CN101870003A - Hard alloy coated tool for milling steel and stainless steel - Google Patents
Hard alloy coated tool for milling steel and stainless steel Download PDFInfo
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- CN101870003A CN101870003A CN 201010211189 CN201010211189A CN101870003A CN 101870003 A CN101870003 A CN 101870003A CN 201010211189 CN201010211189 CN 201010211189 CN 201010211189 A CN201010211189 A CN 201010211189A CN 101870003 A CN101870003 A CN 101870003A
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Abstract
The invention discloses a hard alloy coated tool for milling steel and stainless steel, which comprises a hard alloy matrix and a coating coated thereon. The hard alloy matrix comprises at least one cutting edge which is formed by crossing a front tool face and a rear tool face. Both the hard alloys on two sides of the cutting edge are in gradient change, namely transit from a homogeneous phase alloy region in an inner layer to a cubic carbon nitride enriched region and then transit to a binding phase enriched surface region, and the content of Co and cubic phase compound in the matrix is controlled. In the gradient change structure, the intersection area of the cutting edge is mainly in the cubic carbon nitride enriched region, and the length of the area exposed at the cutting edge in a direction vertical to the front tool face is more than or equal to 2 times that in the rear tool face direction. The coating comprises a TiN layer, a TiCN layer, a TiCO transition layer and an outermost alpha-Al2O3 layer from the interior to the exterior in turn. The coated tool has the advantages of high abrasive resistance, high cutting edge strength, strong thermal crack propagation resistance, and the like.
Description
Technical field
The present invention relates to a kind of carbide chip, relate in particular to the hard alloy coated blade that a kind of milling is used.
Background technology
In metal cutting process, there are two kinds of inefficacy mechanisms in cutter: wearing and tearing and damaged.Blade abrasion mainly comprises corrosion wear, bonding abrasion, diffusive wear and oxidative wear.Under different machining conditions, during the workpiece of processing different materials, the main cause of its wearing and tearing may be wherein one or both.One, when cutting temperature is low based on corrosion wear, when cutting temperature is higher based on diffusive wear, oxidative wear.The blade breakage mainly be the fragility breakage (tipping, cracked, peel off, crackle breakage etc.) and plastic deformation.Experimental data shows, the blade early damage stress influence that is heated is less, mainly is the fragility breakage that is subjected to due to the mechanical shock effect; Blade later stage endurance failure mainly is the plastic deformation that fragility is damaged and too high processing temperature causes due to machinery and the diffusion of thermal shock effect bottom knife internal fissure unstability.
In steel and stainless Milling Process, cut out cutting temperature with point of a knife acute variation can take place, cause the generation of ardent line, cause the breakage of point of a knife cutting edge generation fragility.Practice shows, when steel and stainless steel were carried out Milling Process, the blade master was lost efficacy and mainly contained cutting edge that fire check causes and collapse scarce, and the wear of the tool flank that causes of work hardening.In order to adapt to the requirement of steel and stainless steel high-speed and high-efficiency Milling Process, milling cutting insert should have the ability of higher toughness, elevated temperature strength and the expansion of cracking resistance line.
At present, the coated cemented carbide insert with binder phase enriched surf zone is widely used in the machining of alloys such as steel, and the binder phase enriched surf zone has been widened the range of application of blade, makes it to be applied to the cutting operation of richer toughness.Contain α-Al
2O
3The laminated coating of coating has improved the anti-wear performance of blade, makes the life-span of blade obtain increasing, and coating and blade base superiority has separately realized unified preferably in coated chip.
In the preparation of blade base, the carbide alloy that manufacturing contains WC, cube phase and binder phase enriched surface region belongs to the gradient sintering technology, (for example US4277283 and US4610931 american documentation literature in the partial monopoly document, and CN1079179A, CN1134470A, CN1229442A, CN1532014A, CN1854320A, CN1891842A Chinese patent literature) hard alloy substrate of bonding phase content graded and preparation method thereof is disclosed, can obtain not have basically the binder phase enriched surface region of cube phase.CN1079179A Chinese patent literature particularly, it relates to a kind of carbide chip that improves toughness and flow drag that has, this blade is with known method in a vacuum behind the nitrogenous material of sintering, again 1280 ℃～1430 ℃ temperature, handle blade 5min～100min in 40mbar～400mbar nitrogen, obtain a kind of carbide alloy with binder phase enriched surface region, it is in the zone of binder phase enriched surface region lower floor, the content of bonding phase be 0.85～1 of this blade inside content, and the content substantially constant of cube phase and equal the content of this blade inside.This kind blade structure has played certain effect to improving blade toughness and flow drag.From view point of fracture mechanics, the carbide alloy with enrichment bonding phase surface district can absorb the crackle propagation energy, prevents the expansion of crackle, thereby improves the toughness of blade, shows more tough character.Yet in application practice thereafter, we find that the existence in enrichment bonding phase surface district has reduced the yield strength and the hardness of blade material, cause blade cutting edge to be easy to generate plastic deformation, and back knife face antiwear property descends.The CN101214743A Chinese patent literature discloses a kind of coated chip that is used for processing cast iron, the cutting edge both sides of this blade base form the binder phase enriched surface region, sector region in the middle of the binder phase enriched surface region is a cube phase enrichment region, this structure has improved the plasticity_resistant deformation ability of cutting edge, but in the Milling Process of steel, thereafter knife face antiwear property performance is relatively poor, and the plasticity_resistant deformation ability also remains further to be improved.
