CN102465257B - Hard coating layer plays the excellent resistance to surface-coated cutting tool collapsing cutter - Google Patents
Hard coating layer plays the excellent resistance to surface-coated cutting tool collapsing cutter Download PDFInfo
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- 238000005520 cutting process Methods 0.000 title claims abstract description 31
- 239000011247 coating layer Substances 0.000 title claims abstract description 25
- 239000010410 layer Substances 0.000 claims abstract description 172
- 239000013078 crystal Substances 0.000 claims abstract description 101
- 230000008020 evaporation Effects 0.000 claims abstract description 27
- 238000001704 evaporation Methods 0.000 claims abstract description 27
- 150000001875 compounds Chemical class 0.000 claims abstract description 9
- 239000010936 titanium Substances 0.000 claims description 32
- 238000009826 distribution Methods 0.000 claims description 16
- 238000005259 measurement Methods 0.000 claims description 15
- 238000010276 construction Methods 0.000 claims description 14
- 238000000227 grinding Methods 0.000 claims description 13
- 229910052593 corundum Inorganic materials 0.000 claims description 6
- 239000010431 corundum Substances 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 241000446313 Lamella Species 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- PIZYHTQSHRQOBI-UHFFFAOYSA-N [C].O=[N] Chemical compound [C].O=[N] PIZYHTQSHRQOBI-UHFFFAOYSA-N 0.000 claims description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 3
- 150000004767 nitrides Chemical class 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 claims description 2
- 239000000956 alloy Substances 0.000 claims description 2
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 2
- 230000015572 biosynthetic process Effects 0.000 abstract description 5
- 238000012545 processing Methods 0.000 abstract description 4
- 239000011248 coating agent Substances 0.000 description 53
- 238000000576 coating method Methods 0.000 description 53
- 239000000203 mixture Substances 0.000 description 22
- 239000012298 atmosphere Substances 0.000 description 21
- 239000000843 powder Substances 0.000 description 21
- 238000006243 chemical reaction Methods 0.000 description 18
- 230000000694 effects Effects 0.000 description 12
- 238000003754 machining Methods 0.000 description 12
- 239000007789 gas Substances 0.000 description 11
- 239000000376 reactant Substances 0.000 description 11
- 238000011068 loading method Methods 0.000 description 8
- 229910000831 Steel Inorganic materials 0.000 description 7
- 238000010586 diagram Methods 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 239000010959 steel Substances 0.000 description 7
- 239000004575 stone Substances 0.000 description 7
- 229910001018 Cast iron Inorganic materials 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 239000002245 particle Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- 238000005229 chemical vapour deposition Methods 0.000 description 3
- 229910052739 hydrogen Inorganic materials 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 238000007747 plating Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 230000015556 catabolic process Effects 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000006731 degradation reaction Methods 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000003245 working effect Effects 0.000 description 2
- 229910001149 41xx steel Inorganic materials 0.000 description 1
- 229910018575 Al—Ti Inorganic materials 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000000498 ball milling Methods 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 239000012188 paraffin wax Substances 0.000 description 1
- 230000011218 segmentation Effects 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
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- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
The invention provides a kind of resistance to surface-coated cutting tool collapsing cutter that hard coating layer performance is excellent in the processing of high speed heavy cut.On the surface of tool base, form Ti compound layer as (a) lower layer evaporation, as the formation of (b) upper layer evaporation, there is dull and stereotyped Polygons (comprising smooth hexagon) and the α type Al of grain structure structure also containing Ti of perpendicular long shape
2o
3surface-coated cutting tool in, in the crystal grain of upper layer, count the inside of the crystal grain of more than 60% at area ratio, by least more than one, have the morphotic crystal lattice interface of lattice point by the constituting atom represented with ∑ 3 and split.
Description
Technical field
The present invention relates to a kind of surface-coated cutting tool (hereinafter referred to as coating tool), even if it is in adjoint high heating and under the high speed heavy cut condition of blade effect high loading, carry out various steel or cast iron etc. be cut the machining of material time, hard coating layer also can not produce and collapse cutter, plays excellent cutting ability in life-time service.
Background technology
In the past, be known to following coating tool: on the surface of the matrix (below these being referred to as tool base) be made up of wolfram varbide (representing with WC below) base cemented carbide or titanium carbonitride (representing with TiCN below) based ceramic metal, evaporation forms the lower layer that is made up of Ti compound layer and by α type Al
2o
3layer form upper layer as in the coating tool of hard coating layer,
About upper layer, use field emission type scanning electronic microscope and Electron Back-Scattered Diffraction image device, one by one electron rays is irradiated to the crystal grain be present in the measurement range in surface grinding face, measure the angle that each normal forming crystal face of the crystal grain be made up of hexagonal system lattice is crossing with the normal in described surface grinding face, the mutual crystal orientation relation of neighboring die is calculated by this measurement result, calculate each constituting atom forming interface has the lattice point (constituting atom has lattice point) of 1 constituting atom each other distribution at described crystal grain, with ∑ N+1 represent described constituting atom have to exist between lattice point N number of (wherein, N be corundum type close-packed hexagonal crystallographic system crystalline structure on more than 2 even number, but from when the upper limit of N being set to 28 on distribution frequency, there is not even number 4, 8, 14, 24 and 26) when the constituting atom of the lattice point of not total constituting atom has lattice point form,
Representing that the constituting atom that each ∑ N+1 accounts for the distribution proportion of ∑ N+1 entirety has in lattice point distribution plan, there is climax in ∑ 3 place, and by represent distribution proportion that described ∑ 3 accounts for ∑ N+1 entirety be 60 ~ 80% constituting atom have the α type Al of lattice point distribution plan
2o
3layer forms upper layer, and is known to this coating tool and plays in high rate intermittent machining and excellent resistance toly collapse cutter.
