CN100569421C - Cermet insert and cutting element - Google Patents
Cermet insert and cutting element Download PDFInfo
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- CN100569421C CN100569421C CNB2006800213497A CN200680021349A CN100569421C CN 100569421 C CN100569421 C CN 100569421C CN B2006800213497 A CNB2006800213497 A CN B2006800213497A CN 200680021349 A CN200680021349 A CN 200680021349A CN 100569421 C CN100569421 C CN 100569421C
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Abstract
The invention provides good cermet insert of breakage resistance and mar proof and cutting element.Have and comprise hard phase and bonding little tissue mutually; Form as sintered body, about Ti, and Nb and/or Ta, and W, the value that value that value that converts by carbonitride with described Ti and described Nb and/or Ta convert by carbide and described W convert by carbide close quantifier, all with respect to described little tissue, contain 70 to 95 weight %, described W is 15 to 35 weight % by the value that carbide converts; Contain Co and/or Ni.And as the hard phase, have in following (1) to (3) one or more: (1) has the first hard phase of cored structure, wherein core contains the titanium carbonitride phase, and periphery contains (Ti, W, Ta/Nb) CN phase, (2) have the second hard phase of cored structure, and wherein core and periphery all contain (Ti, W, Ta/Nb) CN phase, the 3rd hard phase of (3) phase structure, it comprises the titanium carbonitride phase, and described titanium carbonitride mutually in, rich W distributes mutually unevenly.
Description
Technical field
The present invention relates to cermet insert and cutting element, in particular to the good cermet insert of mar proof and breakage resistance and have the cutting element of this cermet insert.
Background technology
In the past,, used cermet insert,, proposed various technical schemes in order to improve the performance of this cermet insert with the little tissue that constitutes mutually by hard phase (hard particles) bonding alternate with being present in hard in order to cut steel etc.
For example, in the following patent documentation 1, proposed a kind of high-toughness metal ceramal, it is set at more than the 10 mutually all volume % of hard by the ratio that inside is contained independently the particle of metal phase, and its breakage resistance is improved.
In addition, in the following patent documentation 2, proposed a kind of cutting tool made of cermet, it is by the Ti that disperses to have core in the inside of cutting element, the particle that W content distributes than periphery high concentration, and its breakage resistance is improved.
Patent documentation 1: No. 2775646 communique of Japan Patent
Patent documentation 2: Japanese kokai publication hei 9-1405 communique
Summary of the invention
But, in the technology of aforementioned patent document 1,,, therefore have the problem that hard phase hardness reduces, mar proof reduces because the hear resistance of the metal phase in the particle is low although breakage resistance has improvement to a certain degree.
In addition, in the technology of aforementioned patent document 2, bonding and the bonding strength height of hard between mutually, but there is the problem of the reduction of hard phase hardness, mar proof reduction equally.
The present invention carries out in order to address the above problem, and its objective is that providing a kind of can keep high abrasion resistance, can realize the cermet insert and the cutting element of high breakage resistance simultaneously.
Being used to solve first invention (cermet insert) of foregoing problems, is a kind of cermet insert,
Have and comprise hard mutually and mutually the little tissue of boning,
Form as sintered body, about Ti; And Nb and/or Ta; And W, the value that value that value that converts by carbonitride with described Ti and described Nb and/or Ta convert by carbide and described W convert by carbide close quantifier, all with respect to described little tissue, contain 70 to 95 weight % (wherein, described W all is 15 to 35 weight % by the value that carbide converts with respect to little tissue), simultaneously, contain Co and/or Ni
Wherein, as described hard phase, have one or more (situations that still, do not comprise following separately (2)) in following (1) to (3):
(1) the first hard phase of cored structure is arranged, wherein core contains the titanium carbonitride phase, periphery contain (Ti, W, Ta/Nb) CN phase,
(2) the second hard phase of cored structure is arranged, wherein core and periphery contain (Ti, W, Ta/Nb) CN phase,
(3) the 3rd hard phase of phase structure, it comprises the titanium carbonitride phase,
And, described titanium carbonitride mutually in, than around contain and more many rich W of W and distribute unevenly mutually.
Cermet insert of the present invention, expression ground is such as schematically shown in Figure 1, in fact by comprising hard phase (hard particles) and covering its bonding little organizational composition mutually on every side.
Among the present invention, the Ti of hard phase will be used to form; With Nb and/or Ta; Being set at 70 to 95 weight % with the total of each scaled value of W, is because following reason.In addition, Ti is the value that TiCN converts, and Nb and/or Ta are the values that (Nb/Ta) C converts, and W is the value that WC converts.
At first, form the composite carbon nitride and the carbonitride of hard phase (hard particles), has the effect that improves ceramic-metallic hardness, improves mar proof, but, when the ratio of hard phase surpasses all 95 weight % of blade, the ratio of the phase that relatively bonds will be less than 5 weight %, thereby toughness descends, breakage resistance descends.On the other hand, the ratio of hard phase is during less than 70 weight %, and the ratio of the phase that relatively bonds will be above 30 weight %, so the mar proof of blade descends.
In addition, by contain the W of 15 to 35 weight % with respect to little tissue all (WC conversion), can improve the mar proof and the breakage resistance of blade.
In addition, Co improves agglutinating property, forms the bonding phase, and improves the intensity of blade.Ni forms the bonding phase when sintering, the hear resistance of bonding phase is improved, and can improve the mar proof of blade.
In addition, described hard becomes the formation that is selected from above-mentioned three kinds of hard phases mutually, can improve hardness, the raising mar proof of blade thus.
Especially, in the present invention, as Fig. 2 schematically represents (the little structure observation result of the TEM of hard phase section), rich W layer the titanium carbonitride of the hard phase of described (1) or (3) mutually in uneven distribution.At this, so-called uneven distribution, be meant W be not be scattered in equably titanium carbonitride mutually in, but exist lopsidedly at specific position W and form rich W phase.
Among the present invention, by W the titanium carbonitride of described (1) or (3) mutually in uneven distribution, and have high abrasion resistance and breakage resistance, about the reason that this mar proof and breakage resistance improve, consider as follows.
Promptly, by containing W in mutually at hard, improve the breakage resistance of hard phase, in addition, not only to contain W in mutually at hard, there is rich W phase at hard unevenly in mutually, TiCN is cut apart mutually by rich W and is bulk and has (with reference to Fig. 3) thus, in this bulk portion, kept the high rigidity of TiCN self, and can realize high abrasion resistance.In addition, Fig. 3 has schematically shown W intrusion (for example, atom be that clathrate distributes and form) the inner mutually dislocation part that produces of titanium carbonitride, has formed the state of rich W phase with for example planar (stratiform).
Therefore, hard mutually in W exist with scheduled volume, with and exist with state in the rich W phase uneven distribution of titanium carbonitride in mutually, obtained the remarkable result that can realize high abrasion resistance and high breakage resistance simultaneously thus.
In addition, described " A and/or B " is meant A and B at least one (down with).
Second invention, wherein, at least one little tissue of the surface of described cermet insert and section, described titanium carbonitride mutually in, described rich W with wire and netted at least a state uneven distribution.