In the preparation of blade base face coat, the coating (as TiN, TiC, TiCN, CrN etc.) that applies high rigidity at tool surface can alleviate corrosion wear, bonding abrasion and the diffusive wear of blade, increases the durability of blade; And apply the Al of high rigidity in blade face
2O
3Coating can effectively be avoided oxidative wear.Adopt nitride, carbide, carbonitride and the aluminium oxide of CVD method titanium deposition on the cutting tip matrix, this has had description in existing a lot of patent documentations.For example US4490191 and US3736107 american documentation literature, EP0408535A1 and EP0738336A1 European patent document and CN1091683A and CN1107901A Chinese patent literature etc. disclose the preparation method of oxide coated cutting tool and the preprocess method of various raising oxide coating adhesion properties.JP7075903A Japanese documentation, SE511089C2 Swedish patent document and WO0052225A1 international publication patent documentation disclose the preparation method and the application of this coating in cubic boron nitride cutting tool, hard alloy cutter, overbrushing layer cutter of MTCVD-TiC or TiCN coating.The CVD coating of existing coated chip generally adopts MTCVD-TiCN coating and Al
2O
3The skin design of coating, the typical coating structure is TiCN (skin)+Al
2O
3The multilayer architecture of (middle level)+TiCN (internal layer), though this multilayer architecture has certain versatility, can be applicable to the cutting tip of each manufacture field, but we find that the CVD coating can reduce the intensity of blade significantly, so at specific field (for example steel and stainless steel milling), the concrete structure of coating (for example combination of coating layer thickness and each layer thickness) should have very big difference.
To sum up, we are necessary microstructure and the further adjustment of parameters index do, combination and the optimization of blade matrix and insert coating, to adapt to the needs of different processing objects, different processing modes.
Summary of the invention
The technical problem to be solved in the present invention is to overcome the deficiencies in the prior art, and the hard alloy coated blade that is used for steel and stainless steel milling that a kind of wearability is good, cutting edge strength is high, heat resistanceheat resistant crackle extended capability is strong is provided.
For solving the problems of the technologies described above, the technical scheme that the present invention proposes is a kind of hard alloy coated blade that is used for steel and stainless steel milling, comprise hard alloy substrate and the coating that applies on it, described hard alloy substrate comprises that at least one intersects formed cutting edge by rake face and back knife face, the carbide alloy that described cutting edge both sides are positioned at rake face and back knife face all presents the graded structure, this graded structure is meant that the homogeneous phase alloy zone by internal layer carries out the transition to a cube carboritride enrichment region, carry out the transition to the binder phase enriched surface region again, it is characterized in that: the content of Co is 7wt%～12wt% in the described hard alloy substrate, the content of described cube of phase compound is 0.2wt%～3.5wt%, the intersectional region of described graded structure at the cutting edge place is mainly a cube carboritride enrichment region, and cube carboritride enrichment surf zone that is exposed to the cutting edge place (is being L1 〉=2L2) more than or equal to it perpendicular to 2 times of the length L 2 on the knife face direction of described back perpendicular to the length L 1 on the described rake face direction;
Described coating is thin brilliant laminated coating, includes successively from inside to outside:
The TiN layer of-innermost layer, thickness are 0.1 μ m～2 μ m, mean grain size≤0.5 μ m;
-one deck TiCN layer, column crystal, thickness are 1 μ m～6 μ m, and mean grain size is 0.1 μ m～2 μ m;
-one deck TiCO transition zone, thickness are 0.1 μ m～1.5 μ m, and this layer crystal grain is acicular grains or equi-axed crystal, mean grain size≤0.5 μ m;
-outermost α-Al
2O
3Layer, thickness is 1 μ m～5 μ m, equi-axed crystal, mean grain size is 0.1 μ m～2 μ m, the surface roughness Ra that records on the length of 300 μ m≤0.25 μ m.