Further, for described coating tool, it is also known that by the α type (Al, Ti) on a small quantity containing Ti
2o
3layer (hereinafter referred to as AlTiO layer in the past) forms the coating tool (hereinafter referred to as coating tool in the past) of its upper layer, and, known this coating tool was identical with described in the past, play excellent resistance toly to collapse cutter in high rate intermittent machining.
Patent documentation 1: Japanese Patent Publication 2006-198735 publication
Patent documentation 2: Japanese Patent Publication 2006-289556 publication
The high performance of topping machanism is remarkable in recent years, be strongly required saving labourization and energy-saving and the cost degradation of machining on the other hand, become with this, the trend of machining high speed more, but present situation is as follows: in above-mentioned coating tool in the past, when using in high-speed and continuous is cut or high rate intermittent cuts, upper layer possesses excellent hot strength, excellent impact resistance, therefore can prevent from collapsing excellence in the generation this point such as cutter, but form the described α type Al of the upper layer of hard coating layer
2o
3layer, the described layer of AlTiO in the past cannot meet hot strength and surface texture, therefore by with Gao Re and to blade effect high loading, under more high-speed condition, carry out heavy cut add man-hour, easily produce and collapse cutter, as reason, reach work-ing life in the short period of time.
So, the present inventors are for above-mentioned viewpoint, and particularly in the heavy cut processing under more high-speed condition, hard coating layer can not produce and collapse cutter, and the structure of the upper layer that can play excellent cutting ability in life-time service is studied, result draws following opinion.
A the upper layer be made up of AlTiO layer in the past of () above-mentioned coating tool in the past, if such as use common chemical evaporation plating device, proceeds as follows:
As the 1st stage, under the following conditions, namely
Reactant gases composition (capacity %):
AlCl
3：2.3～4％、
TiCl
4：0.02～0.13％、
CO
2：1～5％、
HCl：1.5～3％、
H
2S：0.05～0.2％、
H
2: residue,
Reaction atmosphere temperature: 750 ~ 900 DEG C,
Reaction atmosphere pressure: 6 ~ 10kPa,
On the surface of the Ti compound layer as lower layer,
Formation meets composition formula: (Al
1-Xti
x)
2o
3, (wherein, with atomic ratio measuring, X:0.005 ~ 0.05), Al-Ti composite oxides core (hereinafter referred to as the AlTiO core) film of the average thickness preferably with 20 ~ 200nm (0.02 ~ 0.2 μm),
Then, so that heating atmosphere is being become pressure: the hydrogen atmosphere of 3 ~ 13kPa, and by under the condition of heating atmosphere temperature to 1100 ~ 1200 DEG C, described AlTiO core film is implemented to the state of heat treated, as the 2nd stage,
Reactant gases composition (capacity %):
AlCl
3：2.3～4％、
TiCl
4：0.02～0.13％、
CO
2：3～8％、
HCl：1.5～3％、
H
2S：0.05～0.2％、
H
2: residue,
Reaction atmosphere temperature: 1020 ~ 1050 DEG C,
Reaction atmosphere pressure: 6 ~ 10kPa
Condition under carry out evaporation, then formed have Ti composition account for its total amount with Al composition containing proportional be the layer of AlTiO in the past of the composition of 0.005 ~ 0.05 (being wherein atomic ratio), and, if when by field emission type scanning electronic microscope, to this, AlTiO layer carries out structure observation in the past, there is the weave construction be made up of following crystal grain, as shown in (a) of Fig. 2, when observing in the face perpendicular to thickness direction, described crystal grain is fine Polygons, and as shown in (b) of Fig. 2, when observing in the face being parallel to thickness direction, exist pyramidal concavo-convex on layer surface, described crystal grain has perpendicular long shape (hereinafter referred to as " concave-convex polygonal erects long shape ") on thickness direction.
B () on the other hand, the Ti compound layer of the lower layer as hard coating layer is used common chemical evaporation plating device, is proceeded as follows:
First, as the 1st stage,
(first) reactant gases composition (capacity %):
AlCl
3：1～5％、
CO
2：2～6％、
HCl：1～5％、
H
2S：0.25～0.75％、
H
2: residue,
(second) reaction atmosphere temperature: 960 ~ 1010 DEG C,
(the third) reaction atmosphere pressure: 6 ~ 10kPa
Condition under carry out the evaporation in the 1st stage after,
Then, as the 2nd stage, in following condition, namely
(first) reactant gases composition (capacity %):
AlCl
3：6～10％、
TiCl
4：0.05～0.6％
CO
2：4～8％、
HCl：3～5％、
H
2S：0～0.05％、
H
2: residue,
(second) reaction atmosphere temperature: 920 ~ 1000 DEG C,
(the third) reaction atmosphere pressure: 6 ~ 10kPa,
Carry out evaporation, form the upper layer be made up of the alpha-type aluminum oxide layer (hereinafter referred to as " upgrading AlTiO layer ") of the Ti containing 2 ~ 15 μm of average thickness,
The upgrading AlTiO layer then formed under this condition, have Ti composition account in this layer with the total amount of Al composition containing the proportional composition meeting 0.002 ~ 0.01 (wherein for atomic ratio).
