CN110284038B - PVD coating with strong (111) texture and preparation method thereof - Google Patents
PVD coating with strong (111) texture and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a PVD coating with strong (111) texture and a preparation method thereof. The PVD coating has a single or composite phase crystal structure at least the same as or similar to one of fcc-TiN or fcc-AlN, and a (111) plane texture coefficient > 2.5. The preparation method adopts WC-based hard alloy or TiCN-based cermet hard material as a matrix, and realizes the target regulation of the surface structure of the hard material matrix by carrying out secondary sintering regulation on the hard material matrix before coating; through the change of the surface structure of the substrate, the nucleation and growth conditions of the PVD coating are changed, so that a strong (111) texture is formed, the service life of the coated cutter is obviously prolonged, and the requirements of high performance and long service life of the PVD coated cutter on the efficient processing of materials difficult to process are met.
Description
Technical Field
The invention relates to a PVD coating with strong (111) texture and a preparation method thereof, belonging to the technical field of powder metallurgy composite materials and the field of cutting tools.
Background
The coating hard material consists of a hard material matrix and a coating. The surface structure of the hard material matrix has an important influence on nucleation and growth of the coating in direct contact with the hard material matrix. If the coating is a multilayer composite coating, the subsequently grown coating in turn has inheritance for this effect. Changes in the nucleation and growth environment of the coating can affect the performance of the coating and the useful life of the cutting tool.
The WC-based cemented carbide and the TiCN-based cermet refer to a cemented carbide and a cermet mainly composed of WC and TiCN, respectively, and are typical hard materials. Hard materials consist of a hard phase and a tough binder phase. The "bonding metal" of the hard material corresponds to the original addition state, such as Co, Ni and Co-Ni; the "binder phase" of the hard material corresponds to the alloy state after sintering. During sintering, the hard phase alloy components typically form a solid solution in the binder metal, forming a binder phase in a solid solution state.
Metal nitrides are common materials for coatings in hard materials. Metal nitrides with AlTiN, TiSiN, AlCrN, etc. as the main component are currently the more common commercial coating components. The above metal nitride generally has the same crystal structure as AlN or TiN, and other alloying elements are generally solid-dissolved in the AlN or TiN crystal lattice to form a solid solution. In the above nitride, when the mole fraction of Ti therein is higher than the total amount of other metal components, the same crystal structure as TiN is formed; when the molar fraction of Al therein is higher than the total amount of the other metal components, the same crystal structure as AlN is formed. The TiN and AlN are typically cubic crystal structures.
The anisotropy of the coating is generally characterized by a texture coefficient tc (hkl), which is calculated as follows:
in the formula, N is the total number of crystal faces taken in calculation; h. k and l are crystal face indexes of diffraction crystal faces; i is(hkl)And I0(hkl)Are respectively trueDiffraction peak intensities of (hkl) crystal planes of corresponding standard samples in a database identified by the joint commission on powder diffraction standards (JCPDS).
The texture coefficient of a crystal with randomly oriented crystal planes is 1. TC (hkl) > 2.5, the (hkl) crystal plane of which has a significant preferred orientation. The higher the texture coefficient of the coating, the better the crystalline integrity of the coating, thereby being beneficial to improving the crack expansion resistance and the wear resistance of the coating and being beneficial to prolonging the service life of the coated cutter. At present, no report of PVD coating with TC (111) > 2.5 is found.
Disclosure of Invention
The first purpose of the invention is to provide a PVD coating with (111) crystal plane texture coefficient TC (111) > 2.5, thereby obviously improving the crack propagation resistance and the wear resistance of the coating and obviously prolonging the service life of a coating cutter.
The invention also aims to provide a preparation method of the PVD coating with TC (111) > 2.5, excellent crack propagation resistance and high wear resistance, which can obviously improve the service life of the coated cutting tool, so as to meet the requirements of difficult-to-machine materials and high-efficiency machining on the high performance and long service life of the PVD coated cutting tool.