According to us long-term practice and observation, bonding phase content height good toughness then in the carbide alloy, but antiwear property can descend, and is easy to generate plastic deformation; Then high temperature hardness raising behind the interpolation cube carboritride in the carbide alloy, antiwear property strengthens, but toughness reduction relatively is easy to generate crackle and tipping.The increase of coating layer thickness can cause coating stress to increase, thereby obviously reduces the bending strength of cutter.In metal cutting process, smear metal and workpiece material and blade cutting edge generation effect, produce very big cutting force and very high cutting temperature, after the binder phase enriched surface region at cutting edge position is removed, expose and contain cube carboritride enrichment region and form the skeleton supporting construction, this skeleton supporting construction can improve the high-temperature behavior of blade cutting edge effectively, the cutting edge of avoiding the binder phase enriched surface region to cover produces plastic deformation under the effect of cutting force and heat in metal cutting, this is the basic advantage that the present invention possesses.But the more important thing is, the present invention is except paying close attention to the plastic deformation of cutting edge, also to improve the antiwear property of blade simultaneously, based on this, the present invention is by adding a spot of nitrogenous cube of compound or being main additive by the solid solution that these cubes compound is formed, the gradient hard alloy matrix that has prepared surperficial rich cobalt in conjunction with gradient sintering technology, again by cutting edge is handled, form cube carboritride enrichment surf zone perpendicular to the length L 1 on the described rake face direction greater than its cutting edge skeleton supporting construction perpendicular to the length L 2 on the knife face direction of described back, this structural design can effectively be avoided descending and the cutting edge tipping owing to the transition of cube carboritride enrichment region on rake face exposes the cutting edge strength cause, improves the antiwear property of knife face behind the blade simultaneously.In addition, the blade base of above-mentioned band gradient function surface and cutting edge structure improvement is combined with the laminated coating that described thin crystalline substance approaches, this further improves the toughness and the intensity of hard alloy coated blade, on the wearability basis that keeps coated chip, reduce cutting edge that the fire check expansion causes greatly and collapsed scarcely, satisfied the requirement of steel and stainless steel milling.
The above-mentioned hard alloy coated blade that is used for steel and stainless steel milling is positioned at rake face and is preferably greater than near the thickness L3 of the described binder phase enriched surface region in cutting edge zone and is positioned at the back knife face and near the thickness L4 of the described binder phase enriched surface region in cutting edge zone; The value of described L3 is preferably 10 μ m≤L3≤70 μ m.Preferred, be positioned at the back knife face and equal zero near the thickness L4 of the described binder phase enriched surface region in cutting edge zone, promptly be positioned at the back knife face and removed fully near the top layer binder phase enriched layer in the certain zone of cutting edge.The rake face of carbide chip of the present invention adopts the design of binder phase enriched surface region can effectively reduce the expansion of ardent line in the working angles, improves the blade cutting edge obdurability; Then the binder phase enriched surface region does not significantly act on improving the blade cutting edge obdurability on the knife face, therefore, back knife face adopts relatively thin binder phase enriched surface region or does not have the design of binder phase enriched surface region, can further improve the antiwear property of knife face behind the blade, improve the service life of blade.
The above-mentioned hard alloy coated blade that is used for steel and stainless steel milling, the content of described Co is preferably 8wt%～11wt%, and the content of described cube of phase compound is preferably 0.5wt%～2.5wt% (most preferably being 0.8%～1.5%).The content of higher Co can improve the intensity and the toughness of cutter, in WC/Co carbide alloy system, add a spot of nitrogenous cube of phase compound, the graded alloy matrix that can have the binder phase enriched surface region by the preparation of gradient sintering technology, cutting edge structure design of the present invention is achieved, can also avoids because the too high decline that causes hard alloy substrate intensity and heat resistanceheat resistant crackle extended capability of cube phase compounds content.
The above-mentioned hard alloy coated blade that is used for steel and stainless steel milling, be positioned at rake face and be preferably 20 μ m≤L3≤50 μ m near the value of the thickness L3 of the described binder phase enriched surface region in cutting edge zone, the content of Co is 1～1.5 times of Co nominal content in the hard alloy substrate in this binder phase enriched surface region.The above-mentioned hard alloy coated blade that is used for steel and stainless steel milling, the thickness of described cube of carboritride enrichment region is preferably 20 μ m～60 μ m, and the content of cube phase compound is preferably 1～1.5 times of cube phase compound nominal content in the hard alloy substrate in this cube carboritride enrichment region.The having of the binder phase enriched surface region of this gradient hard alloy matrix is beneficial to and stops the micro-crack that produces in the insert coating to be expanded to matrix, make it to show than better impact resistance of ordinary rigid alloy substrate and anti-tipping blade ability, can reduce the negative influence that decline brought of the whole toughness of cube matrix that the phase compound causes; And the adding of a small amount of cube of carboritride can improve the high-temperature behavior and the hardness of cutter effectively.
The above-mentioned hard alloy coated blade that is used for steel and stainless steel milling, the thickness of described TiN layer are preferably 0.2 μ m～1 μ m; The thickness of described TiCN layer is preferably 2 μ m～5 μ m; The thickness of described TiCO transition zone is preferably 0.2 μ m～1 μ m; Described α-Al
2O
3The thickness of layer is preferably 1 μ m～3 μ m.
The above-mentioned hard alloy coated blade that is used for steel and stainless steel milling, (be MT-Ti (C, N) layer), the mean grain size of described TiCN layer is preferably 0.3 μ m～1.5 μ m to warm chemical vapor deposited coatings during described TiCN layer is preferably; Described α-Al
2O
3The mean grain size of layer is preferably 0.4 μ m～1.5 μ m.