(c) and, field emission type scanning electronic microscope is used to carry out structure observation to above-mentioned upgrading AlTiO layer, there is the weave construction be made up of following crystal grain, as shown in (a) of Fig. 1, when observing in the face perpendicular to thickness direction, described crystal grain is the dull and stereotyped Polygons of Large stone, and, as shown in (b) of Fig. 1, when observing in the face being parallel to thickness direction, layer surface is almost smooth, and described crystal grain has perpendicular long shape (hereinafter referred to as " dull and stereotyped Polygons erects long shape ") on thickness direction.
Especially following weave construction is formed: when evaporation forms described upgrading AlTiO layer, if with the evaporation condition limited further (such as, by the H in the reactant gases in the 1st stage
2s is set to 0.50 ~ 0.75 capacity %, and reaction atmosphere temperature is set to 980 ~ 1000 DEG C, in addition, by the TiCl in the reactant gases in the 2nd stage
4be set to 0.05 ~ 0.2 capacity %, H
2s is 0 ~ 0.03 capacity %, reaction atmosphere temperature is set to the condition of 960 ~ 980 DEG C) carry out evaporation, then as shown in (c) of Fig. 1, when observing in the face perpendicular to thickness direction, crystal grain is the smooth hexagon of Large stone, and, when observing in the face being parallel to thickness direction, identical with shown in (b) of Fig. 1, layer surface is almost smooth, crystal grain has perpendicular long shape on thickness direction, and this crystal grain accounts for the area ratio of more than 35% of entirety in the face perpendicular to thickness direction.
And, about this upgrading AlTiO layer, use field emission type scanning electronic microscope and Electron Back-Scattered Diffraction image device, one by one electron rays is irradiated to the crystal grain be present in the measurement range in surface grinding face, measure the angle that each normal of the lattice plane be made up of hexagonal system lattice is crossing with the normal in described surface grinding face
The mutual crystal orientation relation of adjacent crystal lattice is calculated by this measurement result, calculate each constituting atom forming crystal lattice interface has the lattice point (constituting atom has lattice point) of 1 constituting atom each other distribution in described crystal lattices, with ∑ N+1 represent described constituting atom have to exist between lattice point N number of (wherein, N be corundum type close-packed hexagonal crystallographic system crystalline structure on more than 2 even number, but when the N upper limit being set to 28 distribution frequency, there is not even number 4, 8, 14, 24 and 26) when the constituting atom of the lattice point of not total constituting atom has lattice point form,
As shown in Figure 3, the dull and stereotyped Polygons forming upgrading AlTiO layer erects in long shape crystal grain, count the inside of the described crystal grain of more than 60% with area ratio, by least more than one, to be had the morphotic crystal lattice interface of lattice point (hereinafter referred to as the corresponding interface of ∑ 3) segmentation by the constituting atom represented with ∑ 3.
D upper layer that () is made up of the upgrading AlTiO layer formed with chemical vapor deposition condition (hereinafter referred to as the condition of the present invention) evaporation in the 1st stage of above-mentioned (b) and the 2nd stage, crystal face due to its surface has same orientation with the crystal face (such as (0001)) in the face in the thickness direction perpendicular to this layer, therefore (when observing in the face being parallel to thickness direction, ) layer surface be formed as almost smooth tabular, the excellent resistance to cutter that collapses is shown due to its surface texture, and, intensity in crystal grain is improved because dull and stereotyped Polygons erects the existence at the corresponding interface of ∑ 3 of the intra-die of long shape, therefore compared with the layer of AlTiO in the past of coating tool in the past, there is more excellent hot hardness, hot strength, surface texture, its result, even if during upgrading AlTiO layer of the present invention is processed the high speed heavy cut of blade part effect high loading while generating heat with height, also can not produce and collapse cutter, excellent cutting ability is played in life-time service.
Summary of the invention
This invention completes in view of above-mentioned opinion, has following characteristics:
(1) a kind of surface-coated cutting tool (coating tool), on the surface of the tool base be made up of tungsten carbide base carbide alloy or base titanium carbonitride, evaporation forms the hard coating layer be made up of following (a), (b), wherein
A () lower layer is more than 1 layer or the 2 layers Ti compound layer formed in the carbide lamella of the Ti of the ensemble average thickness with 3 ~ 20 μm, nitride layer, carbonitride layer, oxycarbide layer and carbon nitrogen oxide layer,
B () upper layer is have the average thickness of 2 ~ 15 μm, and have the crystalline structure of α type and the alumina layer containing Ti, it is characterized in that,
When structure observation being carried out to above-mentioned upper layer by field emission type scanning electronic microscope, have the weave construction be made up of following crystal grain, described crystal grain is dull and stereotyped Polygons in the face perpendicular to thickness direction, and has perpendicular long shape on the inner-layer thick direction, face being parallel to thickness direction, in addition
About this upper layer, use field emission type scanning electronic microscope and Electron Back-Scattered Diffraction image device, one by one electron rays is irradiated to the crystal grain be present in the measurement range in surface grinding face, measure the angle that each normal of the lattice plane be made up of hexagonal system lattice is crossing with the normal in described surface grinding face
The mutual crystal orientation relation of adjacent crystal lattice is calculated by this measurement result, calculate each constituting atom forming crystal lattice interface has the lattice point (constituting atom has lattice point) of 1 constituting atom each other distribution in described crystal lattices, with ∑ N+1 represent described constituting atom have to exist between lattice point N number of (wherein, N be corundum type close-packed hexagonal crystallographic system crystalline structure on more than 2 even number, but when the upper limit of N being set to 28 distribution frequency, there is not even number 4, 8, 14, 24 and 26) when the constituting atom of the lattice point of not total constituting atom has lattice point form,
Count the inside of the crystal grain of more than 60% in the crystal grain forming above-mentioned upper layer with area ratio, by least more than one, have the morphotic crystal lattice interface of lattice point by the constituting atom represented with ∑ 3 and split.
