CN110284038B - A kind of PVD coating with strong (111) texture and preparation method thereof - Google Patents

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

A kind of PVD coating with strong (111) texture and preparation method thereof

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 technique

Coated hard material consists of hard material base and coating. The surface structure of the hard material substrate has an important influence on the nucleation and growth of the coating in direct contact with it. If the coating is a multi-layer composite coating, subsequently grown coatings will in turn inherit this effect. Changes in coating nucleation and growth conditions can affect the performance of the coating and its cutting tool life.

WC-based cemented carbide and TiCN-based cermet refer to cemented carbide and cermet with WC and TiCN as the main components, respectively, which are typical hard materials. Hard materials consist of a hard phase and a tough binder phase. The "binder metal" of hard materials corresponds to the original added state, such as Co, Ni and Co-Ni, etc.; the "binder phase" of hard materials corresponds to the alloy state after sintering. During the sintering process, the hard phase alloy components usually generate solid solution in the binder metal to form a binder phase that exists in a solid solution state.

Metal nitrides are a common material for coatings in coated hard materials. Metal nitrides with AlTiN, TiSiN, AlCrN, etc. as the main components are the most common commercial coating components. The above-mentioned metal nitrides usually have the same crystal structure as AlN or TiN, and other alloy elements are usually solid-dissolved in the AlN or TiN lattice to form a solid solution. In the above nitrides, when the mole fraction of Ti is higher than the total amount of other metal components, the same crystal structure as TiN is formed; when the mole fraction of Al is higher than the total amount of other metal components, the same crystal structure as AlN is formed. the same crystal structure. The TiN and AlN are generally cubic crystal structures.

The anisotropy of the coating is usually characterized by the texture coefficient TC(hkl), which is calculated as follows:

In the formula, N is the total number of crystal planes taken in the calculation; h, k, l are the crystal plane indices of the diffraction crystal planes; I _(hkl) and I _{0 (hkl)} are the actual measurement and the Joint Committee on Powder Diffraction Standards (JCPDS), respectively ) the diffraction peak intensity of the corresponding standard sample in the (hkl) crystal plane in the database identified.

For crystals with randomly oriented crystal planes, the texture coefficient is 1. For materials with TC(hkl)>2.5, the (hkl) crystal plane has a significant preferred orientation. The higher the texture coefficient of the coating, the better the integrity of its crystallization, which is conducive to the improvement of its crack growth resistance and wear resistance, and is conducive to the improvement of the service life of the coating tool. There are no reports on PVD coatings with TC(111)>2.5.

SUMMARY OF THE INVENTION

The first object of the present invention is to provide a PVD coating with a (111) crystal plane texture coefficient TC(111)>2.5, thereby significantly improving the crack propagation resistance and wear resistance of the coating, and significantly improving the coating tool's durability. service life.

Another object of the present invention is to provide a preparation method of PVD coating with TC(111)>2.5, which has excellent crack growth resistance and high wear resistance, and can significantly improve the service life of coated tools, so as to meet the requirements of difficult-to-machine materials. Its high-efficiency machining requires high performance and long life of PVD-coated tools.

The present invention is a PVD coating with strong (111) texture, the PVD coating is prepared by a physical vapor deposition method, and comprises at least one of a single-layer and a multi-layer composite coating; the single-layer and multi-layer composite coatings The crystal structure of the single or composite phase in the layer composite coating is at least the same as or similar to one of fcc-TiN or fcc-AlN; the (111) crystal plane texture coefficient of the single or composite phase of the PVD coating > 2.5, realized by the second sintering adjustment of the surface structure of the hard material substrate before coating; the fcc represents the face-centered cubic crystal structure The PVD coating uses hard material as the substrate and is deposited on the surface of the hard material substrate , constitute the coating part in the coating alloy; the hard material refers to WC-based cemented carbide and TiCN-based cermet; the binder metals of the WC-based cemented carbide and TiCN-based cermet include Co, Ni, etc. At least one of the elements; the mass fraction of the binder metal in the hard material in the alloy is ≥6%.

Cutting tools prepared by using 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 that does not include a transition layer in the coating; for single-layer coating layer, the phase of each layer of the coating is the phase of the single-layer coating.