In the coating structure of technique scheme, and MT-Ti (C, N) the coating internal stress is less, can improve the toughness of coating under same thickness, stops the diffusion of crackle, reduces the tipping of cutter; Or under identical stress, can increase the thickness of coating, improve wearability.(C, N) layer has the good hardness of excellent toughness and the TiC of TiN concurrently, the service life that can improve coated chip significantly as the main coating of coated chip of the present invention with MT-Ti.Al
2O
3Have excellent mechanical property, heat endurance and non-oxidizability, what is more important Al
2O
3Little with the chemical affinity of iron and steel and stainless steel-like workpiece material, work in-process shows good anti-chemical abrasion performance.Because the CVD coating generally is in tensile stress state, be easy to generate crackle, and coating crack has the trend of increase with the increase of coating layer thickness, so for Milling Process, the present invention adopts thin coated designs, to reduce the stress and the crack density of coating.
The above-mentioned concrete preparation method who is used for the hard alloy coated blade matrix of steel and stainless steel milling is:
Be mixed with into uniform powder mixture with tungsten carbide powder, cobalt powder (Co) and cubic carbonitride or by the solid solution additive that these cubes compound is formed, and powder mixture suppressed, adopt the gradient sintering technology to carry out sintering then, form one deck binder phase enriched surface region in cemented carbide substrate surfaces, under the binder phase enriched surface region, form one deck cube carboritride enrichment region; The content of Co is greater than Co nominal content in the hard alloy substrate in the described binder phase enriched surface region, and the content of carboritride is more than or equal to carboritride nominal content in the hard alloy substrate in cube carboritride enrichment region; Then, the hard alloy substrate with gradient-structure for preparing is adopted one or more combinations in the methods such as chamfered edge, sandblast, grinding, polishing, polish-brush, the cutting edge of blade, back knife face, rake face are handled, remove binder phase enriched surface region and part cube carboritride enrichment region on cutting edge, back knife face, the rake face selectively, obtain the carbide chip that improves cutting edge structure of the present invention at last.
Combination by following existing technology on the carbide blade base of above-mentioned preparation can obtain laminated coating: adopt existing C VD technology to deposit the TiN layer of innermost layer earlier on hard alloy substrate; Utilize MTCVD technology (also can utilize the CVD method) depositing Ti CN layer on the TiN layer again; Utilize existing HTCVD technology on the TiCN layer, to deposit one deck TiCO layer then; Utilize HTCVD technology on the TiCO layer, to deposit outermost α-Al at last
2O
3Layer.Hard alloy coated blade behind the applying coating is adopted surface treatments such as sandblast, siliceous nylon bruss polishing, the surface roughness Ra that on the length of 300 μ m, records≤0.25 μ m.
Compared with prior art, the invention has the advantages that: the characteristics that the present invention is directed to steel and stainless steel Milling Process, by adding a small amount of cube of carboritride, prepared gradient hard alloy matrix with binder phase enriched surface region, coating adopts thin TiN/MTCVD/TiCO/ α-Al
2O
3The laminated coating design.The present invention is according to the cutting tip rake face, cutting edge, the functional characteristic at back knife face position is optimized design to the cutting edge structure with binder phase enriched surface region blade and improves, adopt the design that keeps the binder phase enriched surface region at rake face, expose a cube carboritride enrichment region at the cutting edge place, adopt the binder phase enriched surface region of thin layer or do not have the design of binder phase enriched surface region at the back knife face, these three characteristics can effectively be avoided collapsing scarce because of the cutting edge that the fire check expansion causes in conjunction with the cutting edge structure that forms, the wear of the tool flank that burning cutter that plastic deformation causes and work hardening cause, can be when improving cutting edge strength, improve carbide chip greatly before, the antiwear property of back knife face.
In addition, the present invention is optimized by thickness and the microstructure to binder phase enriched surface region, cube carboritride enrichment region and laminated coating, make hard alloy coated blade of the present invention have excellent comprehensive performances more, in steel and stainless Milling Process, demonstrate its good high-temperature performance, high tenacity and anti-wear performance.
Description of drawings
Fig. 1 is the structural representation of carbide chip in the embodiment of the invention 1.
Fig. 2 is the structural representation of carbide chip in the embodiment of the invention 2.
Fig. 3 is the structural representation of contrast product A in the specific embodiment of the invention.
Marginal data:
1, hard alloy substrate; 11, rake face; 12, back knife face; 13, cutting edge; 14, homogeneous phase alloy zone; 15, cube carboritride enrichment region; 16, binder phase enriched surface region; 17, intersectional region; 2, coating; 21, TiN layer; 22, TiCN layer; 23, TiCO transition zone; 24, α-Al
2O
3Layer.