(2) as described in (1) surface-coated cutting tool (coating tool) of recording, wherein, when structure observation being carried out to described upper layer (b) by field emission type scanning electronic microscope, it is smooth hexagon in the face perpendicular to thickness direction, and there is the crystal grain of perpendicular long shape in the face being parallel to thickness direction on thickness direction, in the face perpendicular to thickness direction, account for the area ratio of more than 35% of entirety.
Under regard to the hard coating layer of coating tool of the present invention structural sheet illustrate in greater detail.
(a) lower layer (Ti compound layer)
By the carbide lamella of Ti, nitride layer, carbonitride layer, oxycarbide layer, with 1 in carbon nitrogen oxide layer layer or more than the 2 layers Ti compound layers formed, except the lower layer as hard coating layer exists, and the hot strength of the excellence had by self contributes to outside the hot strength of raising hard coating layer, also be sealed at any one in tool base and upgrading AlTiO layer securely, therefore there is the effect improved the bond strength of the tool base of hard coating layer, but, if its average thickness is less than 3 μm, then cannot give full play to described effect, on the other hand, if its average thickness is more than 20 μm, then especially in the thermogenetic high speed cutting of height, easily cause pyroplastic deformation, this can become the reason of partial wear, therefore its average thickness is defined as 3 ~ 20 μm.
(b) upper layer (upgrading AlTiO layer)
About the upper layer be made up of the upgrading AlTiO layer of chemical vapor deposition on lower layer, Al composition due to its constituent improves hot hardness and the thermotolerance of layer, and trace (accounts for the ratio with the total amount of Al in it in layer, Ti/ (Al+Ti) be 0.002 ~ 0.01 (being wherein atomic ratio)) the Ti composition that contains improves the crystal grain-boundary strength of upgrading AlTiO layer, contribute to improving hot strength, but, if containing of Ti composition is proportional less than 0.002, then cannot expect above-mentioned effect, on the other hand, if containing of Ti composition is proportional more than 0.01, then owing to separating out TiO in layer
2particle, grain-boundary strength declines, and therefore, what Ti composition accounted for its total amount with Al is preferably 0.002 ~ 0.01 (being wherein atomic ratio) containing proportional (ratio of Ti/ (Al+Ti)).
And, above-mentioned upgrading AlTiO layer, each chemical vapor deposition condition of such as, reactant gases composition, reaction atmosphere temperature and reaction atmosphere pressure time by adjusting evaporation as follows and evaporation is formed.
That is, first, under the following conditions, the evaporation in the 1st stage of about 1 hour is carried out,
(first) reactant gases composition (capacity %):
AlCl
3：1～5％、
CO
2：2～6％、
HCl：1～5％、
H
2S：0.25～0.75％、
H
2: residue,
(second) reaction atmosphere temperature: 960 ~ 1010 DEG C,
(the third) reaction atmosphere pressure: 6 ~ 10kPa,
Then, the evaporation in the 2nd stage is carried out under the following conditions,
(first) reactant gases composition (capacity %):
AlCl
3：6～10％、
TiCl
4：0.05～0.6％
CO
2：4～8％、
HCl：3～5％、
H
2S：0～0.05％、
H
2: residue,
(second) reaction atmosphere temperature: 920 ~ 1000 DEG C,
(the third) reaction atmosphere pressure: 6 ~ 10kPa,
Thus, if the evaporation layer of the average thickness of film forming 2 ~ 15 μm, then the ratio that can form Ti/ (Al+Ti) take atomic ratio measuring as the upgrading AlTiO layer of 0.002 ~ 0.01.
And, about above-mentioned upgrading AlTiO layer, when carrying out structure observation by field emission type scanning electronic microscope, form the weave construction be made up of following crystal grain: as shown in (a) of Fig. 1, when observing in the face perpendicular to thickness direction, described crystal grain is the dull and stereotyped Polygons of macrocrystal particle diameter, and, as shown in (b) of Fig. 1, when observing in the face being parallel to thickness direction, layer surface is almost smooth, and there is perpendicular long shape (dull and stereotyped Polygons erects long shape crystal grain) on thickness direction, due to this layer of upgrading AlTiO layer surperficial flatness, with exist compared with the concavo-convex layer of AlTiO in the past on surface, the resistance to cutter that collapses improves more.
Especially following weave construction is formed: in the evaporation of described upgrading AlTiO layer, if with the condition limited further (such as, by the H in the reactant gases in the 1st stage
2s is set to 0.50 ~ 0.75 capacity %, and reaction atmosphere temperature is set to 980 ~ 1000 DEG C, in addition, by the TiCl in the reactant gases in the 2nd stage
4be set to 0.05 ~ 0.2 capacity %, H
2s is set to 0 ~ 0.03 capacity %, reaction atmosphere temperature is set to the condition of 960 ~ 980 DEG C) carry out evaporation, then as shown in (c) of Fig. 1, when observing in the face perpendicular to thickness direction, crystal grain is the smooth hexagon of Large stone, and, when observing in the face being parallel to thickness direction, identical with shown in (b) of Fig. 1, layer surface is almost smooth, crystal grain has perpendicular long shape on thickness direction, and this crystal grain accounts for the area ratio of more than 35% of entirety in the face perpendicular to thickness direction.