The invention relates to a PVD coating with strong (111) texture, which is prepared by adopting a physical vapor deposition method and comprises at least one of a single-layer composite coating and a multi-layer composite coating; the single or composite phase in the single and multilayer composite coatings has a crystal structure at least the same as or similar to one of fcc-TiN or fcc-AlN; the (111) crystal face texture coefficient of a single or composite phase of the PVD coating is more than 2.5, and the PVD coating is realized by performing secondary sintering regulation on the surface structure of a hard material matrix before coating; the fcc represents a face-centered cubic crystal structure, and the PVD coating adopts a hard material as a matrix and is deposited on the surface of the hard material matrix to form a coating part in a coating alloy; the hard material refers to WC-based hard alloy and TiCN-based cermet; the bonding metal of the WC-based hard alloy and the TiCN-based cermet comprises at least one of Co, Ni and other elements; the mass fraction of the bonding metal in the hard material in the alloy is more than or equal to 6 percent.
Cutting tools made with the PVD coating alloy have significantly improved service life; the single or composite phase of the coating refers to the phase of each layer of the coating which does not comprise the transition layer in the coating; for a single layer coating, the phases of the layers of the coating are the phases of the single layer coating.
According to the preparation method of the PVD coating with the strong (111) texture, the surface structure of the hard material matrix before coating is regulated and controlled by sintering for the second time, the nucleation and growth conditions of the PVD coating on the surface of the hard material matrix can be changed without changing the coating process, and the purpose of enabling the coating to have the strong (111) texture can be achieved; the preparation process flow comprises the second sintering regulation of the surface structure of the hard material matrix before coating and the physical vapor deposition of the coating on the surface of the hard material matrix regulated by the second sintering regulation of the surface structure; the second sintering regulation and control of the surface structure of the hard material matrix before coating refers to that a homogeneous and continuous bonding metal enrichment layer is formed on the surface of the hard material matrix before coating in situ; the bonding metal enrichment layer uniformly covers the surface of the whole alloy matrix, and the thickness of the bonding metal enrichment layer is 0.5-2.0 mu m.
The invention discloses a method for forming a homogeneous continuous bonding metal enrichment layer on the surface of a hard material matrix in situ, realizing uniform coverage on the surface of the whole alloy matrix and controlling the thickness of the alloy matrix to be 0.5-2.0 mu m, which comprises the following steps:
(1) putting hard material products treated by the conventional process before the first sintering and coating into a high-purity graphite boat, and uniformly burying the hard material products in a mixed powder filler consisting of high-purity rare earth oxide and high-purity graphite powder in an isolated state, wherein the products are isolated by the mixed powder filler; (2) putting the product loaded into the boat into a sintering furnace for vacuum sintering, cooling along with the furnace and discharging; (3) removing the filler on the surface of the product;
the mass fraction of the high-purity graphite powder in the mixed powder filler is 3-6%;
the sintering temperature of the vacuum sintering is controlled to be 10-40 ℃ above the eutectic temperature of an alloy system, and the heat preservation time is controlled to be 40-120 min.
The screen mesh aperture corresponding to the high-purity rare earth oxide particle size is 75-115 mu m, the screen mesh aperture corresponding to the high-purity graphite powder particle size is 38-75 mu m, the high purity refers to the purity of more than 99.5%, and the rare earth comprises at least one of common rare earth L a, Ce, Pr, Nd, Y and the like.
The eutectic temperature of the alloy system can be obtained by a differential scanning calorimetry analysis, a differential thermal analysis or other thermal analysis method.
The step of removing the filler on the surface of the product comprises the step of placing the product in an alcohol medium for ultrasonic cleaning.
The homogeneous continuous and uniform covering is carried out on the surface of the hard material matrix, and the bonding metal enrichment layer with the thickness of 0.5-2.0 mu m is formed in situ by controllably inducing the directional migration of a liquid phase in the hard material through the tunnel effect formed by powder gaps in the mixed powder filler in the vacuum sintering process; the thickness of the material is cooperatively regulated and controlled through sintering temperature and heat preservation time; and the sintering temperature and the heat preservation time are respectively controlled to be 10-40 ℃ and 40-120 min above the eutectic temperature of the alloy system.