The specific embodiment
A kind of hard alloy coated blade that is used for steel and stainless steel milling of the present invention as shown in Figure 1, comprise hard alloy substrate 1 and the coating 2 that applies on it, hard alloy substrate 1 comprises that at least one intersects formed cutting edge 13 by rake face 11 and back knife face 12, the carbide alloy that cutting edge 13 both sides are positioned at rake face 11 and back knife face 12 all presents the graded structure, this graded structure is meant that the homogeneous phase alloy zone 14 by internal layer carries out the transition to a cube carboritride enrichment region 15, carry out the transition to binder phase enriched surface region 16 again, the intersectional region 17 of graded structure at cutting edge 13 places is mainly a cube carboritride enrichment region, and cube carboritride enrichment surf zone that is exposed to cutting edge 13 places perpendicular to the length L 1 on rake face 11 directions (being about 40 μ m) greater than it perpendicular to the length L 2 (being about 20 μ m) on knife face 12 directions of back;
The TiN layer 21 of-innermost layer, equiax crystal, thickness are 0.5 μ m, mean grain size≤0.5 μ m;
-one deck TiCN layer 22, column crystal, thickness are 6 μ m, and mean grain size is 0.8 μ m;
-one deck TiCO transition zone 23, thickness are 0.5 μ m, and this layer crystal grain is an acicular grains, mean grain size≤0.5 μ m;
-outermost α-Al
2O
3Layer 24, thickness is 1.5 μ m, equi-axed crystal, mean grain size is 1.1 μ m, the surface roughness Ra that records on the length of 300 μ m=0.25 μ m.
The preparation method of the hard alloy coated blade that is used for steel and stainless steel milling of present embodiment is as follows: with tungsten carbide powder, cobalt powder (Co) is mixed with into uniform powder mixture with cubic carbonitride or by the solid solution additive that these cubes compound is formed, and powder mixture suppressed, adopt the gradient sintering technology to carry out sintering then (at 1440 ℃ of following sintering, cool off taking off under the N atmosphere behind the high temperature sintering), form one deck binder phase enriched surface region 16 on hard alloy substrate 1 surface, form one deck cube carboritride enrichment region 15 16 times at the binder phase enriched surface region.The thickness of binder phase enriched surface region 16 is 30 μ m, and the content of Co is 1.3 times of Co nominal content in the hard alloy substrate 1 in it; The thickness L5 of cube carboritride enrichment region 15 is 50 μ m, and content of carboritride is 1.2 times of carboritride nominal content in the hard alloy substrate 1 in it.The composition of the hard alloy substrate with gradient-structure 1 that this method makes includes the Ti of Co, 1wt% of 10wt% and the cubic carbonitride of Ta, and surplus is WC..Then, the hard alloy substrate with gradient-structure 1 that sintering is prepared adopts the binder phase enriched surface region 16 that grinds removal back knife face 12, with the nylon bruss that contains SiC cutting edge 13 is carried out sphering again and handle, obtain the hard alloy substrate 1 of the hard alloy coated blade that is used for steel and stainless steel milling of present embodiment.As shown in Figure 1, L4=0, and be positioned at rake face 11 and still remain 30 μ m near the thickness L3 of the binder phase enriched surface region 16 in cutting edge 13 zones.
Above-mentioned carbide blade base 1 is deposited following coating in same coating cycle:
1) utilize existing C VD method on hard alloy substrate 1, to deposit the above-mentioned TiN layer 21 of one deck earlier;
2) utilize MTCVD technology (also can utilize the CVD method) on TiN layer 21, to deposit the above-mentioned TiCN layer 22 of one deck then and (be specially TiC
0.5N
0.5Layer);
3) utilize existing C VD method on TiCN layer 22, to deposit the above-mentioned TiCO transition zone 23 of one deck again;
4) utilize the CVD method on TiCO transition zone 23, to deposit the above-mentioned α-Al of one deck at last
2O
3Layer 24 obtains the hard alloy coated blade that is used for steel product turning of present embodiment as outermost layer.
Hard alloy coated blade to the above-mentioned present embodiment that makes adopts surface treatments such as sandblast, siliceous nylon bruss polishing, the surface roughness Ra that records=0.25 μ m on the length of 300 μ m.
Embodiment 2:
A kind of hard alloy coated blade that is used for steel and stainless steel milling of the present invention as shown in Figure 2, comprise hard alloy substrate 1 and the coating 2 that applies on it, hard alloy substrate 1 comprises that at least one intersects formed cutting edge 13 by rake face 11 and back knife face 12, the carbide alloy that cutting edge 13 both sides are positioned at rake face 11 and back knife face 12 all presents the graded structure, this graded structure is meant that the homogeneous phase alloy zone 14 by internal layer carries out the transition to a cube carboritride enrichment region 15, carry out the transition to binder phase enriched surface region 16 again, the intersectional region 17 of graded structure at cutting edge 13 places is mainly a cube carboritride enrichment region, and cube carboritride enrichment surf zone that is exposed to cutting edge 13 places perpendicular to the length L 1 on rake face 11 directions (being about 40 μ m) greater than it perpendicular to the length L 2 (being about 10 μ m) on knife face 12 directions of back;
The TiN layer 21 of-innermost layer, equiax crystal, thickness are 0.5 μ m, mean grain size≤0.5 μ m;
-one deck TiCN layer 22, column crystal, thickness are 5 μ m, and mean grain size is 0.8 μ m;
-one deck TiCO transition zone 23, acicular grains, thickness is 0.5 μ m, mean grain size≤0.5 μ m;
-outermost α-Al
2O
3Layer 24, equi-axed crystal, thickness are 3 μ m, mean grain size is 1.1 μ m, the surface roughness Ra that records on the length of 300 μ m=0.25 μ m.