Among the present invention, the uneven distribution state of rich W phase is illustrative with two dimension.That is, illustration the rich W state mutually that occurs in surface and the section of blade.
Shown in Figure 2 as described, (1) first hard mutually with (3) the 3rd hard titanium carbonitride mutually mutually in, rich W is with wire or netted uneven distribution.In addition, in the TEM photo for example with rich W layers of expression such as the lines of white.
That is, among the present invention, for example carry out result's demonstration of little structure observation by TEM, rich W can observe with wire or netted two dimension mutually.Consider this be because: titanium carbonitride for example is the end face of the rich W phase that stratiform exists in mutually, in the surface of blade or section with wire or netted being observed.
In addition, rich W phase for example as shown in Figure 4, when existing to the vertical section medium dip of the film sample that uses in tem observation, in the TEM photo, is observed as the line of the white of wide H.
The 3rd invention, wherein, described titanium carbonitride mutually in, described rich W is with at least a state uneven distribution in stratiform, the cylindric and prism-shaped.
Among the present invention, illustration the three-dimensional uneven distribution state of the rich W phase of titanium carbonitride in mutually.
As state with this stratiform, cylindric, prism-shaped uneven distribution, can enumerate the state that for example constitutes with plane or flexure plane, also can perforate on these faces.In addition, these rich W layers also can be to exist with a plurality of layers or cylinder or the prismatic state that mixes mutually, the state that for example forms with the perhaps a plurality of bubble shapes set of squamous etc.
In addition, rich W layer is during for example with the stratiform uneven distribution, when carrying out tem observation perpendicular to this layer, such as illustrated in Figure 9, rich W is observed as the white plane with predetermined broadening mutually, around this white plane, observe the line of the wire that constitutes other rich W phase or netted white usually.
The 4th invention wherein, in described hard phase and/or in boning mutually, also contains Mo.
By containing Mo, the wetability of hard phase or bonding phase improves, and therefore can improve agglutinating property.
The 5th invention, wherein, described bonding mutually in, all also contain the W of 40 to 60 weight % mutually with respect to described bonding.
Among the present invention, contain the W of 40 to 60 weight % in boning mutually, the high temperature hardness of the phase that therefore bonds improves, and thus, for example in the high-speed cutting processing that produces with high temperature, can bring into play good mar proof.
The 6th invention (cutting element) wherein, has above-mentioned first to the 5th each described cermet insert in retainer.
Cutting element of the present invention, owing in retainer, have above-mentioned cermet insert, so mar proof and breakage resistance excellence.
At this, as optimal way of the present invention, the also described such following formation that adopts of application Japanese Patent Application 2005-173463 that proposed of the applicant for example.
For example, as blade, can adopt " a kind of have a tungsten carbide of comprising: 20 to 30 weight %, ramet and/or niobium carbide: 5 to 10 quality %, Co:5 to 10 quality %, Ni:5 to 10 quality %, titanium carbonitride: the sintered body of the briquetting that the cooperation of surplus (wherein, containing 50 to 60 quality %) is formed ".
In addition, for example,, can adopt " according to the little structure observation of transmission electron microscope, have comprise that hard is that 75 to 90 area %, bonding are the formation of little tissue of surplus mutually mutually " as described sintered body.
And, as described bonding phase, can adopt and " contain Co:18 to 33 quality %, Ni:20 to 35 quality %, Ti with shared proportional meter in boning mutually; And Ta and/or Nb:5 quality % are following, W: the formation of surplus (wherein, W:40 to 60 quality %) ".
In addition, in the surplus of composition etc., contain unavoidable impurities usually.
Description of drawings
Fig. 1 is a key diagram of schematically representing the section of cermet insert of the present invention.
Fig. 2 schematically represents the present invention and the key diagram of hard section mutually of example in the past.
Fig. 3 is the key diagram of the hard phase internal structure of expression cermet insert of the present invention.
Fig. 4 is a key diagram of schematically representing the sample vertical section of transmission electron microscope.
Fig. 5 is the perspective view of the cermet insert of expression embodiment 1.
Fig. 6 is the key diagram of the cutting element of expression embodiment 1.
Fig. 8 is the photo of expression the present invention example sample by little tissue of transmission electron microscope shooting.
Fig. 9 is the photo of expression the present invention example sample by little tissue of transmission electron microscope shooting.
Figure 10 is the photo of expression the present invention example sample by little tissue of transmission electron microscope shooting.
Figure 11 is the photo of expression comparative example sample by little tissue of transmission electron microscope shooting.
Figure 12 is the photo of expression comparative example sample by little tissue of transmission electron microscope shooting.
Figure 13 is the key diagram of sample vertical section of schematically representing the transmission electron microscope of embodiment 3.
Figure 14 is the key diagram of sample vertical section of schematically representing the transmission electron microscope of embodiment 4.
Figure 15 is the key diagram of sample vertical section of schematically representing the transmission electron microscope of embodiment 5.
Figure 16 is the key diagram of manufacture method of the cermet insert of expression embodiment 6.
Symbol description
1... blade
3... retainer
5... stationary fixture
7... cutting element
The specific embodiment
Below, for the example (embodiment) of best mode for carrying out the invention, be that the embodiment of cermet insert and cutting element describes.
Embodiment 1
A) at first, the cermet insert (following only note is made " blade ") for present embodiment describes.
As shown in Figure 5, the blade 1 of present embodiment is to comprise iso standard: the cutting tip of the sintered body of the shape of SNGN120408 (cutting チ Star プ).
This blade 1, shown in Figure 1 as described, by comprising hard phase (hard particles) and covering around it and the bonding little tissue (containing unavoidable impurities) mutually that exists constitutes.
In addition, sintered body as blade 1 is formed, about Ti and, Nb and/or Ta and W, value that value that converts by carbonitride with Ti and Nb and/or Ta convert by carbide and value that W is converted by carbide close quantifier, all contain 70 to 95 weight % with respect to blade.Wherein, for W, the value to convert by carbide all contains 15 to 35 weight % with respect to blade.In addition, as the hard phase, as described later, contain the composite carbon nitride of titanium carbonitride and Ti and W and Ta and/or Nb.
In addition, in this blade 1, the bonding phase as the surplus of hard phase contains W and Co and/or Ni.In addition, W all contains 40 to 60 weight % mutually with respect to bonding, and Co contains 18 to 33 weight %, and Ni contains 20 to 35 weight %.
And, as described hard phase, have whole hard phases of following (1) to (3).
(1) the first hard phase of cored structure is arranged, wherein core contains the titanium carbonitride phase, periphery contain (Ti, W, Ta/Nb) CN phase,
(2) the second hard phase of cored structure is arranged, wherein core and periphery contain (Ti, W, Ta/Nb) CN phase,
(3) the 3rd hard phase of phase structure, it comprises the titanium carbonitride phase.
Especially, shown in Figure 2 as described in the present embodiment, titanium carbonitride mutually in, than around contain and more many rich W of W and distribute unevenly mutually.Particularly, when observing the section of (carrying out little structure observation) titanium carbonitride phase, with wire and netted state uneven distribution by TEM.