In addition, in AlTiO layer in the past, the crystal face on its surface has the orientation different from the crystal face (such as (0001)) in the face in the thickness direction perpendicular to this layer (such as, have (1-102)), therefore, (when observing in the face being parallel to thickness direction) as shown in (b) of Fig. 2, layer surface exists pyramidal concavo-convex, for this reason, the resistance to cutter that collapses is deteriorated.
Further, about this upgrading AlTiO layer, use field emission type scanning electronic microscope and Electron Back-Scattered Diffraction image device, one by one electron rays is irradiated to the crystal grain be present in the measurement range in surface grinding face, measure the angle that each normal of the lattice plane be made up of hexagonal system lattice is crossing with the normal in described surface grinding face
The mutual crystal orientation relation of adjacent crystal lattice is calculated by this measurement result, calculate each constituting atom forming crystal lattice interface has the lattice point (constituting atom has lattice point) of 1 constituting atom each other distribution in described crystal lattices, with ∑ N+1 represent described constituting atom have to exist between lattice point N number of (wherein, N be corundum type close-packed hexagonal crystallographic system crystalline structure on more than 2 even number, but when the upper limit of N being set to 28 distribution frequency, there is not even number 4, 8, 14, 24 and 26) when the constituting atom of the lattice point of not total constituting atom has lattice point form,
As shown in (c) of Fig. 1, count the inside of the crystal grain of more than 60% in the perpendicular long shape crystal grain of the above-mentioned dull and stereotyped Polygons (comprising smooth hexagon) of known formation upgrading AlTiO layer with area ratio, by least more than one, the corresponding interface of ∑ 3 splits.
And, in the inside of the perpendicular long shape crystal grain of the dull and stereotyped Polygons (comprising smooth hexagon) of upgrading AlTiO layer, there is the above-mentioned corresponding interface of ∑ 3, the raising of intensity in crystal grain can be sought thus, its result, man-hour is added at high speed heavy cut, can suppress to produce crack in upgrading AlTiO layer, in addition, even if produce crack, also can hinder expansion, the propagation in crack, resistance to raising of collapsing cutter, fracture resistance, peel resistance can be sought.
Therefore, the corresponding interface of ∑ 3 is there is by the inside at the perpendicular long shape crystal grain of dull and stereotyped Polygons (comprising smooth hexagon), and the upper layer of the present invention that the upgrading AlTiO layer possessing the smooth surface texture in surface is formed, even if in processing with various steel or the contour heating of cast iron and to the high speed heavy cut of blade part effect high loading, also can not produce and collapse cutter, defect, stripping etc., the long-term cutting ability playing excellence.
But, if the thickness of the upper layer be made up of upgrading AlTiO layer is less than 2 μm, then cannot give full play to the characteristic of the excellence of above-mentioned upper layer, on the other hand, if the thickness of upper layer is more than 15 μm, then easily produce the pyroplastic deformation becoming partial wear reason, also easily produce and collapse cutter, therefore, the average thickness of upper layer is defined as 2 ~ 15 μm.
In addition, for the coating tool in the past that the upper layer of hard coating layer is made up of AlTiO layer in the past, use field emission type scanning electronic microscope, Electron Back-Scattered Diffraction image device, weave construction and the constituting atom of investigating the crystal grain of upper layer have lattice point form, result is about the weave construction of crystal grain, what have as shown in (a), (b) of Fig. 2 is pyramidal concavo-convex, there is the weave construction that the crystal grain that erects long shape by Polygons is formed, therefore, compared with upgrading AlTiO layer, wear resistance is insufficient.
In addition, have with regard to lattice point form with regard to the constituting atom of crystal grain, the area ratio that the concave-convex polygonal forming AlTiO layer in the past erects the crystal grain that there is the corresponding interface of ∑ 3 in the inside of long shape crystal grain is little of less than 40%, cannot seek the raising of intensity in crystal grain.
Therefore, forming the coating tool in the past of the upper layer of hard coating layer by AlTiO layer in the past, in the high speed heavy cut processing of blade part effect high loading while with high heating, cannot meet for preventing to collapse cutter, defect, stripping etc.
Invention effect
As mentioned above, coating tool of the present invention, the weave construction be made up of the crystal grain of the perpendicular long shape of the dull and stereotyped Polygons possessing surface (comprising smooth hexagon) is set to about the upgrading AlTiO layer forming upper layer, in addition, form the corresponding interface of ∑ 3 at above-mentioned intra-die and enhance intensity in crystal grain, to form with the crystal grain being erected long shape by concave-convex polygonal thus and using the layer of AlTiO in the past few for corresponding for ∑ in crystal grain 3 interface compared with the coating tool in the past of upper layer, except the hot hardness that AlTiO layer in the past has, thermotolerance, also have more excellent hot strength and more excellent wear resistance concurrently, its result, while with high heating to the high speed heavy cut condition of blade part effect high loading under the various steel of machining or cast iron etc. time, hard coating layer also can play the resistance to of excellence and collapse cutter, fracture resistance, peel resistance, can increase the service life further.