The preparation method of the hard alloy coated blade that is used for steel product turning of present embodiment is as follows: with tungsten carbide powder, cobalt powder (Co) is mixed with into uniform powder mixture with cubic carbonitride or by the solid solution additive that these cubes compound is formed, and powder mixture suppressed, adopt the gradient sintering technology to carry out sintering then (at 1440 ℃ of following sintering, cool off taking off under the N atmosphere behind the high temperature sintering), form one deck binder phase enriched surface region 16 on hard alloy substrate 1 surface, form one deck cube carboritride enrichment region 15 16 times at the binder phase enriched surface region; The thickness of binder phase enriched surface region 16 is 40 μ m, and the content of Co is 1.2 times of Co nominal content in the hard alloy substrate 1 in it; The thickness L5 of cube carboritride enrichment region 15 is 60 μ m, and content of carboritride is 1.2 times of carboritride nominal content in the hard alloy substrate 1 in it.The composition of the hard alloy substrate with gradient-structure 1 that this method makes includes the Ti of Co, 3wt% of 8wt% and the cubic carbonitride of Ta, and surplus is WC; Then, to the hard alloy substrate for preparing 1 with gradient-structure adopt with blade after the mode at 12 one-tenth 80 ° of angles of knife face this blade is carried out the wet abrasive blasting processing, make blade cutting edge 13 spherings, part is removed the binder phase enriched surface region on knife face 12 top layers, back simultaneously, make and be positioned at back knife face 12 and be about 10 μ m near the thickness L4 of the binder phase enriched surface region in cutting edge 13 zones, and be positioned at rake face 11 and still remain 40 μ m near the thickness L3 of the binder phase enriched surface region in cutting edge 13 zones, obtain the hard alloy substrate 1 that is used for steel and stainless steel milling of present embodiment.Adopt the painting method identical to carry out coating again, obtain the hard alloy coated blade that is used for steel and stainless steel milling of present embodiment by above-mentioned coating structure with embodiment 1.
The contrast experiment
Contrast product A
Be mixed with into uniform powder mixture with tungsten carbide powder, cobalt powder (Co) and cubic carbonitride or by the solid solution additive that these cubes compound is formed, and powder mixture suppressed, adopt the gradient sintering technology to carry out sintering then (at 1440 ℃ of following sintering, cool off taking off under the N atmosphere behind the high temperature sintering), form one deck binder phase enriched surface region 16 in cemented carbide substrate surfaces, form one deck cube carboritride enrichment region 15 16 times at the binder phase enriched surface region, cube carboritride enrichment region 15 belows are homogeneous phase alloy zone 14; The thickness of this binder phase enriched surface region is 20 μ m, and the content of Co is 1.3 times of Co nominal content in the hard alloy substrate in the binder phase enriched surface region; The thickness L5 of cube carboritride enrichment region is about 28 μ m, the content of carboritride is 1.2 times of carboritride nominal content in the hard alloy substrate in cube carboritride enrichment region, the hard alloy substrate with gradient-structure that makes is formed the Ti of the Co, the 8.5wt% that include 5wt% and the cubic carbonitride of Ta, and surplus is WC; Then, the hard alloy substrate employing with gradient-structure for preparing is carried out wet abrasive blasting with the mode at blade rake face angle at 45 to this blade to be handled, remove the binder phase enriched surface region of blade cutting edge, make the blade cutting edge sphering, obtain the hard alloy substrate 1 of contrast product A as shown in Figure 3 at last, cube carboritride enrichment surf zone that wherein is exposed to cutting edge 13 places is being 20 μ m perpendicular to the length L on rake face 11 directions 1, and it is 25 μ m perpendicular to the length L 2 on knife face 12 directions of back.
Contrast product B
Select the blade base that has same structure with contrast product A for use, this matrix is deposited following coating in same coating cycle:
1) utilize existing C VD method to deposit the TiN layer 21 of one deck equi-axed crystal earlier, its thickness is 0.5 μ m;
2) utilize MTCVD technology (also can utilize the CVD method) to deposit the TiCxNy layer 22 of one deck columnar grain again, its thickness is 9 μ m, and mean grain size is for being 0.8 μ m;
3) utilize existing C VD method to deposit the TiCO layer 23 of one deck acicular grains then, its thickness is 0.5 μ m;
4) utilize HTCVD deposition techniques one deck compact grained α-Al at last
2O
3Layer 24 is as outermost layer, and its thickness is 7 μ m, and mean grain size is 1.1 μ m.
