CN116140661A - Residual stress toughened metal ceramic cutter and processing system thereof - Google Patents
Residual stress toughened metal ceramic cutter and processing system thereof Download PDFInfo
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- CN116140661A CN116140661A CN202310042478.XA CN202310042478A CN116140661A CN 116140661 A CN116140661 A CN 116140661A CN 202310042478 A CN202310042478 A CN 202310042478A CN 116140661 A CN116140661 A CN 116140661A
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- 229910052751 metal Inorganic materials 0.000 title claims abstract description 34
- 239000002184 metal Substances 0.000 title claims abstract description 34
- 239000000919 ceramic Substances 0.000 title claims abstract description 25
- 238000012545 processing Methods 0.000 title claims abstract description 14
- 239000011159 matrix material Substances 0.000 claims abstract description 49
- 238000000034 method Methods 0.000 claims abstract description 28
- 238000005245 sintering Methods 0.000 claims abstract description 18
- 238000005728 strengthening Methods 0.000 claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 claims abstract description 9
- 230000000694 effects Effects 0.000 claims abstract description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 239000000463 material Substances 0.000 claims description 30
- 239000000758 substrate Substances 0.000 claims description 22
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- 239000011248 coating agent Substances 0.000 claims description 14
- 238000000576 coating method Methods 0.000 claims description 14
- 238000003754 machining Methods 0.000 claims description 10
- 238000001514 detection method Methods 0.000 claims description 9
- 239000004615 ingredient Substances 0.000 claims description 9
- 238000005488 sandblasting Methods 0.000 claims description 9
- 230000003014 reinforcing effect Effects 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 7
- 238000005422 blasting Methods 0.000 claims description 7
- 238000005516 engineering process Methods 0.000 claims description 7
- 238000012360 testing method Methods 0.000 claims description 7
- 239000010936 titanium Substances 0.000 claims description 7
- 229910052719 titanium Inorganic materials 0.000 claims description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 239000002994 raw material Substances 0.000 claims description 6
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 5
- 229920000049 Carbon (fiber) Polymers 0.000 claims description 4
- 239000004917 carbon fiber Substances 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 4
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 3
- 239000007789 gas Substances 0.000 claims description 3
- 238000000227 grinding Methods 0.000 claims description 3
- 229910052739 hydrogen Inorganic materials 0.000 claims description 3
- 239000001257 hydrogen Substances 0.000 claims description 3
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 claims description 3
- 238000002156 mixing Methods 0.000 claims description 3
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- 238000010521 absorption reaction Methods 0.000 abstract description 2
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- 239000010410 layer Substances 0.000 description 109
- 239000011195 cermet Substances 0.000 description 12
- 238000005520 cutting process Methods 0.000 description 12
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 5
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 3
- 229910010293 ceramic material Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 230000000670 limiting effect Effects 0.000 description 3
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- 230000004048 modification Effects 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
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- 230000000737 periodic effect Effects 0.000 description 2
- OFNHPGDEEMZPFG-UHFFFAOYSA-N phosphanylidynenickel Chemical compound [P].[Ni] OFNHPGDEEMZPFG-UHFFFAOYSA-N 0.000 description 2
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- 239000000126 substance Substances 0.000 description 2
- 208000010392 Bone Fractures Diseases 0.000 description 1
- 229910017488 Cu K Inorganic materials 0.000 description 1
- 229910017541 Cu-K Inorganic materials 0.000 description 1
- 206010017076 Fracture Diseases 0.000 description 1
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 1
- 229910001634 calcium fluoride Inorganic materials 0.000 description 1
- 238000005229 chemical vapour deposition Methods 0.000 description 1
- 230000002860 competitive effect Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
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- 230000007774 longterm Effects 0.000 description 1
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- 239000012779 reinforcing material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 150000003609 titanium compounds Chemical class 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000001238 wet grinding Methods 0.000 description 1
- 229910052724 xenon Inorganic materials 0.000 description 1
- FHNFHKCVQCLJFQ-UHFFFAOYSA-N xenon atom Chemical compound [Xe] FHNFHKCVQCLJFQ-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
- B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
- B22F3/1007—Atmosphere
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
- C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
- C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
- C23C16/36—Carbonitrides
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
- C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
- C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
- C23C16/40—Oxides
- C23C16/403—Oxides of aluminium, magnesium or beryllium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/241—Chemical after-treatment on the surface
- B22F2003/242—Coating
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/247—Removing material: carving, cleaning, grinding, hobbing, honing, lapping, polishing, milling, shaving, skiving, turning the surface
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Inorganic Chemistry (AREA)
- General Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Composite Materials (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
The invention provides a residual stress toughened metal ceramic cutter and a processing system thereof, wherein the cutter takes Ti (C, N) -based metal ceramic as a cutter matrix, and a toughening layer is arranged on the surface of the matrix; the toughening layer is provided with an outer layer and an inner layer which are the same in composition but different in composition, so that residual compressive stress is generated after the toughening layer is sintered and formed, and the toughening effect is provided through the residual compressive stress; and by providing a strengthening layer over the toughening layer; the reinforced layer consists of metal components with gradually-changed heat absorption coefficients, a certain amount of residual compressive stress is generated through gradual linear change among multiple layers in the sintering process, and finally, the toughening effect of the cutter is realized through the residual stress toughening principle; and the processing system for producing the cutter is provided, so that continuous monitoring of sintering and residual stress is realized, and the production efficiency and the quality of finished products of the cutter are improved.