Therefore, the blade of present embodiment is owing to have the formation of above-mentioned uniqueness, therefore as described later shown in the experimental example, has high abrasion resistance and breakage resistance simultaneously.
In addition, above-mentioned blade for example as shown in Figure 6, is fixed on for example end of steel column retainer 3 by stationary fixture 5.And, use the cutting element 7 on this retainer 3, fixed blade 1 and to have formed, can carry out the cutting of steel etc.
B) then, the manufacture method to the present embodiment blade describes.In addition, be that example describes in this manufacture method that can enumerate the blade that is used for the aftermentioned experiment.
◆ in the present embodiment, at first, carry out the precomminution of TiCN.
Particularly, prepare TiC with 0.5 to 2 μ m average grain diameter
0.5N
0.5Powder and TiC
0.3N
0.7Powder (C/N is than the expression atomic ratio) utilizes ball mill to pulverize 5 hours in alcohol simultaneously two material powders as the material powder of precomminution.
◆ then, TiCN powder and other material powder of described precomminution carried out wet mixed.
Particularly, as shown in table 1 below, prepare the TiC that obtains by precomminution
0.5N
0.5Powder and TiC
0.3N
0.7The TaC powder of the WC powder of powder, average grain diameter 1 to 2 μ m, average grain diameter 1 to 2 μ m, the Mo of average grain diameter 2 to 3 μ m
2The Ni powder of the Co powder of the NbC powder of C powder, average grain diameter 1 to 2 μ m, average grain diameter 2 to 3 μ m and average grain diameter 2 to 3 μ m cooperates the composition of the cooperation shown in these material powder accordings to the form below 1, has prepared seven kinds of mixed-powders of A to G.
Table 1
Then, each mixed-powder of described A to G is utilized ball mill wet mixed 24 hours in alcohol respectively, dry then.
Then, powder that this is dry is configured as briquetting with the exert pressure of 98MPa.
Then, this briquetting is calcined down at following calcination condition (a) to (e) as shown in Figure 7.
(a) in the vacuum environment below 10Pa (V), be warming up to 1200 ℃ from room temperature with 10 ℃/minute speed,
(b) at the time point that is warming up to 1200 ℃, carry out environment and replace change process, wherein, the short time Ar environment that will in the Ar of 35kPa environment, keep 2 minutes keep with vacuum environment below 10Pa in the short time vacuum environment that kept 15 minutes keep, alternately repeat
(c) after above-mentioned environment replaced change process, the speed with 2 ℃/minute in the vacuum environment below 10Pa was warming up to 1350 ℃,
(d) carry out from the intensification of 1350 ℃ of extremely predetermined sintering temperatures (1500 ℃) with 2 ℃/minute speed, and in the nitrogen environment of 1.3kPa, under described sintering temperature, kept 60 minutes,
(e) it is cold to carry out the stove that begins from above-mentioned sintering temperature in the Ar environment below 90kPa.
Comprising that above (a) carries out sintering to the condition of (e) step, polish processing behind the sintering, thus, made and had iso standard: the blade 1 of the cutting tip of SNGN120408 (チ Star プ) shape.
That is, as shown in table 3 below, made the blade of the sample No.1 to 7 corresponding respectively with described seven kinds of mixed-powders.
In addition, in order to compare, as shown in table 3 below, except not carrying out precomminution (sample No.10,11) under the substantially identical condition, except not carrying out that above-mentioned environment in the sintering temperature temperature-rise period replaces (sample No.8,9) under the condition substantially identical the change process and except not carrying out precomminution and environment replaces change process, under the substantially identical condition (sample No.12 to 14), having made the blade of comparative example respectively.
C) then, the cutting evaluation for the blade of the sample No.8 to 14 of the blade of the sample No.1 to 7 of the example of the present invention by above-mentioned manufacture method manufacturing and comparative example describes.
At this, as shown in table 2 below, carry out breakage resistant luer test and wear-resistant test.
(1) breakage resistant luer test
Utilize the stationary fixture screw to be fixed on the top ends of instrument steel cutter head (retainer) on the blade of each sample, obtain cutting element.
And, use this cutting element, under the machining condition of following table 2, carry out the interrupted high-speed cutting test of dry type of steel alloy.In addition, the breakage resistant luer test uses 20 blades of the same race to carry out.
And, examined or check that to impact number of times be 700 times accumulation breakage rate (producing the ratio of the number of damaged blade in 700 times).The result is as shown in table 3 below.
(2) wear-resistant test
Utilize the stationary fixture screw to be fixed on the top ends of instrument steel cutter head (retainer) on the blade of each sample, obtain cutting element.
And, use this cutting element, under the machining condition of following table 2, carry out the interrupted high-speed cutting test of dry type of steel alloy.
And, measure 4 minutes wear of the tool flank amount (V after the processing
BWear extent).The result is as shown in table 3 below.
(3) little structure observation
Use the blade of each sample, carry out tem observation.Particularly, the thickness that makes sample is below the 200 μ m, uses TEM (transmission electron microscope) to take the TEM photo, and it is observed.
And, by this tem observation, confirm to have or not the uneven distribution of W.In addition, use described TEM, the bonding of mensuration blade is the content of middle W mutually.The result is as shown in table 3 below.
In addition, the part of TEM photo is shown among Fig. 8 to Figure 12, and Fig. 8 is the TEM photo (100,000 times) of the sample No.1 of example of the present invention, the TEM photo (200,000 times) that Fig. 9 is the sample No.6 of example of the present invention, the TEM photo (450,000 times) that Figure 10 is the sample No.4 of example of the present invention, the TEM photo (100,000 times) that Figure 11 is the sample No.8 of comparative example, the TEM photo (200,000 times) that Figure 12 is the sample No.13 of comparative example.
(4) composition analysis
By EDS (can arching pushing), ingredient (element) in the blade of each sample No.1 to 7 of the present invention of forming A to G be carried out quantitatively.And the compound that carries out its composition converts.The result is as shown in table 4 below.
Table 2
Table 3
Table 4
Result from aforementioned table 1 to table 4 as can be known, the blade of example of the present invention, particularly the titanium carbonitride of hard phase mutually in, than around contain more many W rich W mutually for example Fig. 8 have the remarkable result that can realize high-wearing feature and breakage resistance simultaneously thus to such uneven distribution shown in Figure 10.In addition, in Fig. 8 to Figure 10, the wire and the netted white line of the rich W phase of expression can be observed, in addition, among Fig. 9, the stratiform hickie of the rich W phase of expression can be observed.
Relative therewith, although the blade mar proof of comparative example is excellent to a certain extent, can not realize high abrasion resistance and breakage resistance simultaneously, therefore not preferred.