Hard alloy coated blade to the above-mentioned present embodiment that makes adopts surface treatments such as sandblast, siliceous nylon bruss polishing, the surface roughness Ra that records=0.25 μ m on the length of 300 μ m.
Contrast product C
Contrast product C is the common coated chip of selling on the existing market, the matrix of this coated chip is formed the Co that includes 9wt%, surplus is WC, blade base does not form the skeleton supporting construction of cube phase enrichment at the cutting edge place, its coating includes thick TiCxNyOz layer of one deck 3 μ m and the thick α-Al of one deck 2.5 μ m
2O
3Outer.
The contrast experiment
The foregoing description 1,2 is as follows with contrast product A, B, C contrast test data and the test result under different machining conditions:
1, milling 45# steel compare test to the anti-wear performance of above-mentioned blade.The cutter life standard is the process time of wear of the tool flank when being 0.25mm.
Machining condition:
| Material | 45# steel (HB170-190) |
| Cutting speed V | ??400m/min、300m/min |
| Feed engagement Fz | ??0.3mm |
| Cutting-in Ap | ??1.5mm |
| Cut wide Ae | ??60 |
| Cooling agent | Do not have |
Test result:
Result of the test shows: in high speed (400m/min, the 300m/min) Milling Process of steel, embodiments of the invention 1,2 are owing to have the cutting edge supporting construction of optimization, the carbide alloy composition and the coating structure of optimization, than contrast product A, B, C (prior art), have obtained obvious improvement in its anti-wear performance and service life.
2, milling 45# steel compare the failure mode of above-mentioned blade.
Machining condition:
| Material | 45# steel (HB170-190) |
| Cutting speed V | ??400m/min |
| Feed engagement Fz | ??0.3mm |
| Cutting-in Ap | ??1.5mm |
| Cut wide Ae | ??60 |
| Material | 45# steel (HB170-190) |
| Time | ??10′ |
| The test blade | 10 |
| Cooling agent | Do not have |
Test result:
Result of the test shows: in high speed (400m/min) Milling Process of steel, embodiments of the invention 1,2 are owing to have the cutting edge supporting construction of optimization, the carbide alloy composition and the coating structure of optimization, than contrast product A, B, C (prior art), the stability of blade has obtained obvious improvement.
3, milling 1Cr18Ni9Ti stainless steel compares test to the anti-wear performance of above-mentioned blade.The cutter life standard is the process time of wear of the tool flank when being 0.2mm.
Machining condition:
| Material | ??NAK80(HB170-190) |
| Cutting speed V | ??180m/min |
| Feed engagement Fz | ??0.2mm |
| Cutting-in Ap | ??1mm |
| Cut wide Ae | ??30 |
| Cooling agent | Do not have |
Test result:
| Test products | Time |
| Embodiments of the |
??48′00″ |
| Embodiments of the |
??42′30″ |
| Contrast product A | ??25′20″ |
| Contrast product B | ??23′00″ |
| Contrast product C | ??36′30″ |
Result of the test shows: in the stainless high-speed milling processing of 1Cr18Ni9Ti, embodiments of the invention 1,2 are owing to have by cube supporting construction that the phase enrichment region forms and the matrix and the coating texture of optimization are arranged, than contrast product A, B, C (prior art), have obtained obvious improvement in the stability of cutter and service life.
Claims (8)
1. hard alloy coated blade that is used for steel and stainless steel milling, comprise hard alloy substrate and the coating that applies on it, described hard alloy substrate comprises that at least one intersects formed cutting edge by rake face and back knife face, the carbide alloy that described cutting edge both sides are positioned at rake face and back knife face all presents the graded structure, this graded structure is meant that the homogeneous phase alloy zone by internal layer carries out the transition to a cube carboritride enrichment region, carry out the transition to the binder phase enriched surface region again, it is characterized in that: described hard alloy substrate comprises the hard phase based on WC, based on the bonding phase of Co with to take from periodic table IVb, cube phase compound of Vb and/or VIb family metallic element; The content of Co is 7wt%～12wt% in the described hard alloy substrate, and the content of described cube of phase compound is 0.2wt%～3.5wt%; The intersectional region of described graded structure at the cutting edge place is mainly a cube carboritride enrichment region, and cube carboritride enrichment surf zone that is exposed to the cutting edge place perpendicular to the length L 1 on the described rake face direction more than or equal to its 2 times perpendicular to the length L 2 on the knife face direction of described back;
Described coating is thin brilliant laminated coating, includes successively from inside to outside:
The TiN layer of-innermost layer, thickness are 0.1 μ m～2 μ m, mean grain size≤0.5 μ m;
-one deck TiCN layer, column crystal, thickness are 1 μ m～6 μ m, and mean grain size is 0.1 μ m～2 μ m;
-one deck TiCO transition zone, thickness are 0.1 μ m～1.5 μ m, and this layer crystal grain is acicular grains or equi-axed crystal, mean grain size≤0.5 μ m;
-outermost α-Al
2O
3Layer, thickness is 1 μ m～5 μ m, equi-axed crystal, mean grain size is 0.1 μ m～2 μ m, the surface roughness Ra that records on the length of 300 μ m≤0.25 μ m.