Description
Technical Field
The present invention relates to the field of machining. In particular to a residual stress toughened metal ceramic cutter and a processing system thereof.
Background
The metal ceramic cutter material has the advantages of high hardness, good wear resistance, high temperature resistance, stable chemical property, low affinity with metal and the like, has the advantages that the traditional high-speed steel and hard alloy cutters are difficult to compare in the field of high-speed cutting, can be used for processing difficult-to-process materials such as quenched steel, nickel-based alloy and the like, and is called the most promising and competitive cutter material at present. However, low fracture toughness is a major factor limiting the development of cermet tools. The chemical bond in the metal ceramic material is mainly covalent bond and ionic bond, so that the metal ceramic material has strong directivity and high bonding strength, and is difficult to generate dislocation movement, so that the plastic deformation capability is poor, and the service life of the cutter is obviously influenced by the brittleness characteristic.
At present, various toughening modes are proposed for metal ceramic cutters. According to the disclosed technical scheme, the technical scheme with the publication number of CN106810259A provides a self-lubricating ceramic cutter material added with nickel-phosphorus alloy coated calcium fluoride composite powder and a preparation method thereof, and the microstructure of the self-lubricating ceramic cutter material is improved by coating nickel-phosphorus alloy on the surface of the cutter, so that the self-lubricating ceramic cutter material is toughened and reinforced; the technical proposal with the publication number KR20210020054A provides a process for overcoming the edge structure of the prior cermet reactor core, wherein the reinforced material with a plurality of coating layers is manufactured by particles in a complete solid solution phase of carbide of two or more metals selected from IVa group, va group and VIa group in the periodic table of elements, so that the toughness performance of the cermet is effectively improved; the solution disclosed in JP2013108134a proposes a composite cermet material comprising at least an iron group metal as a binder phase and at least one or more carbides, nitrides and carbonitrides of metals selected from groups IVa, va and VIa of the periodic table as a cemented carbide phase, wherein the cermet contains 0.4 to 20% by mass of Cu and/or Zn and has properties equivalent to those of the iron group metal, thereby improving the toughness of the cermet.
The above solutions all refer to solutions for improving the cermet by means of reinforcing materials or applying new materials, however, there is no mention of solutions for improving the toughness of the cermet by improving the manufacturing process.
The foregoing discussion of the background art is intended to facilitate an understanding of the present invention only. This discussion is not an admission or admission that any of the material referred to was common general knowledge.
Disclosure of Invention
The invention aims to provide a residual stress toughened metal ceramic cutter and a processing system thereof; the cutter takes TiCN-based metal ceramic as a cutter matrix, and a toughening layer is arranged on the surface of the matrix; the toughening layer is provided with an outer layer and an inner layer which are the same in composition but different in composition, so that residual compressive stress is generated after the toughening layer is sintered and formed, and the toughening effect is provided through the residual compressive stress; and by providing a strengthening layer over the toughening layer; the reinforced layer is composed of metal components with gradually changed heat absorption coefficients, a certain amount of residual compressive stress is generated by gradually changing the metal components between multiple layers in the sintering process, and finally the cutter has a toughening effect by the residual stress toughening principle.