The present invention is a preparation method of a PVD coating with strong (111) texture, which only needs to perform a second sintering adjustment on the surface structure of the hard material substrate before the coating, and does not need to change the coating process. By changing the nucleation and growth conditions of the coating on the surface of the hard material substrate, the goal of making the coating with strong (111) texture can be achieved; the preparation process includes the second step of the surface structure of the hard material substrate before coating Sintering control and physical vapor deposition of coating on the surface of the hard material substrate after the second sintering control of the surface structure; the second sintering control of the surface structure of the hard material substrate before coating refers to making the A homogeneous and continuous bonding metal-enriched layer is formed in situ on the surface of the material substrate; the bonding metal-enriched layer uniformly covers the entire surface of the alloy substrate, and has a thickness of 0.5-2.0 μm.

In the present invention, a homogeneous and continuous bonding metal enrichment layer is formed on the surface of the hard material substrate in situ, so as to achieve uniform coverage of the entire alloy substrate surface, and the method for controlling the thickness thereof to be between 0.5 and 2.0 μm includes the following steps:

(1) The hard material products after the first sintering and conventional processing before coating are loaded into the high-purity graphite boat, and evenly buried in the high-purity rare earth oxide and high-purity graphite powder in a mutually isolated state In the mixed powder filler, the products are separated by the mixed powder filler; (2) put the products loaded into the boat into the sintering furnace for vacuum sintering and cool down with the furnace; (3) remove the filler on the surface of the product ;

The mass fraction of the high-purity graphite powder in the mixed powder filler is between 3% and 6%;

The sintering temperature of the vacuum sintering is controlled at 10-40° C. above the eutectic temperature of the alloy system, and the holding time is controlled between 40-120 minutes.

The mesh aperture corresponding to the particle size of the high-purity rare earth oxide is between 75 and 115 μm; the mesh aperture corresponding to the particle size of the high-purity graphite powder is between 38 and 75 μm; the high purity means that the purity is greater than 99.5%; The rare earth includes at least one of common rare earths La, Ce, Pr, Nd, Y and the like.

The eutectic temperature of the alloy system can be obtained by thermal analysis methods such as differential scanning calorimetry or differential thermal analysis.

The removing the filler on the surface of the product includes placing the product in an alcohol medium for ultrasonic cleaning.

The homogeneous, continuous and evenly covered surface of the hard material substrate and the bonding metal enrichment layer with a thickness of 0.5-2.0 μm is a tunnel effect formed by mixing the powder gaps in the powder filler during the vacuum sintering process. The directional migration of the liquid phase in the hard material is controllably induced to form in-situ; its thickness is regulated by the sintering temperature and the holding time; the sintering temperature and holding time are respectively controlled at 10-40° C. 120min.

The mechanism and advantages of the present invention are briefly described below:

The invention can controllably induce the directional migration of the liquid phase in the hard material through the tunnel effect formed by the powder gap in the mixed powder filler, so that a homogeneous and continuous bonding metal enrichment layer is formed on the surface of the hard material substrate in situ. High-purity graphite powder and high-purity rare earth oxide are mixed in a certain proportion to achieve carbon-oxygen balance in the mixed powder filler. The mixed powder filler has high purity, high melting point, and high reaction inertness with hard materials. A good clean surface structure of the hard material article can thus be maintained.

The inventors have found through theoretical calculations and experimental studies that the thickness of the bonding metal enrichment layer can be controlled to be between 0.5 and 2.0 μm through the coordinated regulation of the vacuum sintering temperature and the holding time; within this thickness range, the bonding metal enrichment The existence of the layer will not affect the matching of elastic modulus, Poisson's ratio, thermal expansion coefficient, etc. between the hard coating and the hard substrate, but will significantly affect the nucleation and crystal growth of the PVD coating, which is conducive to the formation of the coating. The obvious texture effect is beneficial to the release of coating stress.

The (111) crystal plane texture coefficient of the single or composite phase of the PVD coating of the present invention is greater than 2.5. With this texturing technique, the crystalline integrity of the coating can be significantly improved, crystalline defects can be reduced, the wear resistance of the coating can be significantly improved, and the coating's resistance to crack formation and crack propagation can be significantly improved, thereby significantly improving the coating tool. service life.

Description of drawings

FIG. 1 shows the appearance and geometric dimensions of the milling insert for the milling experiment in Example 1.