Embodiment 2
Prepare the TiC that any all has the average grain diameter of 0.5 to 2 μ m
0.5N
0.5Powder, TiC
0.3N
0.7Powder, TiC
0.15N
0.85Powder (above C/N represents atomic ratio), NbC powder, TaC powder, WC powder, Co powder and Ni powder are as material powder, these material powders are cooperated by the composition of the cooperation shown in the table 5, with ball mill wet mixed 24 hours and dry, then, utilize the exert pressure of 98MPa to be configured as briquetting, with this briquetting at following sintering condition, promptly comprise sintering under the condition of (a) to (e) described step:
(a) speed with 2 ℃/minute is warming up to 1280 ℃ from room temperature in the vacuum environment below 10Pa,
(b) at the time point that is warming up to 1280 ℃, carry out environment and replace change process, wherein, the short time Ar environment that will in the Ar of 35kPa environment, keep 2 minutes keep with vacuum environment below 10Pa in the short time vacuum environment that kept 15 minutes keep, alternately repeat the number of times shown in the table 5 respectively
(c) after above-mentioned environment replaced change process, the speed with 2 ℃/minute in the vacuum environment below 10Pa was warming up to 1420 ℃,
(d) carry out the intensification of the predetermined sintering temperature in the scope with 2 ℃/minute speed, and in the nitrogen environment of 1300Pa, under described sintering temperature, kept 1.5 hours from 1420 ℃ to 1480～1560 ℃,
(e) it is cold to carry out the stove that begins from above-mentioned sintering temperature in the vacuum environment below 10kPa,
Behind the sintering, knife edge part is carried out the processing of boring and grinding of R:0.07mm, made the present embodiment blade 1 to 10 of cutting tip shape thus respectively with iso standard CNMG120412.
In addition, as shown in table 6 for relatively, replace the change process except not carrying out above-mentioned environment in the sintering temperature temperature-rise period, made existing blade 1 to 10 under the substantially identical condition respectively.
About embodiment blade 1 to 10 and the existing blade 1 to 10 that so obtains, the little structure observation result of transmission electron microscope who constitutes the TiCN based ceramic metal of these blades is shown in table 7, the table 8 respectively with bonding analysis result mutually.
Then, blade 1 to 10 and existing blade 1 to 10 about above-mentioned present embodiment, top ends at instrument steel cutter head is used it respectively under the fixing state of stationary fixture screw, carries out the interrupted high-speed cutting test of dry type (common cutting speed is 200m/ minute) of steel alloy under following condition (being called machining condition A):
Be cut material: the length direction of JISSCM440 equidistantly has the pole of 4 road longitudinal furrows
Cutting speed: 300m/ minute
Depth of cut: 1.5mm
Feeding: 0.2mm/rev,
Cutting time: 10 minutes;
Under following condition (being called machining condition B), carry out the dry type continuous high speed cutting test (common cutting speed is 250m/ minute) of carbon steel:
Be cut material: the pole of JISS20C
Cutting speed: 350m/ minute
Depth of cut: 1.0mm
Feeding: 0.2mm/rev,
Cutting time: 20 minutes;
And the dry type continuous high speed cutting test (common cutting speed is 280m/ minute) of under following condition (being called machining condition C), carrying out cast iron:
Be cut material: the pole of JISFC300
Cutting speed: 400m/ minute
Depth of cut: 2.5mm
Feeding: 0.3mm/rev,
Cutting time: 20 minutes,
In any cutting test, all measured the wear of the tool flank width of blade.This results are shown in the table 9.
Table 9
From table 5 to the result shown in 9 as can be seen, the blade 1 to 10 of present embodiment, because the bonding of the TiCN based ceramic metal of each blade of formation contains the W composition with 40 to 60% high-load, and has excellent high-temperature hardness, even therefore with in the thermogenetic high-speed cutting processing of height, also can show good mar proof, relative therewith, in the existing blade 1 to 10, the bonding of each blade mutually in the content ratio of W be 1 to 10% low content, the result can not expect that bonding has excellent high-temperature hardness mutually, therefore particularly promoted, because should be former thereby make and in the time of relatively lacking, just reached service life in the wearing and tearing development of bonding phase described in the high-speed cutting processing.
As mentioned above, the blade of this embodiment, machining under the usual conditions of various steel, cast iron etc. certainly needless to say, even also showing good mar proof in the thermogenetic high-speed cutting processing, can fully satisfy laborsavingization of tackling machining, energy-conservationization and cost degradation more with height.
Embodiment 3
Prepare the TiC that any all has the average grain diameter of 0.5 to 2 μ m
0.5N
0.5Powder, TiC
0.3N
0.7Powder, TiC
0.15N
0.85Powder (above C/N represents atomic ratio), WC powder, TaC powder, NbC powder, ZrC powder, VC powder, Mo
2C powder, Co powder and Ni powder are as material powder, these material powders are cooperated by the composition of the cooperation shown in the table 10, with ball mill wet mixed 24 hours and dry, then, utilize the exert pressure of 98MPa to be configured as briquetting, with this briquetting at following sintering condition, promptly comprise sintering under the condition of (a) to (e) described step:
(a) speed with 2 ℃/minute is warming up to 1280 ℃ from room temperature in the vacuum environment below 10Pa,
(b) at the time point that is warming up to 1280 ℃, carry out environment and replace change process, wherein, the short time Ar environment that will in the Ar of 35kPa environment, keep 2 minutes keep with vacuum environment below 10Pa in the short time vacuum environment that kept 10 minutes keep, alternately repeat the number of times shown in the table 10 respectively
(c) after above-mentioned environment replaced change process, the speed with 2 ℃/minute in the vacuum environment below 10Pa was warming up to 1420 ℃,
(d) carry out the intensification of the predetermined sintering temperature in the scope with 2 ℃/minute speed, and in the nitrogen environment of 1300Pa, under described sintering temperature, kept 1.5 hours from 1420 ℃ to 1480～1560 ℃,
(e) it is cold to carry out the stove that begins from above-mentioned sintering temperature in the vacuum environment below 10kPa,
Behind the sintering, knife edge part is carried out the processing of boring and grinding of R:0.07mm, made the present embodiment blade 1 to 15 of cutting tip shape thus respectively with iso standard CNMG120412.
In addition, as shown in table 11 for relatively, about TiCN powder, except only using above-mentioned TiC as material powder
0.5N
0.5Powder and the above-mentioned environment that does not carry out in the sintering temperature temperature-rise period replace beyond the change process, have made existing blade 1 to 15 under the substantially identical condition respectively.
For embodiment blade 1 to 15 that so obtains and existing blade 1 to 15, the little structure observation result of transmission electron microscope who constitutes the TiCN based ceramic metal of these blades is shown in table 12, the table 13 respectively with bonding analysis result mutually.
In addition, the little structure observation result of transmission electron microscope (10,000 times) who has schematically represented the present embodiment blade among Figure 13.
