392B (en) * | 2019-07-18 | 2023-06-02 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
| CN114761371A (en) * | 2019-12-16 | 2022-07-15 | 住友电气工业株式会社 | Cubic boron nitride sintered body |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100584797C (en) | 2010-01-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101031525A (en) | Cubic boron nitride sintered material and cutting tool using the same | |
| CN1148761C (en) | Rare earth permanent magnet and method for producing the same | |
| CN1296508C (en) | Free-cutting tool steel | |
| CN1125793C (en) | Method of mfg. diamond-silicon carbide-silicon composite and composite produced by this method | |
| CN1070540C (en) | Coated hard alloy blade member | |
| CN1293972C (en) | Cutting tool coated with hard alloy on surface for high-speed heavy cutting | |
| CN1097639C (en) | Titanium-based composition material, method for producing the same and engine valve | |
| CN1304626C (en) | Hard film and hard film coated tool | |
| CN1854104A (en) | Solid-solution powder, method to prepare the solid-solution powder, ceramic using the solid-solution powder, method to prepare the ceramic, cermet powder including the solid-solution powder, method to | |
| CN100349825C (en) | Method of manufacturing a diamond composite and a composite produced by same | |
| CN101068759A (en) | CBN sintered body for high surface integrity machining and cBN sintered body cutting tool | |
| CN1362309A (en) | Hard tunide for cutting tool, hard-tunicle-coated cutting tool, method of manufacture of hard-tunicle and target for forming hard tunicle | |
| CN1065614A (en) | Method of making cemented carbide articles | |
| CN1426488A (en) | Cemented carbide tool and method of making | |
| CN1651596A (en) | Hard laminated film, method of manufacturing the same and film-forming device | |
| CN1876368A (en) | Hard-coated member | |
| CN1942274A (en) | Surface-coated cutting tool | |
| CN101074474A (en) | Hard laminated film, method of manufacturing the same and film-forming device | |
| CN1205036A (en) | Steel having excellent machinability and machined component using said steel | |
| CN1344814A (en) | Iron-base sintered powder metal body, its manufacture and manufacture of high-strength high-density iron-base sintering assembly | |
| CN1675409A (en) | Process for producing alumina coating composed mainly of alpha-type crystal structure, alumina coating composed mainly of alpha-type crystal structure, laminate coating including the alumina coating, | |
| CN1049120A (en) | Produce the method for synthetic materials | |
| CN1818125A (en) | Hard coating, target for forming hard coating, and method for forming hard coating | |
| CN1660531A (en) | Coated cement cutting tool with a chipping resistant, hard coating layer | |
| CN1198116A (en) | Iron-base alloy foils for liquid-phase diffusion bonding of iron-base material bondable in oxidizing atmosphere |
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 |