Figure 2 is the X-ray diffraction (XRD) pattern of the PVD-TiSiN/TiAlSiN/AlTiN coating prepared in Example 1 using WC-0.7Cr ₃ C ₂ -0.4VC-10Co as the substrate, and the number in the JCPDS database is marked in the pattern It is the 2θ position of each crystal plane of AlN card of 25-1495 and its theoretical peak intensity.

Figure 3 is the XRD pattern of the PVD-TiSiN/TiAlSiN/AlTiN coating prepared by using WC-0.7Cr ₃ C ₂ -0.4VC-10Co as the substrate in Example 1. The pattern is marked with the number 38-1420 in the JCPDS database. The 2θ position of each crystal plane of TiN card and its theoretical peak intensity.

Figure 4 is the XRD pattern and the comprehensive results of the phase analysis of the PVD-TiSiN/TiAlSiN/AlTiN coating prepared in Example 1 using WC-0.7Cr ₃ C ₂ -0.4VC-10Co as the substrate.

It can be seen from FIG. 1 that the appearance and geometric dimensions of the milling insert used in the milling experiment in Example 1.

It can be seen from Figure 2 that the diffraction peak corresponding to the (111) crystal plane of the AlTiN phase with the same crystal structure as AlN in the coating is the strongest peak in the measured XRD pattern, and the first one corresponding to the (200) crystal plane in the AlN card. The actual peak intensity of the second strong peak (theoretical peak intensity is 75%) is obviously weakened, and the actual peak intensity of the first strong peak (theoretical peak intensity is 100%) corresponding to the (420) crystal plane in the AlN standard card is zero. The conjoined diffraction peak on the left side of the (111) crystal plane of the AlTiN phase in Figure 2 corresponds to the (111) crystal plane of the TiSiN phase in the coating. Since Ti with a larger atomic radius produces a solid solution in the AlN lattice and replaces a large number of Al atoms with a smaller atomic radius, the actual diffraction peaks corresponding to each crystal plane of the AlTiN phase have a small angle relative to the AlN standard peak position. overall offset.

It can be seen from Figure 3 that the diffraction peak corresponding to the (111) crystal plane of the TiSiN phase with the same crystal structure as TiN in the coating is the second strongest peak in the measured XRD pattern, and the (200) crystal plane in the TiN card corresponds to the diffraction peak. The actual peak intensity of the first strong peak (the theoretical peak intensity is 100%) has been significantly weakened. Due to the small amount of solid solution of Si in the TiN lattice, the actual diffraction peak positions corresponding to each crystal plane of the TiSiN phase basically overlap with the standard peak positions of TiN.

It can be seen from Figure 4 that there is an AlTiN phase with the same crystal structure as AlN in the coating, and a TiSiN phase with the same crystal structure as TiN. At the same time, the fcc structure (corresponding to 89-7093 cards) and hcp enriched on the surface of the substrate were also detected. Bond metal Co for structure (corresponding to 89-7094 card).

Detailed ways

The present invention will be further described below in conjunction with the examples.

Example 1:

WC-0.7Cr ₃ C ₂ -0.4VC-10Co (where the value is mass fraction, %, the same below) and WC-0.4Cr ₃ C ₂ -0.3VC-6Co cemented carbide inserts prepared by pressure sintering process, and TiC _0.7 N _0.3 – 25WC – 10TaC – 2Mo ₂ C – 6Co – 6Ni cermet insert is used as the base of the coated insert for milling as shown in Figure 1. At the same time, alloy samples with the corresponding material of 10×10×5mm for testing were also prepared. Scanning electron microscope observation and analysis results show that the grain size of the two cemented carbides is ~0.4μm, and the cermet has a typical core-ring structure (Ti, M)C _0.7 N _0.3 (M=W, Ta, Mo) The grain size of the hard phase is ~1.2 μm; the above three alloys are all normal hard phase + binder phase two-phase structure. Differential scanning calorimetry analysis results show that the eutectic temperatures of the above three alloys are 1310°C, 1325°C and 1340°C, respectively.