The invention adopts the following technical scheme:
a residual stress toughened cermet tool comprising a substrate and a composite coating on a surface of the substrate; among them
The matrix is a metal ceramic base material, and the metal ceramic base material is TiCN-based metal ceramic;
the composite coating comprises a toughening layer and a strengthening layer which are sequentially covered on the matrix;
the toughening layer is provided with an outer layer and an inner layer which have the same components but different components, so that the toughening layer generates residual compressive stress after being sintered and formed, and the toughening effect is provided through the residual compressive stress;
the strengthening layer at least comprises a titanium carbonitride layer and an alumina layer;
wherein the matrix is required to have a thickness of 8.5-9.0 x 10 -6 Linear expansion coefficient of/K and thermal conductivity of 20W/mK or more; and, in addition, the processing unit,
the surface of the forming layer of the toughening layer and the surface of the forming layer of the reinforcing layer are respectively provided with residual compressive stress with the numerical value of 200-800 MPa;
preferably, the materials of the outer layer and the inner layer of the toughening layer comprise alumina, zirconium dioxide and carbon fibers; and the mass ratio of the three materials in the outer layer is different from the mass ratio of the three materials in the inner layer;
preferably, after the toughening layer is formed, wet blasting process treatment is carried out on the surface of the substrate on which the toughening layer is formed;
preferably, after the wet blasting process treatment, at least one residual compressive stress test is performed to determine whether the surface residual stress of the substrate reaches a desired level; if the expected value is not reached, continuing to perform wet sand blasting;
preferably, a method of manufacturing adapted to said tool is included; the manufacturing method comprises the following steps:
s100: preparing materials, namely preparing ingredients of each component according to the formula proportion of the matrix; grinding and mixing the ingredients by adopting a ball mill to enable the ingredients to become mixed powdery materials, and respectively obtaining powdery raw materials of a matrix, a toughening layer and a reinforcing layer;
s200: prepressing and forming, namely prepressing and forming the powdery raw materials of the matrix to obtain a first formed body;
s300: coating an inner layer and an outer layer of the toughening layer on the surface of the first molded body in sequence, and performing pressing again to obtain a pre-pressed molded body;
s400: sintering the pre-pressed molding body to obtain a matrix with a toughening layer formed on the surface;
s500: wet sanding technology is adopted on the surface of the substrate on which the toughening layer is formed after sintering;
s600: forming a strengthening layer on the surface of the substrate on which the toughening layer is formed by a vapor deposition method;
preferably, in step S400, the following sub-steps are included:
s410: heating the pre-pressed molded body to 1200 ℃ and then preserving heat;
s420: sintering the pre-pressed molded body at 1350 ℃ to 1450 ℃ for 90 minutes to 120 minutes, and simultaneously flowing a mixed gas atmosphere of hydrogen with a volume concentration of 1 to 3% and nitrogen with a volume concentration of 97 to 99% in a sintering furnace during the sintering process;
s430: then cooling to 1200 ℃ at a speed of 10 ℃/min;
further, the method includes employing a machining system for machining the tool; the processing system comprises a continuous section; the continuous working section comprises a wet sanding working section and a detection working section; the detection section comprises the step of detecting the residual stress of the matrix after forming the toughening layer by adopting an X-ray residual stress detection technology.
The beneficial effects obtained by the invention are as follows:
1. the TiCN-based metal ceramic with the special modulation component is used as the matrix of the cutter, and the linear expansion coefficient and the thermal conductivity of the TiCN-based metal ceramic are both larger than those of the composite coating on the surface of the matrix, so that the deformation of the matrix generated by the heat generated by the cutter in high-speed cutting can be larger than that of the composite coating, thereby generating compressive stress on the composite coating, inhibiting further expansion of surface thermal cracks, reducing the fracture risk of the cutter, and macroscopically showing that the toughness of the cutter is improved;
2. according to the cutter, through the toughening layer arranged on the further substrate and with different compositions between the outer layer and the inner layer, certain residual compressive stress is generated after the toughening layer is sintered and formed, so that the toughness of the cutter is further improved;
3. the cutter disclosed by the invention is matched with a production system using an X-ray diffraction principle to perform online continuous monitoring and surface sand blasting treatment, so that the residual stress finally formed on the reinforced layer by the cutter produced in the same batch is as consistent as possible, and the consistency of the service performance of the product is ensured.