Then, blade 1 to 15 and existing blade 1 to 15 for above-mentioned present embodiment, top ends at instrument steel cutter head is used it respectively under the fixing state of stationary fixture screw, carries out the interrupted high-speed cutting test of dry type (common cutting speed is 250m/ minute) of carbon steel under following condition (being called machining condition A):
Be cut material: the length direction of JISS20C equidistantly has the pole of 4 road longitudinal furrows
Cutting speed: 380m/ minute
Depth of cut: 1.5mm
Feeding: 0.2mm/rev,
Cutting time: 10 minutes;
Under following condition (being called machining condition B), carry out the dry type continuous high speed cutting test (common cutting speed is 200m/ minute) of steel alloy:
Be cut material: the pole of JISSCM440
Cutting speed: 300m/ minute
Depth of cut: 1mm
Feeding: 0.2mm/rev,
Cutting time: 20 minutes;
Under following condition (being called machining condition C), carry out the dry type continuous high speed cutting test (common cutting speed is 280m/ minute) of cast iron:
Be cut material: the pole of JISFC300
Cutting speed: 380m/ minute
Depth of cut: 2.5mm
Feeding: 0.3mm/rev,
Cutting time: 20 minutes,
In any cutting test, all measured the wear of the tool flank width of blade.This results are shown in the table 14.
Table 14
From table 10 to the result shown in 14 as can be seen, the blade 1 to 15 of present embodiment, since constitute each blade the TiCN based ceramic metal bonding with 40 to 60% contain the W composition at high proportion, and has excellent high-temperature hardness, even therefore with in the thermogenetic high-speed cutting processing of height, also can show good mar proof, relative therewith, in the existing blade 1 to 15, the bonding of each blade mutually in the content ratio of W be 1 to 10% low content, the result can not expect that bonding has excellent high-temperature hardness mutually, therefore particularly promoted, because should be former thereby make and in the time of relatively lacking, just reached service life in the wearing and tearing development of bonding phase described in the high-speed cutting processing.
As mentioned above, the blade of this embodiment, machining under the usual conditions of various steel, cast iron etc. certainly needless to say, even also showing good mar proof in the thermogenetic high-speed cutting processing, can fully satisfy laborsavingization of tackling machining, energy-conservationization and cost degradation more with height.
Embodiment 4
Prepare (the Ti that any all has the average grain diameter of 0.5 to 2 μ m
0.95Nb
0.05) C
0.5N
0.5Powder (raw material A shown in the table 15), (Ti
0.9Nb
0.1) C
0.5N
0.5Powder (the raw material B shown in the table 15), (Ti
0.85Nb
0.15) C
0.5N
0.5Powder (the raw material C shown in the table 15), (Ti
0.9Nb
0.1) C
0.4N
0.6Powder (the raw material D shown in the table 15), (Ti
0.9Nb
0.1) C
0.6N
0.4Powder (the raw material E shown in the table 15) (content ratio in the above material powder is represented atomic ratio), NbC powder, TaC powder, WC powder, Co powder and Ni powder are as material powder, these material powders are cooperated by the composition of the cooperation shown in the table 15, with ball mill wet mixed 24 hours and dry, then, utilize the exert pressure of 98MPa to be configured as briquetting, with this briquetting at following sintering condition, promptly comprise sintering under the condition of (a) to (e) described step:
(a) speed with 2 ℃/minute is warming up to 1280 ℃ from room temperature in the vacuum environment below 10Pa,
(b) at the time point that is warming up to 1280 ℃, carry out environment and replace change process, wherein, the short time Ar environment that will in the Ar of 35kPa environment, keep 2 minutes keep with vacuum environment below 10Pa in the short time vacuum environment that kept 10 minutes keep, alternately repeat the number of times shown in the table 15 respectively
(c) after above-mentioned environment replaced change process, the speed with 2 ℃/minute in the vacuum environment below 10Pa was warming up to 1420 ℃,
(d) carry out the intensification of the predetermined sintering temperature in the scope with 2 ℃/minute speed, and in the nitrogen environment of 1300Pa, under described sintering temperature, kept 1.5 hours from 1420 ℃ to 1480～1560 ℃,
(e) it is cold to carry out the stove that begins from above-mentioned sintering temperature in the vacuum environment below 10kPa,
Behind the sintering, knife edge part is carried out the processing of boring and grinding of R:0.07mm, made the present embodiment blade 1 to 10 of cutting tip shape thus respectively with iso standard CNMG120412.
In addition, shown in table 16 for relatively, the TiC that has the average grain diameter of 1 μ m except use
0.5N
0.5Powder (C/N represents with atomic ratio) replace above-mentioned raw materials A to E as material powder, do not carry out above-mentioned environment in the sintering temperature temperature-rise period simultaneously and replace beyond the change process, made existing blade 1 to 10 under the substantially identical condition respectively.
For embodiment blade 1 to 10 that so obtains and existing blade 1 to 10, the little structure observation result of ceramic-metallic transmission electron microscope who constitutes these blades is shown in table 17, the table 18 respectively with bonding analysis result mutually.
In addition, schematically represented the little structure observation result of the ceramic-metallic transmission electron microscope of present embodiment (10,000 times) among Figure 14.
Then, blade 1 to 10 and existing blade 1 to 10 for above-mentioned present embodiment, top ends at instrument steel cutter head is used it respectively under the fixing state of stationary fixture screw, carries out the dry type continuous high speed cutting test (common cutting speed is 200m/ minute) of steel alloy under following condition (being called machining condition A):
Be cut material: the pole of JISSCM440
Cutting speed: 350m/ minute
Depth of cut: 1mm
Feeding: 0.2mm/rev,
Cutting time: 20 minutes;
Under following condition (being called machining condition B), carry out the interrupted high-speed cutting test of dry type (common cutting speed is 250m/ minute) of carbon steel:
Be cut material: the length direction of JISS20C equidistantly has the pole of 4 road ditches
Cutting speed: 350m/ minute
Depth of cut: 1.5mm
Feeding: 0.2mm/rev,
Cutting time: 10 minutes;
Under following condition (being called machining condition C), carry out the dry type continuous high speed cutting test (common cutting speed is 280m/ minute) of cast iron:
Be cut material: the pole of JISFC300
Cutting speed: 420m/ minute
Depth of cut: 2.5mm
Feeding: 0.3mm/rev,
Cutting time: 20 minutes,
In any cutting test, all measured the wear of the tool flank width of blade.This results are shown in the table 19.
Table 19
From table 15 to the result shown in 19 as can be seen, the blade 1 to 10 of present embodiment, since the ceramic-metallic bonding that constitutes each blade with 40 to 60% contain the W composition at high proportion, and has excellent high-temperature hardness, therefore the core of hard phase has very high high temperature hardness owing to containing the Nb composition, simultaneously, even in the thermogenetic high-speed cutting processing of height, also can show good mar proof, relative therewith, in the existing blade 1 to 10, the bonding of each blade mutually in the content ratio of W be 1 to 10% low content, the result can not expect that bonding has excellent high-temperature hardness mutually, is therefore particularly promoted in the wearing and tearing development of bonding phase described in the high-speed cutting processing, because should be former thereby make just reached service life in the time of relatively lacking.
As mentioned above, the blade of this embodiment, machining under the usual conditions of various steel, cast iron etc. certainly needless to say, even also showing good mar proof in the thermogenetic high-speed cutting processing, can fully satisfy laborsavingization of tackling machining, energy-conservationization and cost degradation more with height.