Accompanying drawing explanation
(a) of Fig. 1 is for coating tool 1 ~ 9 of the present invention, 12, 14, the upper layer be made up of upgrading AlTiO layer of 15, field emission type sem observation is used and the schematic diagram of the dull and stereotyped polygonal grain structure structure of the expression that obtains in the face perpendicular to thickness direction, b () similarly in the face being parallel to thickness direction, uses field emission type sem observation and the presentation layer surface that obtains is almost smooth and on thickness direction, have the schematic diagram of the grain structure structure of perpendicular long shape, c () is for coating tool 10 of the present invention, 11, the upper layer be made up of upgrading AlTiO layer of 13, field emission type sem observation is used and the schematic diagram of the smooth hexagonal grain structure structure of expression obtained in the face perpendicular to thickness direction.
(a) of Fig. 2 is the upper layer be made up of AlTiO layer in the past for coating tool 1 ~ 15 in the past, in the face perpendicular to thickness direction, use field emission type sem observation and the schematic diagram of the polygonal grain structure structure of expression that obtains, (b) similarly uses field emission type sem observation and the presentation layer surface that obtains has pyramidal concavo-convex and on thickness direction, have the schematic diagram of the grain structure structure of perpendicular long shape in the face being parallel to thickness direction.
Fig. 3 is the upper layer be made up of upgrading AlTiO layer for coating tool 1 ~ 9,12,14,15 of the present invention, use the crystal boundary analysis chart in the face perpendicular to thickness direction that field emission type scanning electronic microscope and Electron Back-Scattered Diffraction image device measure, solid line represents the polygonal crystal boundary of flat board with field emission type sem observation, and dotted line represents the corresponding interface of ∑ 3 measured by Electron Back-Scattered Diffraction image device.
Embodiment
Then, coating tool of the present invention is further illustrated by embodiment.
[embodiment]
As raw material powder, prepare WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, the Cr all with 2 ~ 4 μm of median sizes
3c
2powder, TiN powder, TaN powder and Co powder, these raw material powders are fitted in the cooperation composition shown in table 1, and add paraffin in acetone ball milling mix 24 hours, after drying under reduced pressure, the pressed compact of predetermined shape is shaped to the pressure extrusion of 98MPa, in the vacuum of 5Pa, this pressed compact of vacuum sintering under the maintenance condition of 1 hour in preset temperature within the scope of 1370 ~ 1470 DEG C, after sintering, blade part is applied to the Honing process of R:0.07mm, manufacture the WC base cemented carbide tool base A ~ E with the indexable insert tip, throw away tip shape that ISOCNMG120408 specifies thus respectively.
In addition, as raw material powder, prepare TiCN (by quality ratio, being TiC/TiN=50/50) powder, the Mo all with 0.5 ~ 2 μm of median size
2c powder, ZrC powder, NbC powder, TaC powder, WC powder, Co powder and Ni powder, these raw material powders are fitted in the cooperation composition shown in table 2,24 hours wet mixing are carried out with ball mill, after drying, pressed compact is shaped to the pressure extrusion of 98MPa, in the nitrogen atmosphere of 1.3kPa, with temperature: keep in 1540 DEG C sintering this pressed compact under the condition of 1 hour, after sintering, blade part is applied to the Honing process of R:0.07mm, form the TiCN based ceramic metal tool base a ~ e with the blade shapes of ISO specification CNMG120408 thus.
Then; these tool base A ~ E and tool base a ~ e is respectively charged in usual chemical evaporation plating device; first by table 3, (1-TiCN in table 3 represents the formation condition with the TiCN layer of longitudinal growth crystalline structure recorded in Japanese Patent Publication 6-8010 publication; represent the formation condition of common bulk crystalline tissue in addition) shown in condition, form the lower layer of Ti compound layer as hard coating layer using the combination shown in table 6 and target thickness evaporation.
Then, according to the evaporation condition shown in table 4, same evaporation forms the upper layer of upgrading AlTiO layer as hard coating layer of the target thickness shown in table 6, manufactures coating tool 1 ~ 15 of the present invention respectively thus.
In addition, with the object compared, after forming lower layer with evaporation under coating tool 1 ~ 15 the same terms of the present invention, under the conditions shown in Table 5, form AlTiO layer in the past using the combination shown in table 7 and target thickness and, as the upper layer of hard coating layer, manufacture coating tool 1 ~ 15 in the past thus respectively.
Then, for forming the invention described above coating tool 1 ~ 15 and the upgrading AlTiO layer of the upper layer of the hard coating layer of coating tool 1 ~ 15 and AlTiO layer in the past in the past, use field emission type scanning electronic microscope, Electron Back-Scattered Diffraction image device, investigation grain structure structure and constituting atom have lattice point form.
Namely, first, to the layer of AlTiO in the past of the upgrading AlTiO layer of the invention described above coating tool 1 ~ 15 and coating tool 1 ~ 15 in the past, use field emission type sem observation, result is observed (a) of Fig. 1 in coating tool of the present invention, b the dull and stereotyped Polygons (comprising smooth hexagon) shown typically in () and the grain structure structure of the Large stone of perpendicular long shape are (in addition, (a) of Fig. 1 is the coating tool of the present invention 1 ~ 9 observed in the face perpendicular to thickness direction, 12, 14, the weave construction schematic diagram of 15, and (c) of Fig. 1 is the coating tool of the present invention 10 observed in the face perpendicular to thickness direction, 11, 13, smooth hexagon and the Large stone grain structure structural representation of perpendicular long shape).