The mechanism and advantages of the present invention are briefly described as follows:
the invention can induce the liquid phase in the hard material to move directionally in a controllable way through the tunnel effect formed by powder gaps in the mixed powder filler, so that a homogeneous and continuous bonding metal enrichment layer is formed on the surface of the hard material matrix in situ. The high-purity graphite powder and the high-purity rare earth oxide are mixed according to a certain proportion, so that carbon-oxygen balance in the mixed powder filler can be realized, and the mixed powder filler has high purity, high melting point and high reaction inertia with hard materials, so that a good clean surface structure of the hard material product can be maintained.
The inventor discovers through theoretical calculation and experimental research that the thickness of a bonding metal enrichment layer can be controlled to be 0.5-2.0 mu m through the cooperative regulation and control of the vacuum sintering temperature and the heat preservation time; in the thickness range, the existence of the bonding metal enrichment layer can not influence the matching of the elastic modulus, Poisson's ratio, thermal expansion coefficient and the like between the hard coating and the hard matrix, but can obviously influence the nucleation and crystal growth of the PVD coating, is favorable for the formation of obvious texture effect of the coating and is favorable for the release of coating stress.
The PVD coating of the invention has a (111) crystal face texture coefficient of a single or composite phase of more than 2.5. By adopting the texture technology, the crystal integrity of the coating can be obviously improved, the crystal defects are reduced, the wear resistance of the coating is obviously improved, and the capabilities of resisting crack formation and crack propagation of the coating are obviously improved, so that the service life of the coated cutter is obviously prolonged.
Drawings
Fig. 1 shows the appearance and geometry of the milling insert for the milling experiment in example 1.
FIG. 2 shows the results of example 1 using WC-0.7 Cr3C2And-0.4 VC-10 Co is used as a substrate, and the prepared PVD-TiSiN/TiAlSiN/AlTiN coating has an X-ray diffraction (XRD) spectrum, wherein the 2 theta position of each crystal face of AlN card with the serial number of 25-1495 in a JCPDS database and the theoretical peak intensity of the AlN card are marked in the spectrum.
FIG. 3 shows the results of example 1 using WC-0.7 Cr3C2And-0.4 VC-10 Co is used as a substrate, and the XRD map of the prepared PVD-TiSiN/TiAlSiN/AlTiN coating is marked with the 2 theta position and the theoretical peak intensity of each crystal face of a TiN card with the number of 38-1420 in a JCPDS database.
FIG. 4 shows the results of example 1 using WC-0.7 Cr3C2The PVD-TiSiN/TiAlSiN/AlTiN coating prepared by taking-0.4 VC-10 Co as a substrate has an XRD spectrum and a phase analysis comprehensive result thereof.
The appearance and geometry of the milling insert for the milling experiment of example 1 can be seen from fig. 1.
As can be seen from fig. 2, the diffraction peak corresponding to the (111) crystal face of the AlTiN phase having the same crystal structure as AlN in the coating is the strongest peak in the actually measured XRD pattern, the actual peak intensity of the second strong peak (theoretical peak intensity of 75%) corresponding to the (200) crystal face in the AlN card is significantly weakened, and the actual peak intensity of the first strong peak (theoretical peak intensity of 100%) corresponding to the (420) crystal face in the AlN standard card is zero. The integral diffraction peak to the left of the (111) crystal plane of the AlTiN phase in fig. 2 corresponds to the (111) crystal plane of the TiSiN phase in the coating. Because Ti with larger atomic radius generates solid solution in AlN crystal lattice and replaces Al atoms with smaller atomic radius in a large quantity, actual diffraction peaks corresponding to all crystal faces of the AlTiN phase integrally shift towards a small angle direction relative to the standard AlN peak position.