Embodiment 5
Prepare (the Ti that any all has the average grain diameter of 0.5 to 2 μ m
0.85Nb
0.05Zr
0.1) C
0.5N
0.5Powder (raw material shown in the table 20 a), (Ti
0.8Nb
0.1Zr
0.1) C
0.5N
0.5Powder (the raw material b shown in the table 20), (Ti
0.75Nb
0.15Zr
0.1) C
0.5N
0.5Powder (the raw material c shown in the table 20), (Ti
0.85Nb
0.1Zr
0.05) C
0.5N
0.5Powder (the raw material d shown in the table 20), (Ti
0.75Nb
0.1Zr
0.15) C
0.5N
0.5Powder (the raw material e shown in the table 20), (Ti
0.8Nb
0.1Zr
0.1) C
0.4N
0.6Powder (the raw material f shown in the table 20) and (Ti
0.8Nb
0.1Zr
0.1) C
0.6N
0.4Powder (the raw material g shown in the table 20) (content ratio in the above material powder is represented atomic ratio), NbC powder, TaC powder, WC powder, Co powder and Ni powder are as material powder, these material powders are cooperated by the composition of the cooperation shown in the table 20, with ball mill wet mixed 24 hours and dry, then, utilize the exert pressure of 98MPa to be configured as briquetting, with this briquetting at following sintering condition, promptly comprise sintering under the condition of (a) to (e) described step:
(a) speed with 2 ℃/minute is warming up to 1280 ℃ from room temperature in the vacuum environment below 10Pa,
(b) at the time point that is warming up to 1280 ℃, carry out environment and replace change process, wherein, the short time Ar environment that will in the Ar of 35kPa environment, keep 2 minutes keep with vacuum environment below 10Pa in the short time vacuum environment that kept 10 minutes keep, alternately repeat the number of times shown in the table 20 respectively
(c) after above-mentioned environment replaced change process, the speed with 2 ℃/minute in the vacuum environment below 10Pa was warming up to 1420 ℃,
(d) carry out the intensification of the predetermined sintering temperature in the scope with 2 ℃/minute speed, and in the nitrogen environment of 1300Pa, under described sintering temperature, kept 1.5 hours from 1420 ℃ to 1480～1560 ℃,
(e) it is cold to carry out the stove that begins from above-mentioned sintering temperature in the vacuum environment below 10kPa,
Behind the sintering, knife edge part is carried out the processing of boring and grinding of R:0.07mm, made the present embodiment blade 1 to 10 of cutting tip shape thus respectively with iso standard CNMG120412.
In addition, shown in table 21 for relatively, the TiC that has the average grain diameter of 1 μ m except use
0.5N
0.5Powder (C/N represents with atomic ratio) replace above-mentioned raw materials a to f as material powder, do not carry out above-mentioned environment in the sintering temperature temperature-rise period simultaneously and replace beyond the change process, made existing blade 1 to 10 under the substantially identical condition respectively.
About embodiment blade 1 to 10 and the existing blade 1 to 10 that so obtains, the little structure observation result of ceramic-metallic transmission electron microscope who constitutes these blades is shown in table 22, the table 23 respectively with bonding analysis result mutually.
In addition, schematically represented the little structure observation result of the ceramic-metallic transmission electron microscope of present embodiment (10,000 times) among Figure 15.
Then, blade 1 to 10 and existing blade 1 to 10 about above-mentioned present embodiment, top ends at instrument steel cutter head is used it respectively under the fixing state of stationary fixture screw, carries out the dry type continuous high speed cutting test (common cutting speed is 200m/ minute) of steel alloy under following condition (being called machining condition A):
Be cut material: the pole of JISSCM440
Cutting speed: 350m/ minute
Depth of cut: 1mm
Feeding: 0.2mm/rev,
Cutting time: 20 minutes;
Under following condition (being called machining condition B), carry out the interrupted high-speed cutting test of dry type (common cutting speed is 250m/ minute) of carbon steel:
Be cut material: the length direction of JISS20C equidistantly has the pole of 4 road ditches
Cutting speed: 380m/ minute
Depth of cut: 1.5mm
Feeding: 0.2mm/rev,
Cutting time: 10 minutes;
Under following condition (being called machining condition C), carry out the dry type continuous high speed cutting test (common cutting speed is 280m/ minute) of cast iron:
Be cut material: the pole of JISFC300
Cutting speed: 400m/ minute
Depth of cut: 2.5mm
Feeding: 0.3mm/rev,
Cutting time: 20 minutes,
In any cutting test, all measured the wear of the tool flank width of blade.This results are shown in the table 24.
Table 24
Can be clear and definite from table 20 to the result shown in 24, the blade 1 to 10 of present embodiment, since the ceramic-metallic bonding that constitutes each blade with 40 to 60% contain the W composition at high proportion, and has excellent high-temperature hardness, therefore the core of hard phase is because demonstration excellent wetting capacity when containing Nb composition and Zr composition and having very high high temperature hardness and sintering, simultaneously, even in the thermogenetic high-speed cutting processing of height, do not produce chip yet, show good mar proof, relative therewith, in the existing blade 1 to 10, the bonding of each blade mutually in the content ratio of W be 1 to 10% low content, the result can not expect that bonding has excellent high-temperature hardness mutually, therefore particularly promoted, because should be former thereby make and in the time of relatively lacking, just reached service life in the wearing and tearing development of bonding phase described in the high-speed cutting processing.
As mentioned above, the blade of this embodiment, machining under the usual conditions of various steel, cast iron etc. certainly needless to say, even also showing good mar proof in the thermogenetic high-speed cutting processing, can fully satisfy laborsavingization of tackling machining, energy-conservationization and cost degradation more with height.
Embodiment 6
A) at first, the blade to present embodiment describes.
Shown in Figure 5 as described above, the blade 1 of present embodiment is the cutting tip of sintered body that comprises the shape of iso standard: SNGN120408.
This blade 1, shown in Figure 1 as described, constitute by the bonding little tissue (containing unavoidable impurities) mutually that exists around comprising hard phase (hard particles) and covering it.Wherein, hard comprise mutually (Ti, W, Ta/Nb) CN and titanium carbonitride, bonding is a principal component with W and Co and/or Ni.
Sintered body as described blade 1 is formed, about Ti and, Nb and/or Ta and W, the value that value that value that converts by carbonitride with Ti and Nb and/or Ta convert by carbide and W convert by carbide close quantifier, all contain 70 to 95 weight % with respect to blade.Wherein, the value of W to convert by carbide all contains 20 to 35 weight % with respect to little tissue.
In addition, Ti is all with respect to little tissue, and the value that converts by carbonitride contains 45 to 60 weight %, simultaneously, Nb and/or Ta, the value that converts in carbide contains 5 to 10 weight %.
In addition, hard mutually in, by the value that carbide converts, all contain 40 to 65 weight % in W with respect to little tissue, simultaneously, contain the surplus of W in mutually in bonding.
And, as the hard phase, have whole hard phases of for example following (1) to (3).
(1) the first hard phase of cored structure is arranged, wherein core contains the titanium carbonitride phase, periphery contain (Ti, W, Ta/Nb) CN phase,
(2) the second hard phase of cored structure is arranged, wherein core and periphery all contain (Ti, W, Ta/Nb) CN phase,
(3) the 3rd hard phase of phase structure, it comprises the titanium carbonitride phase.