Drawings
The invention will be further understood from the following description taken in conjunction with the accompanying drawings. The components in the figures are not necessarily to scale, emphasis instead being placed upon illustrating the principles of the embodiments. Like reference numerals designate corresponding parts throughout the different views.
FIG. 1 is a schematic layered view of a tool according to the present invention;
FIG. 2 is a schematic diagram of steps for producing the tool according to the embodiment of the invention;
FIG. 3 is a schematic view of microscopic observations of the surface of a substrate after a wet sanding process in accordance with an embodiment of the present invention.
Reference numerals illustrate:
110-matrix; 120-a toughening layer; 121-an outer layer; 122-an inner layer; 130-strengthening layer.
Detailed Description
In order to make the technical scheme and advantages of the present invention more apparent, the present invention will be further described in detail with reference to the following examples thereof; it should be understood that the specific embodiments described herein are for purposes of illustration only and are not intended to limit the scope of the invention. Other systems, methods, and/or features of the present embodiments will be or become apparent to one with skill in the art upon examination of the following detailed description. It is intended that all such additional systems, methods, features and advantages be included within this description, be within the scope of the invention, and be protected by the accompanying claims. Additional features of the disclosed embodiments are described in, and will be apparent from, the following detailed description.
The same or similar reference numbers in the drawings of embodiments of the invention correspond to the same or similar components; in the description of the present invention, it should be understood that, if there is an orientation or positional relationship indicated by the terms "upper", "lower", "left", "right", etc., based on the orientation or positional relationship shown in the drawings, this is for convenience of description and for simplification of the description, rather than to indicate or imply that the apparatus or component referred to must have a specific orientation.
Embodiment one:
as shown in fig. 1, a residual stress toughened metal ceramic tool comprises a substrate and a composite coating on the surface of the substrate; among them
The substrate 110 is a metal ceramic base material, and the metal ceramic base material is TiCN-based metal ceramic;
the composite coating comprises a toughening layer 120 and a strengthening layer 130 which are sequentially covered on the substrate 110;
the toughening layer 120 has the same components, but different components of the outer layer 121 and the inner layer 122, so that the toughening layer generates residual compressive stress after being sintered, and the toughening effect is provided by the residual compressive stress;
the strengthening layer 130 comprises at least a titanium carbonitride layer and an aluminum oxide layer;
wherein the matrix is required to have a thickness of 8.5-9.0 x 10 -6 Linear expansion coefficient of/K and thermal conductivity of 20W/mK or more; and, in addition, the processing unit,
the surface of the forming layer of the toughening layer and the surface of the forming layer of the reinforcing layer are respectively provided with residual compressive stress with the numerical value of 200-800 MPa;
preferably, the outer layer of the toughening layer is made of alumina, zirconium dioxide and carbon fiber with the weight ratio of 55-75: 13 to 18:6 to 12 mass portions; the inner layer of the toughening layer is formed by 35 to 55 percent of aluminum oxide, zirconium dioxide and carbon fiber: 33 to 38:6 to 12 mass portions;
preferably, the thickness of the outer layer and the inner layer of the toughening layer is 500-800 μm;
preferably, after forming the toughening layer, wet blasting is performed on the surface of the substrate 110 on which the toughening layer is formed;
preferably, after the wet blasting process treatment, at least one residual compressive stress test is performed to determine whether the surface residual stress of the substrate reaches a desired level; if the expected value is not reached, continuing to perform wet sand blasting;
preferably, the TiCN-based cermet adopted by the matrix consists of 30-62 parts by weight of TiCN phase and 5-25 parts by weight of Mo 2 Phase C, and the rest of the bonding phase; and the composition of the combined phase includes Fe and Ni;
preferably, a method of manufacturing adapted to said tool is included; the manufacturing method comprises the following steps:
s100: preparing materials, namely preparing ingredients of each component according to the formula proportion of the matrix; grinding and mixing the ingredients by adopting a ball mill to enable the ingredients to become mixed powdery materials, and respectively obtaining powdery raw materials of a matrix, a toughening layer and a reinforcing layer;
s200: prepressing and forming, namely prepressing and forming the powdery raw materials of the matrix to obtain a first formed body;