As can be seen from FIG. 3, the diffraction peak corresponding to the (111) crystal face of the TiSiN phase with the same crystal structure as TiN in the coating layer is the second strong peak in the actually measured XRD spectrum, and the actual peak intensity of the first strong peak corresponding to the (200) crystal face in the TiN card (the theoretical peak intensity is 100%) is obviously weakened. Because the solid solution amount of Si in TiN crystal lattice is very small, the actual diffraction peak position corresponding to each crystal face of the TiSiN phase is basically overlapped with the standard peak position of TiN.
As can be seen from FIG. 4, there are an AlTiN phase having the same crystal structure as AlN and a TiSiN phase having the same crystal structure as TiN in the coating layer, and the binder metal Co having an fcc structure (corresponding to 89-7093 cards) and an hcp structure (corresponding to 89-7094 cards) enriched in the surface of the substrate was also detected.
Detailed Description
The present invention will be further described with reference to the following examples.
Example 1:
WC-0.7 Cr prepared by respectively adopting pressure sintering process3C2-0.4 VC-10 Co (wherein the numerical values are mass fraction,%, hereinafter the same) and WC-0.4 Cr3C2-0.3 VC-6 Co cemented carbide insert, and TiC0.7N0.3–25WC–10TaC–2Mo2The C-6 Co-6 Ni cermet blade is used as a substrate of a coated blade for milling as shown in figure 1, meanwhile, an alloy sample for testing, which is made of a corresponding material 10 × 10 × 5mm, is also prepared, and the results of scanning electron microscope observation and analysis show that the grain sizes of 2 hard alloys are all 0.4 mu M, and the cermet has (Ti, M) C with a typical core-ring structure0.7N0.3(M ═ W, Ta, Mo) the grain size of the hard phase was-1.2 μ M; the 3 alloys are all normal hard phase + binding phase two-phase structures. Differential scanning calorimetry analysis shows that the eutectic temperatures of the above 3 alloys are 1310 ℃, 1325 ℃ and 1340 ℃.
Loading the alloy blade and square alloy sample into high-purity graphite boat, and uniformly burying them in Y-shaped space in isolated state2O3Mixed powder filler composed of graphite powder, wherein the quality of graphite powderThe weight fraction is 6%, the purity of 2 kinds of powder is 99.9%, Y2O3The aperture of the screen corresponding to the granularity is 75-115 mu m, and the aperture of the screen corresponding to the granularity of the graphite powder is 38-75 mu m. The alloy samples are isolated by mixed powder filler. And (3) putting the blade and the square sample which are arranged in the boat into a sintering furnace for vacuum sintering, wherein the sintering temperature is 1350 ℃, the heat preservation time is 70min, and cooling along with the furnace and discharging.
The observation results of scanning electron microscope on the surface of the alloy sintered body and the polished section show that 3 alloy surfaces after vacuum sintering in the mixed powder filler have homogeneous, continuous and uniformly covered bonding metal enrichment layers, and the average thicknesses of the bonding metal enrichment layers are 1.9, 1.0 and 0.6 mu m respectively.
Removing the filler on the surface of the product by a screening method, then putting the product into an alcohol medium for ultrasonic cleaning, depositing a TiSiN/TiAlSiN/AlTiN (directly contacting with the substrate) multilayer composite coating on the surfaces of the 3 alloy blades and the square alloy substrate by a direct current magnetron sputtering technology, vacuumizing a deposition chamber to 3 × 10 before the coating is deposited–3Pa, heating the substrate to 450 ℃, applying-100V bias voltage to the substrate in high-purity Ar gas, and carrying out sputter etching on the surface of the substrate for 50 min. At the temperature of 450 ℃ of the substrate, the bias voltage of the substrate is-100V, and the high-purity N is2The coating deposition is carried out under atmospheric conditions. The TiSiN layer with the thickness of 2.9 microns and the AlTiN layer with the thickness of 1.6 microns are obtained by independently depositing a TiSi target and a TiAl target respectively; the TiAlSiN transition layer is obtained by simultaneously depositing 2 kinds of target materials, and the thickness of the TiAlSiN transition layer is 50nm (a high-resolution transmission electron microscope measurement result). The electron probe analysis result shows that the coating component is Ti0.94Si0.06N/TiAlSiN/Al0.52Ti0.48N。
FIGS. 2 to 4 show the use of WC-0.7 Cr3C2XRD pattern of surface of coating square hard alloy sample prepared by using-0.4 VC-10 Co alloy as matrix and phase analysis result obtained by adopting MDI Jade software. The calculations show that TC (111) for TiSiN and AlTiN were 3.2 and 5.9, respectively.