On the other hand, in coating tool in the past, as shown typically in (a), (b) of Fig. 2, observe Polygons and the grain structure of perpendicular long shape, but the particle diameter ratio of each crystal grain is of the present invention little, and also can as apparent from (b) of Fig. 2, layer surface is formed pyramidal concavo-convex (in addition, (a), (b) of Fig. 2 is the weave construction schematic diagram of coating tool 1 ~ 15 in the past).
Then, for the upgrading AlTiO layer of the invention described above coating tool 1 ~ 15 and the layer of AlTiO in the past of coating tool 1 ~ 15 in the past, there is the area ratio of the crystal grain at the corresponding interface of ∑ 3 in the inside measuring the crystal grain forming each layer.
First, for the upgrading AlTiO layer of the invention described above coating tool 1 ~ 15, under the state that its surface is set to abrasive surface, be arranged in the lens barrel of field emission type scanning electronic microscope, to described surface grinding face, irradiate the electron rays of the acceleration voltage of 15kV with the input angle of 70 degree with the irradiation electric current of 1nA, and the crystal grain with hexagonal system lattice existed in the measurement range in surface grinding face described in each irradiates electron rays respectively, use Electron Back-Scattered Diffraction image device, to the regions of 30 × 50 μm with the interval of 0.1 μm/step, measure the angle that each normal of each lattice plane of described crystal grain is crossing with the normal in described surface grinding face, the mutual crystal orientation relation of adjacent crystal lattice is calculated by this measurement result, calculate each constituting atom forming crystal lattice interface has the lattice point (constituting atom has lattice point) of 1 constituting atom each other distribution in described crystal lattices, with ∑ N+1 represent described constituting atom have to exist between lattice point N number of (wherein, N be corundum type close-packed hexagonal crystallographic system crystalline structure on more than 2 even number, but when the upper limit of N being set to 28 distribution frequency, there is not even number 4, 8, 14, 24 and 26) when the constituting atom of the lattice point of not total constituting atom has lattice point form, obtain in all crystal grains existed in the measurement range of upgrading AlTiO layer, the area ratio of the crystal grain at least more than one the corresponding interface of ∑ 3 is there is at intra-die, its value is shown in table 6.
Then, for the layer of AlTiO in the past of coating tool 1 ~ 15 in the past, also by the method identical with the situation of coating tool of the present invention, obtain in all crystal grains existed in the measurement range of AlTiO layer in the past, there is the area ratio of the crystal grain at least more than one the corresponding interface of ∑ 3 at intra-die, its value is shown in table 7.
As shown in table 6, table 7, in the upgrading A1TiO layer of coating tool of the present invention, the area ratio of the crystal grain existing for the corresponding interface of ∑ 3 is more than 60%, on the other hand, in the layer of AlTiO in the past of coating tool in the past, the area ratio of the crystal grain existing for the corresponding interface of ∑ 3 is less than 40%, known the corresponding interface of intra-die ∑ 3 to there is rate very little.
In addition, the thickness of use scanning electron microscope mensuration (vertical section mensuration) coating tool 1 ~ 15 of the present invention and the in the past structural sheet of the hard coating layer of coating tool 1 ~ 15, result all shows the thick practically identical average thickness (measuring the mean value of 5) with destination layer.
In addition, for the upgrading AlTiO layer of coating tool 10,11,13 of the present invention, use field emission type scanning electronic microscope, obtain the area ratio of the smooth hexagon crystal grain of the Large stone existed in the face perpendicular to thickness direction, its value is shown in table 6.
In addition, the crystal grain of the present invention's said " smooth hexagon of Large stone " is defined as that " measure the diameter of the particle existed in the face perpendicular to thickness direction by field emission type sem observation; the mean value of 10 particles is 3 ~ 8 μm, the angle with 6 summits is the Polygons of the drift angle of 100 ~ 140 °.”
Then, for the various coating tools of the invention described above coating tool 1 ~ 15 and coating tool 1 ~ 15 in the past, under the state of all tightening at the leading section stationary fixture of instrument steel lathe tool, following test is carried out,
[machining condition A]
Be cut material: the pole of JISS35C,
Cutting speed: 450m/min,
The depth of cut: 2.5mm,
Delivery rate: 0.7mm/rev,
Cutting time: 8 minutes,
Carry out the cutting test (common cutting speed and delivery rate are 250m/min, 0.3mm/rev respectively) of the high delivery rate of dry type high speed of carbon steel under these conditions;
[machining condition B]
Be cut material: the pole of JISSCM430,
Cutting speed: 320m/min,
The depth of cut: 2.2mm,
Delivery rate: 0.3mm/rev,
Cutting time: 5 minutes,
Carry out the cutting test (common cutting speed and the depth of cut are respectively 250m/min, 1.5mm) of the high depth of cut of dry type high speed of chrome-moly steel under these conditions;
[machining condition C]
Be cut material: the pole of JISFC300,
Cutting speed: 545m/min,
The depth of cut: 5.6mm,
Delivery rate: 0.6mm/rev,
Cutting time: 5 minutes,
Carry out the cutting test (common cutting speed and the depth of cut are respectively 350m/min, 2.5mm) of the high depth of cut of wet type high speed of cast iron under these conditions,
The abrasion width of knife face all measure blade in all cutting tests after.This measurement result is shown in table 8.