s300: coating an inner layer and an outer layer of the toughening layer on the surface of the first molded body in sequence, and performing pressing again to obtain a pre-pressed molded body;
s400: sintering the pre-pressed molding body to obtain a matrix with a toughening layer formed on the surface;
s500: wet sanding technology is adopted on the surface of the substrate on which the toughening layer is formed after sintering;
s600: forming a strengthening layer on the surface of the substrate on which the toughening layer is formed by a vapor deposition method;
preferably, in step S400, the following sub-steps are included:
s410: heating the pre-pressed molded body to 1200 ℃ and then preserving heat;
s420: sintering the pre-pressed molded body at 1350 ℃ to 1450 ℃ for 90 minutes to 120 minutes, and simultaneously flowing a mixed gas atmosphere of hydrogen with a volume concentration of 1 to 3% and nitrogen with a volume concentration of 97 to 99% in a sintering furnace during the sintering process;
s430: then cooling to 1200 ℃ at a speed of 10 ℃/min;
further, it includes proposing a machining system for machining the tool; the processing system comprises a continuous section; the continuous working section comprises a wet sanding working section and a detection working section; the detection working section comprises the step of detecting the residual stress of the matrix after forming the toughening layer by adopting an X-ray residual stress detection technology;
the research on the used materials of the matrix shows that the cermet taking TiCN as the matrix has the characteristics of high hardness and high strength, can obviously have longer service life compared with the traditional hard metal matrix cutter, and is suitable for (semi) finish machining of bearing steel and common steel;
in some embodiments, the TiCN-based cermet has an expression of tic0.7n0.3, and the total formulation comprises the following material components in weight percent: tiC0.7N0.3: 40-50%, WC: 5-10%, mo 2 C: 5-10%, ni: 5-10%, co: 5-10% of (W, ti, ta, nb) C polynary complex carbide;
in some embodiments, tiCN has the expression tic0.7n0.3, and the remainder has the composition tic0.7n0.3: 30-62%, co:6 to 10 percent of Mo 2 C: 6-10%, ni: 6-10%, five-membered solid solution: 20-40%;
in some embodiments, the matrix has TiCN, tiC, WC, taNbC, mo C and Cr3C2 as hard phases, co and Ni as binder phases, and Co-Rh-Os master alloy as an additive; the TiCN-based metal ceramic material comprises the following components in percentage by weight: 45-60% of TiCN, 1-5% of TiC, 12-18% of WC, 6-12% of TaNbC and Mo 2 C is 5-12%, cr 3 C 2 0.3 to 1 percent, 6 to 11 percent of Co, 3 to 8 percent of Ni and 1 to 5 percent of intermediate alloy;
the test shows that the Vickers hardness of the sintered matrix material can reach more than 12GPa, the highest Vickers hardness can reach 14.96GPa (HV 20), and the fracture toughness is 8.5MPa m 1/2 The above;
and TiCN-based cermets have excellent thermal conductivity and are more suitableA suitable linear expansion coefficient; wherein the matrix is preferably required to have a value of 8.5 to 9.0 x 10 -6 Linear expansion coefficient of/K and thermal conductivity of 20W/mK or more; in actual operation, the content of each component of the matrix can be adjusted according to the linear expansion coefficient and the thermal conductivity measured after the experiment;
preferably, the linear expansion coefficient of the matrix may be measured, for example, with an dilatometer, and the thermal conductivity of the matrix may be measured, for example, with a xenon flash analyzer;
further, the matrix forming the toughening layer is subjected to wet sand blasting by using particles with the size of 10-150 mu m to reduce residual tensile stress or increase residual compressive stress and reduce surface roughness so as to enhance the deposition effect of the strengthening layer;
preferably, the surface roughness of the substrate surface on which the toughening layer is formed is 0.12 to 0.4 μm;
preferably, the particles for wet blasting are sprayed directly onto the substrate surface using compressed air at a pressure of 3.5 to 5.0 bar;
the residual stress of the matrix is converted from tensile stress to compressive stress, or the residual tensile stress is reduced, or the residual compressive stress is increased through wet sand blasting, so that the toughness of the surface of the matrix is improved; meanwhile, the surface roughness of the outer layer or the outermost layer of the matrix is reduced, so that the peeling and tipping of the reinforcement layer deposited at the later stage are restrained; at the same time, a microscope is used for observing the surface of the toughened layer after sand blasting, as shown in figure 3, before sand blasting treatment is carried out on the surface of the toughened layer in the figure (A), a large number of uneven burrs exist on the surface; after the sand blasting of the graph (B) is finished, the surface has higher flatness;
further, by adding the toughening layer, the residual compressive stress of the matrix can be kept on the surface of the matrix and is continuously stable, so that the toughness of the matrix is further increased;
as proved by experiments, after the toughening layer is added, the fracture toughness can reach 8 MPa-m 1/2 The above.