The above-mentioned sandblasted and ground alloy blades and square alloy samples were loaded into a high-purity graphite boat, and evenly buried in a mixed powder filler composed of Y ₂ O ₃ and graphite powder in a mutually isolated state, in which graphite The mass fraction of the powder is 6%, the purity of the two powders is 99.9%, the sieve aperture corresponding to the particle size of Y ₂ O ₃ is between 75 and 115 μm, and the aperture of the mesh corresponding to the particle size of the graphite powder is between 38 and 75 μm. The alloy samples are separated by mixed powder fillers. The above-mentioned blade and square sample loaded into the boat were put into a sintering furnace for vacuum sintering, the sintering temperature was 1350° C., the holding time was 70 min, and the furnace was cooled and released.

The scanning electron microscope observation results of the surface of the alloy sintered body and the polished section show that the three alloys after vacuum sintering in the mixed powder filler have a homogeneous continuous and uniformly covered binder metal enrichment layer, and the average thickness is 1.9, 1.0 and 0.6 μm.

The filler on the surface of the product is removed by sieving, and then the product is placed in an alcohol medium for ultrasonic cleaning. The TiSiN/TiAlSiN/AlTiN (direct contact with the substrate) multilayer composite coating was deposited on the surfaces of the above three alloy blades and square alloy substrates by DC magnetron sputtering technology. Before coating deposition, the deposition chamber was evacuated to 3 × 10 ^-3 Pa, the substrate was heated to 450 °C, and a bias voltage of –100 V was applied to the substrate in high-purity Ar gas, and the surface was sputter-etched for 50 min. The coating deposition was carried out under the conditions of substrate temperature of 450 °C, substrate bias voltage of -100 V, and high-purity N ₂ atmosphere. The TiSiN layer with a thickness of ~2.9μm and the AlTiN layer with a thickness of ~1.6μm were deposited separately from the TiSi target and the TiAl target, respectively. . Electron probe analysis results show that the coating composition is Ti _0.94 Si _0.06 N/TiAlSiN/Al _0.52 Ti _0.48 N.

Figures 2-4 show the XRD patterns of the surface of the coated square cemented carbide samples prepared by using the WC-0.7Cr ₃ C ₂ -0.4VC-10Co alloy as the matrix and the phase analysis results obtained by the MDI Jade software. The calculated results show that the TC(111) of TiSiN and AlTiN are 3.2 and 5.9, respectively.

The milling experiments were carried out on a vertical machining center. The number of teeth on the cutter head was 3, and one blade was used in each experiment. The processing object is 316L austenitic stainless steel, and the workpiece size is 1200×600×600mm. The dry milling parameters are as follows: cutting speed 180m/min, feed 0.7mm/th (feed per tooth), axial depth of cut 0.7mm, radial depth of cut 20mm. GB/T 16459-1996 face milling cutter life test to determine the tool life: the maximum wear of the flank face VB _max = 0.3mm.

The results of milling experiments show that the WC–0.7Cr ₃ C ₂ –0.4VC–10Co, WC–0.4Cr ₃ C ₂ –0.3VC–6Co and TiC _0.7 N _0.3 –25WC–10TaC–2Mo ₂ C–6Co–6Ni alloys are The average lifespans of the TiSiN/TiAlSiN/AlTiN coated milling tools for the substrate are 59min, 54min and 63min, respectively.

Comparative Example 1:

The three alloy blades and the square alloy base were prepared in the same batch as in Example 1. The only difference from Example 1 is that the alloy inserts and the square alloy samples are not subject to the second sintering control of the surface structure before the coating, that is, they have not undergone the vacuum sintering treatment in the mixed powder filler. Coating deposition and milling experiments were performed in the same batch as Example 1 under the same conditions.

The calculation results based on XRD analysis show that the coatings prepared by using the WC-0.7Cr ₃ C ₂ -0.4VC-10Co alloy with the second sintering control of the uncoated front surface structure as the matrix have the TC of TiSiN and AlTiN coatings. (111) are 1.4 and 1.8, respectively.

The results of milling experiments show that WC _– 0.7Cr3C2–0.4VC–10Co, WC _{– 0.4Cr3C2–0.3VC – 6Co} and _{TiC0.7N0.3–} The average life of the TiSiN/TiAlSiN/AlTiN milling tools based on 25WC–10TaC–2Mo ₂ C–6Co–6Ni alloy is 36min, 32min and 40min, respectively.