The milling experiment is carried out in a vertical machining center, the number of teeth of a cutter head is 3, 1 blade is used in each experiment, and a machining object is 316L austenitic stainless steelThe size of the piece is 1200 × 600 × 600mm dry milling parameters are as follows, the cutting speed is 180m/min, the feed rate is 0.7mm/th (feed rate per tooth), the axial cutting depth is 0.7mm, the radial cutting depth is 20mm, GB/T16459 and 1996 face milling cutter life test determines the service life of the cutter, and the maximum wear rate VB of the flank face is VBmax＝0.3mm。
The milling experiment result shows that WC-0.7 Cr is adopted3C2–0.4VC–10Co、WC–0.4Cr3C2-0.3 VC-6 Co and TiC0.7N0.3–25WC–10TaC–2Mo2The average service life of the TiSiN/TiAlSiN/AlTiN coated milling cutter taking the C-6 Co-6 Ni alloy as the matrix is 59min, 54min and 63min respectively.
Comparative example 1:
3 alloy inserts and square alloy matrices were prepared in the same batch as in example 1. The only difference from example 1 is that the alloy blade and the square alloy sample were not subjected to a second sintering control of the surface structure before coating, i.e. to a vacuum sintering treatment in the mixed powder filler. The coating deposition and milling experiments were carried out in the same batch as in example 1 under the same conditions.
The calculation result based on XRD analysis shows that the WC-0.7 Cr regulated and controlled by the secondary sintering of the uncoated front surface structure3C2The coating prepared by taking the-0.4 VC-10 Co alloy as a substrate has the TC (111) of 1.4 and 1.8 of TiSiN and AlTiN coatings respectively.
The milling experiment result shows that the WC-0.7 Cr which is regulated and controlled by the secondary sintering of the uncoated front surface structure3C2–0.4VC–10Co、WC–0.4Cr3C2-0.3 VC-6 Co and TiC0.7N0.3–25WC–10TaC–2Mo2The average service life of the TiSiN/TiAlSiN/AlTiN milling cutter taking the C-6 Co-6 Ni alloy as the matrix is 36min, 32min and 40min respectively.
Example 2:
the pressure sintering process is adopted to prepare 3 kinds of square hard alloy samples of 10 × 10 × 5mm, such as WC-10 Co, WC-10 Ni, WC-5 Co-5 Ni and the like, as coating matrixes, the observation and analysis results of a scanning electron microscope show that the grain sizes of the 3 kinds of hard alloys are all 1.2 mu m and are both normal hard phase and bonding phase two-phase structures, and the differential scanning calorimetry analysis results show that the eutectic temperatures of the 3 kinds of alloys are 1370 ℃, 1400 ℃ and 1385 ℃ respectively.