Embodiment two:
this embodiment should be understood to include at least all of the features of any one of the foregoing embodiments, and further improvements thereto:
the strengthening layer of the present embodiment preferably includes at least one of a titanium carbonitride layer and an aluminum oxide layer formed by using a chemical vapor deposition method or a physical vapor deposition method; however, other reinforcing layers are additionally added, and titanium compound layers such as a titanium carbide layer, a titanium nitride layer and the like, composite nitride layers of titanium and aluminum, composite oxide layers, composite nitride layers, composite oxide layers and other hard layers known in the art are not excluded;
in addition, the residual compressive stress of the strengthening layer (preferably, the titanium carbonitride layer and/or the aluminum oxide layer) can be reduced by using Cu-K alpha rays
As a radiation source, sin was used 2 The psi method, under the conditions of a scanning step length of 0.013 degrees and each measuring time of 0.48 seconds/step, measuring and calculating the surface residual compressive stress value of the reinforced layer;
in some embodiments, a hard coating layer composed of an aluminum oxide layer, the residual stress is calculated by using the diffraction peak of the (1310) plane, using a Young's modulus of 384GPa and a Poisson's ratio of 0.232. For example, regarding a hard coat layer composed of a titanium carbonitride layer, using a Young's modulus of 475GPa and a Poisson's ratio of 0.2, residual stress was calculated by using a diffraction peak of the (422) plane;
by arranging the reinforcing layer, the hardness and the impact resistance of the surface of the cutter at high temperature can be obviously improved; in particular, after the heat conductivity of the surface is improved, high-temperature heat in the high-speed cutting process can be quickly conducted from the blade part to the whole cutter body, and the residual compressive stress in the base body can be maintained by utilizing the heat.
Embodiment III:
this embodiment should be understood to include at least all of the features of any one of the foregoing embodiments, and further improvements thereto:
the following data were measured through practical machining experiments, and the following table shows that the tool based on the above settings performs better due to the composite coating, enabling a longer service life and faster cutting efficiency of the tool:
processing material for test: national standard 42CrMo cube;
cutting speed: 800m/min;
depth of cut: 1mm;
feed amount: 0.2mm/r;
cutting time: 15min;
the remaining conditions: wet milling, measuring the wear width of the rear cutter surface of the cutting edge, and observing the wear state of the cutting edge by a microscope:
table 1:
the units of the residual compressive stress in the table are all Mpa;
meanwhile, after a large number of test pieces are continuously processed, the surfaces of the test pieces are observed, and even if intermittent and impact mechanical loads and thermal loads caused by rapid heating and rapid cooling thermal cycles are applied to the cutting edge during the cutting process, the cutting edge breakage which obviously affects the cutting life does not occur, and the cutter of the invention shows excellent wear resistance after long-term use.
In the foregoing embodiments, the descriptions of the embodiments are emphasized, and in part, not described or illustrated in any particular embodiment, reference is made to the related descriptions of other embodiments.
While the invention has been described above with reference to various embodiments, it should be understood that many changes and modifications can be made without departing from the scope of the invention. That is, the methods, systems and devices discussed above are examples. Various configurations may omit, replace, or add various procedures or components as appropriate. For example, in alternative configurations, the methods may be performed in a different order than described, and/or various components may be added, omitted, and/or combined. Moreover, features described with respect to certain configurations may be combined in various other configurations, such as different aspects and elements of the configurations may be combined in a similar manner. Furthermore, as the technology evolves, elements therein may be updated, i.e., many of the elements are examples, and do not limit the scope of the disclosure or the claims.