Example 2:

Three 10×10×5mm square cemented carbide samples, WC–10Co, WC–10Ni and WC–5Co–5Ni, prepared by pressure sintering process were used as coating substrates. Scanning electron microscope observation and analysis results show that the grain sizes of the three cemented carbides are all ~1.2 μm, and they are all normal hard phase + binder phase two-phase structure. Differential scanning calorimetry analysis results show that the eutectic temperatures of the above three alloys are 1370℃, 1400℃ and 1385℃, respectively.

The above-mentioned square alloy samples treated by sandblasting and grinding were divided into 4 groups, each group containing 3 kinds of alloys, loaded into high-purity graphite boats, and evenly buried in a state of mutual isolation between La ₂ O ₃ and 3 alloys. % (mass fraction, the same below) graphite powder, CeO ₂ and 4% graphite powder, Pr ₆ O ₁₁ and 5% graphite powder, Nd ₂ O ₃ and 6% graphite powder in the mixed powder filler; the above rare earth oxides The purity of the graphite powder and the graphite powder are both 99.9%; the mesh aperture corresponding to the particle size of the rare earth oxide is between 75 and 115 μm, and the mesh aperture corresponding to the particle size of the graphite powder is between 38 and 75 μm. The alloy samples are separated by mixed powder fillers. The above-mentioned square samples loaded into the boat were placed in a sintering furnace for vacuum sintering in two groups. The first group is an alloy loaded with La ₂ O ₃ +3% graphite powder and CeO ₂ +4% graphite powder mixed powder filler, the sintering temperature is 1410 ° C, the holding time is 40 min, and the furnace is cooled and released. The second group is an alloy loaded with Pr ₆ O ₁₁ +5% graphite powder and Nd ₂ O ₃ +6% graphite powder mixed powder filler.

The scanning electron microscope observation results of the surface of the alloy sintered body and the polished section show that the above three alloys have a homogeneous continuous and uniformly covered bond metal enrichment layer, and the average thickness is less affected by the type of filler, and the holding time is different. The average thickness of the metal-enriched layer on the surface of the WC-10Co alloy for 40min and 120min was 1.0μm and 1.8μm, respectively; the average thickness of the metal-enriched layer on the surface of the WC-10Ni alloy for the holding time of 40min and 120min was 0.7 μm, respectively. μm and 1.1 μm; the average thickness of the metal-enriched layer on the surface of WC–5Co–5Ni alloy with holding time of 40 min and 120 min, respectively, was 1.1 μm and 1.9 μm. The above average thickness is the statistical result of the thickness of the metal-enriched layer on the surface of alloys with different fillers under the same sintering temperature and holding time of the same composition alloy.

The filler on the surface of the product is removed by sieving, and then the product is placed in an alcohol medium for ultrasonic cleaning. AlCrN single-layer coating was deposited on the surface of the square alloy matrix with the above three components by DC magnetron sputtering technology. Before deposition, the deposition chamber was evacuated to a pressure of 3 × 10 ^-3 Pa, the substrate was heated to 450 °C, a bias voltage of –100 V was applied to the substrate in high-purity Ar gas, and the surface was sputter-etched for 50 min. The coating deposition was carried out under the conditions of a substrate temperature of 450 °C, a substrate bias voltage of –100 V and a high-purity _N2 atmosphere. Electron probe analysis results show that the coating composition is Al _0.55 Cr _0.45 N and the thickness is ~4.0 μm.

Based on XRD analysis and calculation results, it is shown that the TC(111) of AlCrN is less affected by the thickness of the bonding metal-enriched layer on the surface of the alloy; WC-10Co, WC-10Ni and WC-5Co-5Ni have fcc The average values of TC(111) for AlCrN coatings with AlN crystal structure are 6.1, 5.5 and 5.9, respectively.

Comparative Example 2:

The three square alloy substrates were prepared in the same batch as Example 2. The only difference from Example 2 is that all the square alloy samples were not conditioned by the second sintering of the surface structure before the coating, that is, they were not subjected to vacuum sintering in the mixed powder filler. Coating deposition was performed on the same batch as Example 2.