Dividing the square alloy samples subjected to sand blasting, grinding and the like into 4 groups, each group containing 3 alloys, placing the 4 groups into a high-purity graphite boat, and uniformly burying the three groups in a mutually isolated state respectively represented by L a2O3And 3% (mass fraction, the same below) of graphite powder and CeO2And 4% of graphite powder and Pr6O11And 5% of graphite powder and Nd2O3And 6% graphite powder, wherein the purities of the rare earth oxide and the graphite powder are both 99.9%, the aperture of the sieve mesh corresponding to the granularity of the rare earth oxide is 75-115 mu m, the aperture of the sieve mesh corresponding to the granularity of the graphite powder is 38-75 mu m, alloy samples are isolated by the mixed powder filler, the square samples filled into the boat are placed into a sintering furnace for 2 groups for vacuum sintering, and the group 1 is that the square samples are filled into L a2O3+ 3% of graphite powder and CeO2And mixing 4% of graphite powder with the alloy in the powder filler, sintering at 1410 ℃, keeping the temperature for 40min, cooling along with the furnace, and discharging. Group 2 is Loading with Pr6O11+ 5% graphite powder and Nd2O3And mixing 6% of graphite powder with the alloy in the powder filler, sintering at 1410 ℃, keeping the temperature for 120min, cooling along with the furnace, and discharging.
The observation results of a scanning electron microscope on the surface of the alloy sintered body and the polished section show that the surfaces of the 3 alloys all have homogeneous, continuous and uniformly covered bonding metal enrichment layers, the average thickness of the bonding metal enrichment layers is less influenced by the types of the fillers, and the average thickness of the bonding metal enrichment layers on the surface of the WC-10 Co alloy with the heat preservation time of 40min and 120min is respectively 1.0 mu m and 1.8 mu m; the average thicknesses of the WC-10 Ni alloy surface bonding metal enrichment layers with the heat preservation time of 40min and 120min are respectively 0.7 mu m and 1.1 mu m; the average thicknesses of the WC-5 Co-5 Ni alloy surface bonding metal enrichment layers with the heat preservation time of 40min and 120min are respectively 1.1 mu m and 1.9 mu m. The average thickness is a statistical result of the thickness of the surface bonding metal enrichment layer of the alloy corresponding to different fillers under the conditions of the same sintering temperature and the same heat preservation time.
Removing the filler on the surface of the product by sieving, then putting the product into alcohol medium for ultrasonic cleaning, depositing AlCrN single-layer coating on the surface of the square alloy substrate with the 3 components by adopting a direct-current magnetron sputtering technology, vacuumizing a deposition chamber to the pressure of 3 × 10 before deposition–3Pa, heating the substrate to 450 ℃, applying-100V bias voltage to the substrate in high-purity Ar gas, and carrying out sputter etching on the surface of the substrate for 50 min. At a matrix temperature of 450 ℃, a matrix bias of-100V and high-purity N2The coating deposition is carried out under atmospheric conditions. The electron probe analysis result shows that the coating component is Al0.55Cr0.45N, thickness of-4.0 μm.
Based on XRD analysis and calculation results, TC (111) of AlCrN is less influenced by the thickness of the alloy surface bonding metal enrichment layer; the average values of TC (111) of 3 alloy matrix surfaces of WC-10 Co, WC-10 Ni, WC-5 Co-5 Ni and the like with the fcc-AlN crystal structure AlCrN coating are respectively 6.1, 5.5 and 5.9.
Comparative example 2:
3 square alloy matrices were prepared in the same batch as example 2. The only difference from example 2 is that all the square alloy samples were not subjected to a second sintering control of the surface structure before coating, i.e. not subjected to a vacuum sintering treatment in the mixed powder filler. The coating deposition was carried out in the same batch as in example 2.
Based on XRD analysis and calculation results, 3 alloys such as WC-10 Co, WC-10 Ni, WC-5 Co-5 Ni and the like which are not regulated and controlled by secondary sintering of the surface structure before coating are adopted as a substrate, and TC (111) of the AlCrN coating with the fcc-AlN crystal structure on the surface is 1.6, 1.4 and 1.5 respectively.
The data acquisition for all examples and comparative examples described above was performed in a random sampling mode, with a number of samples per condition of 3. Under the same test conditions, the product obtained in comparative example 2 has a significantly lower lifetime than the corresponding product in example 2.