Specific details are given in the description to provide a thorough understanding of exemplary configurations involving implementations. However, configurations may be practiced without these specific details, e.g., well-known circuits, processes, algorithms, structures, and techniques have been shown without unnecessary detail in order to avoid obscuring configurations. This description provides only an example configuration and does not limit the scope, applicability, or configuration of the claims. Rather, the foregoing description of the configuration will provide those skilled in the art with an enabling description for implementing the described techniques. Various changes may be made in the function and arrangement of elements without departing from the spirit or scope of the disclosure.
It is intended that the foregoing detailed description be regarded as illustrative rather than limiting, and that it be understood that it is intended that it be regarded as illustrative rather than limiting. Various changes and modifications to the present invention may be made by one skilled in the art after reading the teachings herein, and such equivalent changes and modifications are intended to fall within the scope of the invention as defined in the appended claims.
Claims (7)
1. A residual stress toughened metal ceramic cutter, which is characterized by comprising a matrix and a composite coating on the surface of the matrix; wherein,,
the matrix is a metal ceramic base material, and the metal ceramic base material is TiCN-based metal ceramic;
the composite coating comprises a toughening layer and a strengthening layer which are sequentially covered on the matrix;
the toughening layer is provided with an outer layer and an inner layer which have the same components but different components, so that the toughening layer generates residual compressive stress after being sintered and formed, and the toughening effect is provided through the residual compressive stress;
the strengthening layer at least comprises a titanium carbonitride layer and an alumina layer;
wherein the matrix is required to have a thickness of 8.5-9.0 x 10 -6 /kLinear expansion coefficient and thermal conductivity of 20W/mK or more; and, in addition, the processing unit,
the surfaces of the forming layers of the toughening layer and the reinforcing layer are respectively provided with residual compressive stress with the numerical value of 200-800 MPa.
2. The cutter according to claim 1, wherein the materials of the outer layer and the inner layer of the toughening layer comprise alumina, zirconia and carbon fiber; and the mass ratio of the three materials in the outer layer is different from that in the inner layer.
3. The tool of claim 2, wherein after forming the toughening layer, the surface of the substrate on which the toughening layer is formed is subjected to a wet blasting process.
4. The tool of claim 3, wherein after the wet blasting process, at least one residual compressive stress test is performed to determine whether the surface residual stress of the substrate is expected; if the expected value is not reached, the wet sand blasting treatment is continued.
5. The tool according to claim 4, comprising a manufacturing method adapted to said tool; the manufacturing method comprises the following steps:
s100: preparing materials, namely preparing ingredients of each component according to the formula proportion of the matrix; grinding and mixing the ingredients by adopting a ball mill to enable the ingredients to become mixed powdery materials, and respectively obtaining powdery raw materials of a matrix, a toughening layer and a reinforcing layer;
s200: prepressing and forming, namely prepressing and forming the powdery raw materials of the matrix to obtain a first formed body;
s300: coating an inner layer and an outer layer of the toughening layer on the surface of the first molded body in sequence, and performing pressing again to obtain a pre-pressed molded body;
s400: sintering the pre-pressed molding body to obtain a matrix with a toughening layer formed on the surface;
s500: wet sanding technology is adopted on the surface of the substrate on which the toughening layer is formed after sintering;
s600: and forming a strengthening layer on the surface of the substrate on which the toughening layer is formed by a vapor deposition method.
6. The tool as claimed in claim 6, wherein in step S400, the following sub-steps are included:
s410: heating the pre-pressed molded body to 1200 ℃ and then preserving heat;
s420: sintering the pre-pressed molded body at 1350 ℃ to 1450 ℃ for 90 minutes to 120 minutes, and simultaneously flowing a mixed gas atmosphere of hydrogen with a volume concentration of 1 to 3% and nitrogen with a volume concentration of 97 to 99% in a sintering furnace during the sintering process;
s430: then cooled to 1200 ℃ at a rate of 10 ℃/min.
7. A tool machining system, characterized in that the machining system is used for machining a tool according to one of claims 1-6; the processing system comprises a continuous section; the continuous working section comprises a wet sanding working section and a detection working section; the detection section comprises the step of detecting the residual stress of the matrix after forming the toughening layer by adopting an X-ray residual stress detection technology.
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