Table 6
(bracket inner digital on lower layer hurdle represents target thickness)
Table 7
Table 8
The cutting test result of coating tool represented to collapse cutter or wear of the tool flank (judging service life benchmark: wear of the tool flank width 0.5mm) reach life-span cutting time (minute) for reason in the past.
In addition, the * symbol in hurdle represents that collapsing cutter is the situation that reason reaches the life-span.
Following content is specify that: coating tool of the present invention by the result shown in table 6 ~ 8, its alumina layer (upgrading AlTiO layer) containing Ti forming upper layer erects the weave construction of the crystal grain of long shape and forms as dull and stereotyped Polygons (smooth Polygons), and intra-die to there is the area ratio of the crystal grain at least more than one the corresponding interface of ∑ 3 high, thus, except the hot hardness that the layer of AlTiO in the past of coating tool in the past has, hot strength, thermotolerance, also have more excellent surface and more excellent hot strength concurrently, its result, while with height heating to the machining under the high speed heavy cut condition of blade part effect high loading in when using various steel or cast iron etc., hard coating layer also can play the resistance to of excellence and collapse cutter, fracture resistance, peel resistance, can increase the service life further, on the other hand, formed in the past in the coating tool in the past 1 ~ 15 of AlTiO layer as the upper layer of hard coating layer at evaporation, under high speed heavy cut condition, hot strength is insufficient, easily promote wearing and tearing simultaneously, its result reaches work-ing life within a short period of time.
Industrial applicibility
As mentioned above, coating tool of the present invention, much less the machining under the usual conditions of various steel or cast iron etc., especially in the high speed heavy cut of blade part effect high loading being processed while generating heat with height, hard coating layer also demonstrates the resistance to of excellence and collapses cutter, fracture resistance, peel resistance, excellent cutting ability can be played in life-time service, therefore, saving labourization and energy-saving and the cost degradation of the high performance of topping machanism and machining can be tackled fully contentedly.
Claims (2)
1. a surface-coated cutting tool, on the surface of the tool base be made up of tungsten carbide base carbide alloy or base titanium carbonitride, evaporation forms the surface-coated cutting tool of the hard coating layer be made up of following (a), (b), wherein
(a) lower layer, for have 3 ~ 20 μm ensemble average thickness by more than 1 layer or the 2 layers Ti compound layer formed in the carbide lamella of Ti, nitride layer, carbonitride layer, oxycarbide layer and carbon nitrogen oxide layer,
B () upper layer, for having the average thickness of 2 ~ 15 μm, and having the crystalline structure of α type and the alumina layer containing Ti, it is characterized in that,
When structure observation being carried out to above-mentioned upper layer by field emission type scanning electronic microscope, have the weave construction be made up of following crystal grain, described crystal grain is dull and stereotyped Polygons in the face perpendicular to thickness direction, and on thickness direction, has perpendicular long shape in the face being parallel to thickness direction, in addition
About this upper layer, use field emission type scanning electronic microscope and Electron Back-Scattered Diffraction image device, one by one electron rays is irradiated to the crystal grain be present in the measurement range in surface grinding face, measure the angle that each normal of the lattice plane be made up of hexagonal system lattice is crossing with the normal in described surface grinding face
The mutual crystal orientation relation of adjacent crystal lattice is calculated by this measurement result, calculate each constituting atom forming crystal lattice interface and have in described crystal lattices the distribution that the lattice point of 1 constituting atom and constituting atom have lattice point each other, represent when the constituting atom that described constituting atom has the lattice point that there is N number of not total constituting atom between lattice point has lattice point form with ∑ N+1
Count the inside of the crystal grain of more than 60% in the crystal grain forming above-mentioned upper layer with area ratio, by least more than one, have the morphotic crystal lattice interface of lattice point by the constituting atom represented with ∑ 3 and split,
Wherein said N be corundum type close-packed hexagonal crystallographic system crystalline structure on more than 2 even number, but when the upper limit of N being set to 28 distribution frequency, there is not even number 4,8,14,24 and 26.
2. surface-coated cutting tool as claimed in claim 1, wherein, when structure observation being carried out to described upper layer (b) by field emission type scanning electronic microscope, it is smooth hexagon in the face perpendicular to thickness direction, and there is the crystal grain of perpendicular long shape in the face being parallel to thickness direction on thickness direction, in the face perpendicular to thickness direction, account for the area ratio of more than 35% of entirety.
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| JP2006289556A (en) * | 2005-04-12 | 2006-10-26 | Mitsubishi Materials Corp | Surface-coated cermet cutting tool having hard coating layer for exhibiting superior chipping resistance in high speed intermittent cutting work |
| CN1966264A (en) * | 2005-11-18 | 2007-05-23 | 三菱麻铁里亚尔株式会社 | Surface coated cutting tool made of cermet |
| CN101468401A (en) * | 2007-12-28 | 2009-07-01 | 三菱麻铁里亚尔株式会社 | Surface-coated cutting tool with hard coating layer having excellent abrasion resistance |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2006289556A (en) * | 2005-04-12 | 2006-10-26 | Mitsubishi Materials Corp | Surface-coated cermet cutting tool having hard coating layer for exhibiting superior chipping resistance in high speed intermittent cutting work |
| CN1966264A (en) * | 2005-11-18 | 2007-05-23 | 三菱麻铁里亚尔株式会社 | Surface coated cutting tool made of cermet |
| CN101468401A (en) * | 2007-12-28 | 2009-07-01 | 三菱麻铁里亚尔株式会社 | Surface-coated cutting tool with hard coating layer having excellent abrasion resistance |
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