Therefore, the blade of present embodiment 1 is owing to have the formation of above-mentioned uniqueness, therefore as described later shown in the experimental example, has high abrasion resistance and breakage resistance simultaneously.
In addition, above-mentioned blade 1 as shown in Figure 6, is fixed on for example top of steel column retainer 3 by stationary fixture 5.And, use the cutting element 7 on this retainer 3, fixed blade 1 and to have formed, can carry out the cutting of steel etc.
B) then, the manufacture method to present embodiment blade 1 describes.In addition, describe as an example in this manufacture method that can enumerate the blade that is used for the aftermentioned experiment.
◆ in the present embodiment, at first, carry out the wet mixed of material powder.
Particularly, as shown in table 25 below, the TiC of preparation average grain diameter 0.5 to 2 μ m
0.5N
0.5The TiC of powder, average grain diameter 0.5 to 2 μ m
0.3N
0.7The Ni powder of the Co powder of the NbC powder of the TaC powder of the WC powder of powder, average grain diameter 1 to 2 μ m, average grain diameter 1 to 2 μ m, average grain diameter 1 to 2 μ m, average grain diameter 2 to 3 μ m, average grain diameter 2 to 3 μ m, cooperation shown in these material powder accordings to the form below 25 composition is cooperated, prepared four kinds of mixed-powders of A to D.
Table 25
Then, each powder of described A to D is utilized ball mill wet mixed 24 hours in alcohol respectively, dry then.
Then, utilize the exert pressure of 98MPa to be configured as briquetting in this dried powder.
Then, this briquetting is calcined down at following calcination condition (a) to (e) as shown in figure 16.
(a) speed with 10 ℃/minute is warming up to 1200 ℃ from room temperature in the vacuum environment below 10Pa (V),
(b) be warming up to 1200 ℃ of (medium temperatures: in addition, medium temperature also can adopt 1200 to 1250 ℃) after, carry out environment and replace change process, wherein, the short time Ar environment that will in the Ar of 35kPa environment, keep 2 minutes keep with vacuum environment below 10Pa in the short time vacuum environment that kept 15 minutes keep, alternately repeat mutually
(c) after above-mentioned environment replaced change process, the speed with 2 ℃/minute in the vacuum environment below 10Pa was warming up to 1350 ℃,
(d) carry out from the intensification of 1350 ℃ of extremely predetermined sintering temperatures (1500 ℃) with 2 ℃/minute speed, and in the nitrogen environment of 1.3kPa, under described sintering temperature, kept 60 minutes,
(e) it is cold to carry out the stove that begins from above-mentioned sintering temperature in the Ar environment below 90kPa.
Comprising above (a) sintering to the condition of (e) step, polish processing behind the sintering, thus, made and had iso standard: the blade 1 of the cutting tip shape of SNGN120408.
That is, as shown in table 26 below, made the blade of the sample No.1 to 4 corresponding respectively with described four kinds of mixed-powders.
In addition, as shown in table 26 below for relatively, except that the medium temperature difference, under the substantially identical condition (sample No.5 to 8), made the blade of comparative example respectively.
Table 26
C) then, composition analysis and the cutting evaluation for the blade of the sample No.5 to 8 of the blade of the sample No.1 to 4 of the present embodiment by above-mentioned manufacture method manufacturing and comparative example describes.
(1) composition analysis
By EDS (can arching pushing), ingredient (element) in the blade (sintered body) of the sample No.5 to 8 of each sample No.1 to 4 of present embodiment and comparative example be carried out quantitatively.And the compound that carries out its composition converts.The result is shown in following table 27 and table 28.
Table 27
Table 28
In addition, by using analysis and the EDS of TEM (transmission electron microscope), analyzed the composition of the bonding phase of blade.Its result is shown in following table 29.
Table 29
◆ in addition, obtain its content for W.The result is shown in following table 30.
At this, with respect to the W amount of all bonding of blade in mutually, with respect to the W amount of all hard of blade in mutually, with respect to the bonding of the total W amount W amount in mutually, respectively by following formula＜1 〉～＜3 obtain.In addition, do not use scaled value in the calculating of W amount etc. and be to use the amount (weight %) of element.
● the W amount [weight %] in boning mutually=(W in the bonding phase composition) * (Co+Ni in the sintered body composition)/(Co+Ni in the bonding phase composition) ...＜1 〉
● W amount [weight %]=(the W amount in sintered body) of hard in mutually-(bonding mutually in W amount) ...＜2 〉
● with respect to W amount [weight %] in mutually of the bonding of total W amount=(bonding mutually in W amount)/(total W amount) ...＜3 〉
Table 30
(2) breakage resistant luer test
Utilize the stationary fixture screw to be fixed on the top ends of the cutter head (retainer) of instrument steel on the blade of each sample, obtain cutting element.
And, use this cutting element, under the machining condition of following table 31, carry out the interrupted high-speed cutting test of dry type of steel alloy.In addition, the breakage resistant luer test uses 20 blades of the same race to carry out.
And, examined or check that to impact number of times be 700 times accumulation breakage rate (producing the ratio of the number of damaged blade in 700 times).The result is shown in following table 32.
(3) wear-resistant test
Utilize the stationary fixture screw to be fixed on the top ends of the cutter head (retainer) of instrument steel on the blade of each sample, obtain cutting element.
And, use this cutting element, under the machining condition of following table 31, carry out the interrupted high-speed cutting test of dry type of steel alloy.
And, measure 4 minutes wear of the tool flank amount (V after the processing
BWear extent).The result is shown in following table 32.
Table 31
Table 32
Table 25 is to shown in 32 as described above, 40 to 65 weight % in the blade of present embodiment, particularly blade among the contained W be included in hard mutually in, simultaneously surplus be included in bonding mutually in, therefore have the remarkable result that can realize high abrasion resistance and breakage resistance simultaneously.
In addition, the present invention is not subjected to any restriction of previous embodiment, and the present invention can implement in every way in not departing from the scope of the present invention.
Claims (6)
1. cermet insert,
Have and comprise hard mutually and mutually the little tissue of boning,
Form as sintered body, about Ti; And Nb and/or Ta; And W, the value that value that value that converts by carbonitride with described Ti and described Nb and/or Ta convert by carbide and described W convert by carbide close quantifier, all with respect to described little tissue, contain 70 to 95 weight %, wherein, described W all is 15 to 35 weight % by the value that carbide converts with respect to little tissue, simultaneously, contain Co and/or Ni
Wherein,, have in following (1) to (3) one or more, still, do not comprise the situation of following separately (2) as described hard phase:
(1) the first hard phase of cored structure is arranged, wherein core contains the titanium carbonitride phase, and periphery contains Ti and W; With the composite carbon nitride of Ta and/or Nb mutually, following table be shown (Ti, W, Ta/Nb) CN phase,
(2) the second hard phase of cored structure is arranged, wherein core and periphery all contain (Ti, W, Ta/Nb) CN phase,
(3) the 3rd hard phase of phase structure, it comprises the titanium carbonitride phase,
And, described titanium carbonitride mutually in, than around contain and more many rich W of W and distribute unevenly mutually.