2. the hard alloy coated blade that is used for steel and stainless steel milling according to claim 1 is characterized in that: be positioned at rake face and near the thickness L3 of the described binder phase enriched surface region in cutting edge zone greater than being positioned at the back knife face and near the thickness L4 of the described binder phase enriched surface region in cutting edge zone; The value of described L3 is 10 μ m≤L3≤70 μ m.
3. the hard alloy coated blade that is used for steel and stainless steel milling according to claim 2 is characterized in that: be positioned at the back knife face and equal zero near the thickness L4 of the described binder phase enriched surface region in cutting edge zone.
4. according to claim 1 or the 2 or 3 described hard alloy coated blades that are used for steel and stainless steel milling, it is characterized in that: the content of described Co is 8wt%～11wt%, and the content of described cube of phase compound is 0.5wt%～2.5wt%.
5. according to claim 1 or the 2 or 3 described hard alloy coated blades that are used for steel and stainless steel milling, it is characterized in that: be positioned at rake face and be 20 μ m≤L3≤50 μ m near the value of the thickness L3 of the described binder phase enriched surface region in cutting edge zone, the content of Co is 1～1.5 times of Co nominal content in the hard alloy substrate in this binder phase enriched surface region.
6. according to claim 1 or the 2 or 3 described hard alloy coated blades that are used for steel and stainless steel milling, it is characterized in that: the thickness of described cube of carboritride enrichment region is 20 μ m～60 μ m, and the content of cube phase compound is 1～1.5 times of cube phase compound nominal content in the hard alloy substrate in this cube carboritride enrichment region.
7. according to claim 1 or the 2 or 3 described hard alloy coated blades that are used for steel and stainless steel milling, it is characterized in that: the thickness of described TiN layer is 0.2 μ m～1 μ m; The thickness of described TiCN layer is 2 μ m～5 μ m; The thickness of described TiCO transition zone is 0.2 μ m～1 μ m; Described α-Al
2O
3The thickness of layer is 1 μ m～3 μ m.
8. according to claim 1 or the 2 or 3 described hard alloy coated blades that are used for steel and stainless steel milling, it is characterized in that: described TiCN layer is middle temperature chemical vapor deposited coatings, and the mean grain size of described TiCN layer is 0.3 μ m～1.5 μ m; Described α-Al
2O
3The mean grain size of layer is 0.4 μ m～1.5 μ m.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2010102111890A CN101870003B (en) | 2010-06-28 | 2010-06-28 | Hard alloy coated tool for milling steel and stainless steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2010102111890A CN101870003B (en) | 2010-06-28 | 2010-06-28 | Hard alloy coated tool for milling steel and stainless steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101870003A true CN101870003A (en) | 2010-10-27 |
| CN101870003B CN101870003B (en) | 2011-12-07 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104099580A (en) * | 2014-05-28 | 2014-10-15 | 厦门金鹭特种合金有限公司 | Cutter coating layer having nanometer columnar crystal for enhancing wear resistance and toughness |
| CN112846259A (en) * | 2021-01-05 | 2021-05-28 | 崇义章源钨业股份有限公司 | Cutter for steel turning and preparation method thereof |
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| EP0408535A1 (en) * | 1989-07-13 | 1991-01-16 | Seco Tools Ab | Multi-oxide coated carbide body and method of producing the same |
| CN1038731C (en) * | 1992-02-21 | 1998-06-17 | 桑德维克公司 | Cemented carbide with binder phase enriched surface zone |
| WO2000052225A1 (en) * | 1999-03-02 | 2000-09-08 | Kennametal Inc. | A tool having a multilayer coating comprising multiple mtcvd layers |
| CN101214743A (en) * | 2008-01-11 | 2008-07-09 | 株洲钻石切削刀具股份有限公司 | Coating blade for processing cast iron |
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| US4610931A (en) * | 1981-03-27 | 1986-09-09 | Kennametal Inc. | Preferentially binder enriched cemented carbide bodies and method of manufacture |
| EP0408535A1 (en) * | 1989-07-13 | 1991-01-16 | Seco Tools Ab | Multi-oxide coated carbide body and method of producing the same |
| CN1038731C (en) * | 1992-02-21 | 1998-06-17 | 桑德维克公司 | Cemented carbide with binder phase enriched surface zone |
| WO2000052225A1 (en) * | 1999-03-02 | 2000-09-08 | Kennametal Inc. | A tool having a multilayer coating comprising multiple mtcvd layers |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104099580A (en) * | 2014-05-28 | 2014-10-15 | 厦门金鹭特种合金有限公司 | Cutter coating layer having nanometer columnar crystal for enhancing wear resistance and toughness |
| CN112846259A (en) * | 2021-01-05 | 2021-05-28 | 崇义章源钨业股份有限公司 | Cutter for steel turning and preparation method thereof |
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| Publication number | Publication date |
|---|---|
| CN101870003B (en) | 2011-12-07 |
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