Claims (6)
1. A PVD coating having a strong (111) texture, characterized in that: the PVD coating is prepared by adopting a physical vapor deposition method and comprises at least one of a single-layer coating or a multi-layer composite coating; the single or composite phase in the single and multilayer composite coatings has a crystal structure at least the same as or similar to one of fcc-TiN or fcc-AlN; the (111) crystal face texture coefficient of a single or composite phase of the PVD coating is more than 2.5, and the PVD coating is realized by performing secondary sintering regulation on the surface structure of a hard material matrix before coating; the fcc represents a face centered cubic crystal structure; the PVD coating adopts a hard material as a matrix, and is deposited on the surface of the hard material matrix to form a coating part in the coating alloy; the hard material refers to WC-based hard alloy and TiCN-based cermet; the bonding metal of the WC-based cemented carbide and the TiCN-based cermet comprises at least one of Co and Ni; the mass fraction of the bonding metal in the hard material in the alloy is more than or equal to 6 percent;
the second sintering regulation and control of the surface structure of the hard material matrix before coating refers to that a homogeneous and continuous bonding metal enrichment layer is formed on the surface of the hard material matrix before coating in situ; the bonding metal enrichment layer uniformly covers the surface of the whole alloy matrix, and the thickness of the bonding metal enrichment layer is 0.5-2.0 mu m;
the method for forming the homogeneous continuous bonding metal enrichment layer on the surface of the hard material matrix in situ to realize the uniform coverage of the whole alloy matrix surface and controlling the thickness of the alloy matrix to be 0.5-2.0 mu m comprises the following steps:
(1) putting hard material products treated by the conventional process before the first sintering and coating into a high-purity graphite boat, and uniformly burying the hard material products in a mixed powder filler consisting of high-purity rare earth oxide and high-purity graphite powder in an isolated state, wherein the products are isolated by the mixed powder filler; (2) putting the product loaded into the boat into a sintering furnace for vacuum sintering, cooling along with the furnace and discharging; (3) removing the filler on the surface of the product;
the mass fraction of the high-purity graphite powder in the mixed powder filler is 3-6%;
the sintering temperature of the vacuum sintering is controlled to be 10-40 ℃ above the eutectic temperature of an alloy system, and the heat preservation time is controlled to be 40-120 min.
2. A PVD coating with strong (111) texture, according to claim 1, characterized by: cutting tools made with the PVD coating alloy have significantly improved service life; the single or composite phase of the coating refers to the phase of each layer of the coating which does not comprise the transition layer in the coating; for a single layer coating, the phases of the layers of the coating are the phases of the single layer coating.
3. The PVD coating with the strong (111) texture is characterized in that the screen mesh aperture corresponding to the particle size of the high-purity rare earth oxide is 75-115 mu m, the screen mesh aperture corresponding to the particle size of the high-purity graphite powder is 38-75 mu m, the purity is higher than 99.5%, and the rare earth comprises at least one of common rare earth L a, Ce, Pr, Nd and Y.
4. A PVD coating with strong (111) texture according to claim 1, characterized by: the eutectic temperature of the alloy system is obtained by a thermal analysis means; the thermal analysis means is differential scanning calorimetry analysis or differential thermal analysis.
5. A PVD coating with strong (111) texture according to claim 1, characterized by: the step of removing the filler on the surface of the product comprises the step of placing the product in an alcohol medium for ultrasonic cleaning.
6. PVD coating with a strong (111) texture according to any of the claims 1-5, characterized in that: the homogeneous continuous and uniform covering is carried out on the surface of a hard material matrix, a bonding metal enrichment layer with the thickness of 0.5-2.0 mu m is formed in situ by controllably inducing the directional migration of a liquid phase in the hard material through the tunnel effect formed by powder gaps in mixed powder filler in the vacuum sintering process; the thickness of the material is cooperatively regulated and controlled through sintering temperature and heat preservation time; and the sintering temperature and the heat preservation time are respectively controlled to be 10-40 ℃ and 40-120 min above the eutectic temperature of the alloy system.
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