2. cermet insert according to claim 1, wherein, in at least one little tissue of the surface of described cermet insert and section, described titanium carbonitride mutually in, described rich W with wire and netted at least a state uneven distribution.
3. cermet insert according to claim 1 and 2, wherein, described titanium carbonitride mutually in, described rich W is with at least a state uneven distribution in stratiform, the cylindric and prism-shaped.
4. cermet insert according to claim 1 and 2 wherein, in described hard phase and/or in boning mutually, also contains Mo.
5. cermet insert according to claim 1 and 2, wherein, described bonding mutually in, all also contain the W of 40 to 60 weight % mutually with respect to described bonding.
6. a cutting element wherein, has aforesaid right requirement 1 to 5 each described cermet insert in retainer.
Applications Claiming Priority (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005173463A JP4569767B2 (en) | 2005-06-14 | 2005-06-14 | Titanium carbonitride-based cermet throwaway tip that exhibits excellent wear resistance in high-speed cutting with high heat generation |
| JP173463/2005 | 2005-06-14 | ||
| JP259169/2005 | 2005-09-07 | ||
| JP259170/2005 | 2005-09-07 | ||
| JP259171/2005 | 2005-09-07 | ||
| JP303096/2005 | 2005-10-18 | ||
| JP303095/2005 | 2005-10-18 |
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| Publication Number | Publication Date |
|---|---|
| CN101208166A CN101208166A (en) | 2008-06-25 |
| CN100569421C true CN100569421C (en) | 2009-12-16 |
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ID=37643148
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200680019833A Expired - Fee Related CN100574944C (en) | 2005-06-14 | 2006-06-13 | Cermet insert and cutting element |
| CNB2006800213497A Active CN100569421C (en) | 2005-06-14 | 2006-06-13 | Cermet insert and cutting element |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200680019833A Expired - Fee Related CN100574944C (en) | 2005-06-14 | 2006-06-13 | Cermet insert and cutting element |
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| Country | Link |
|---|---|
| JP (1) | JP4569767B2 (en) |
| CN (2) | CN100574944C (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105817619A (en) * | 2016-06-03 | 2016-08-03 | 广东工业大学 | Multistage composite cermet, preparation method thereof and shield cutter |
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| JP4695960B2 (en) * | 2005-10-18 | 2011-06-08 | 日本特殊陶業株式会社 | Cermet inserts and cutting tools |
| EP1892051A4 (en) | 2005-06-14 | 2014-10-01 | Ngk Spark Plug Co | Cermet insert and cutting tool |
| US8313842B2 (en) | 2007-02-26 | 2012-11-20 | Kyocera Corporation | Ti-based cermet |
| JP5217417B2 (en) * | 2007-12-25 | 2013-06-19 | 三菱マテリアル株式会社 | Titanium carbonitride-based cermet cutting tool with excellent wear resistance |
| SE534073C2 (en) * | 2008-12-18 | 2011-04-19 | Seco Tools Ab | cermet |
| JP4690475B2 (en) * | 2009-03-24 | 2011-06-01 | 住友電気工業株式会社 | Cermet and coated cermet tools |
| CN102304657B (en) * | 2011-09-26 | 2012-10-24 | 四川大学 | Molybdenum-free Ti (C, N)-based cermet wear resistant and corrosion resistant material and preparation method thereof |
| CN103114233B (en) * | 2013-03-13 | 2015-04-15 | 成都广正科技有限公司 | Coating gradient cemented carbide tool material |
| CN103521770B (en) * | 2013-09-22 | 2015-10-28 | 成都工具研究所有限公司 | TiCN based ceramic metal |
| JP6178689B2 (en) * | 2013-09-30 | 2017-08-09 | 株式会社アライドマテリアル | Tungsten heat resistant alloy, friction stir welding tool, and manufacturing method |
| US10208365B2 (en) * | 2014-03-19 | 2019-02-19 | Tungaloy Corporation | Cermet tool |
| JP5807851B1 (en) * | 2014-04-10 | 2015-11-10 | 住友電気工業株式会社 | Cermets and cutting tools |
| DE102016011096B3 (en) * | 2016-09-15 | 2018-02-15 | H. C. Starck Tungsten GmbH | Novel tungsten carbide powder and its production |
| KR102224139B1 (en) * | 2017-03-29 | 2021-03-08 | 교세라 가부시키가이샤 | Cutting insert and cutting tool equipped with it |
| JP7092867B2 (en) * | 2018-03-20 | 2022-06-28 | 京セラ株式会社 | Tools and cutting tools equipped with them |
| EP3795706B1 (en) * | 2018-05-15 | 2024-04-24 | Sumitomo Electric Industries, Ltd. | Cermet, cutting tool containing same, and method for producing cermet |
| CN108950342B (en) * | 2018-07-24 | 2020-09-01 | 三峡大学 | Ti (C, N) -based cermet and preparation method thereof |
| JP7411781B2 (en) * | 2020-03-25 | 2024-01-11 | 京セラ株式会社 | Inserts and cutting tools equipped with them |
| CN111647787B (en) * | 2020-06-16 | 2021-05-25 | 四川神工钨钢刀具有限公司 | TiCN-based particle metal ceramic cutter and preparation method thereof |
| CN114231780B (en) * | 2021-11-08 | 2022-12-23 | 成都美奢锐新材料有限公司 | Cermet material special for cigar scissors and preparation method thereof |
| CN115710665B (en) * | 2022-11-21 | 2023-10-31 | 恒普(宁波)激光科技有限公司 | Ceramic reinforced composite material, application thereof, additive manufacturing method and product |
| CN116162838B (en) * | 2023-04-26 | 2023-06-30 | 崇义章源钨业股份有限公司 | Metal ceramic and preparation method thereof |
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| JPS60106938A (en) * | 1983-11-14 | 1985-06-12 | Hitachi Choko Kk | Tough cermet |
| JPH08170141A (en) * | 1994-10-20 | 1996-07-02 | Mitsubishi Materials Corp | Corrosion resistant cermet material excellent in wear resistance and toughness |
| JPH10110234A (en) * | 1996-10-07 | 1998-04-28 | Mitsubishi Materials Corp | Cutting tool mode of carbo-nitrided titanium cermet excellent in chipping resistance |
| JP2002263940A (en) * | 2001-03-07 | 2002-09-17 | Mitsubishi Materials Corp | Face milling cutter tool with throwaway tip showing superior chipping resistance in high-speed cutting |
-
2005
- 2005-06-14 JP JP2005173463A patent/JP4569767B2/en active Active
-
2006
- 2006-06-13 CN CN200680019833A patent/CN100574944C/en not_active Expired - Fee Related
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105817619A (en) * | 2016-06-03 | 2016-08-03 | 广东工业大学 | Multistage composite cermet, preparation method thereof and shield cutter |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101189090A (en) | 2008-05-28 |
| CN100574944C (en) | 2009-12-30 |
| CN101208166A (en) | 2008-06-25 |
| JP2006346776A (en) | 2006-12-28 |
| JP4569767B2 (en) | 2010-10-27 |
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