Based on XRD analysis and calculation results, it is shown that three alloys, WC-10Co, WC-10Ni and WC-5Co-5Ni, which are controlled by the second sintering of the uncoated front surface structure, are used as the matrix, and the surface has the fcc-AlN crystal structure. The TC(111) of the AlCrN coatings are 1.6, 1.4 and 1.5, respectively.

The data acquisition of all the above embodiments and comparative examples adopts random sampling, and the number of sampling samples for each condition is 3. Under the same test conditions, the product obtained in Comparative Example 2 is significantly shorter than the life of the corresponding product in Example 2.

Claims (6)

1. a PVD coating with strong (111) texture is characterized in that: the PVD coating is prepared by the method of physical vapor deposition, comprising at least one of single-layer coating or multi-layer composite coating; The crystal structure of the single or composite phase in the single-layer and multi-layer composite coatings is at least the same as or similar to one of fcc-TiN or fcc-AlN; the single or composite phase of the PVD coating (111 ) crystal plane texture coefficient > 2.5, which is achieved by the second sintering control of the surface structure of the hard material substrate before coating; the fcc represents the face-centered cubic crystal structure; the PVD coating uses a hard material as the substrate, It is deposited on the surface of the hard material base to form the coating part of the coating alloy; the hard material refers to the WC-based cemented carbide and the TiCN-based cermet; the adhesion of the WC-based cemented carbide and the TiCN-based cermet. The bonding metal includes at least one of Co and Ni; the mass fraction of the bonding metal in the alloy in the hard material is greater than or equal to 6%; The second sintering control of the surface structure of the hard material substrate before coating means that a homogeneous and continuous bonding metal enrichment layer is formed in situ on the surface of the hard material substrate before coating; the bonding metal enrichment layer is uniform Covering the surface of the entire alloy matrix, the thickness is between 0.5 and 2.0 μm; The method of forming a homogeneous and continuous bonding metal-enriched layer on the surface of a hard material substrate in situ to achieve uniform coverage of the entire alloy substrate surface and controlling its thickness to be between 0.5 and 2.0 μm includes the following steps: (1) The hard material products after the first sintering and conventional processing before coating are loaded into the high-purity graphite boat, and evenly buried in the high-purity rare earth oxide and high-purity graphite powder in a mutually isolated state In the mixed powder filler, the products are separated by the mixed powder filler; (2) put the products loaded into the boat into the sintering furnace for vacuum sintering and cool down with the furnace; (3) remove the filler on the surface of the product ; The mass fraction of the high-purity graphite powder in the mixed powder filler is between 3% and 6%; The sintering temperature of the vacuum sintering is controlled at 10-40° C. above the eutectic temperature of the alloy system, and the holding time is controlled between 40-120 minutes. 2. The PVD coating with strong (111) texture according to claim 1, characterized in that: the cutting tool prepared by using the PVD coating alloy has a significantly improved service life; Single or composite phase refers to the phase of each layer of the coating that does not include a transition layer; for a single-layer coating, the phase of each layer of the coating is the phase of the single-layer coating. 3 . The PVD coating with strong (111) texture according to claim 1 , wherein: the sieve aperture corresponding to the particle size of the high-purity rare earth oxide is between 75 and 115 μm; The mesh aperture corresponding to the particle size of the graphite powder is between 38 and 75 μm; the high purity means that the purity is >99.5%; the rare earth includes at least one of the common rare earths La, Ce, Pr, Nd, and Y. 4. A kind of PVD coating with strong (111) texture according to claim 1, characterized in that: the eutectic temperature of the alloy system is obtained by thermal analysis means; the thermal analysis means is differential scanning calorimetry or Differential thermal analysis. 5 . The PVD coating with strong (111) texture according to claim 1 , wherein the removing the filler on the surface of the product comprises placing the product in an alcohol medium for ultrasonic cleaning. 6 . 6. A PVD coating with strong (111) texture according to any one of claims 1-5, characterized in that: it is homogeneously continuous and uniformly covered on the surface of the hard material substrate, and the thickness is between 0.5 and 2.0 μm The bonding metal-enriched layer between them is formed by the tunnel effect formed by the powder gap in the mixed powder filler during the vacuum sintering process, which can controllably induce the directional migration of the liquid phase in the hard material to form in-situ; its thickness is determined by the sintering temperature Coordinated regulation with the holding time; the sintering temperature and holding time are respectively controlled at 10-40° C. and 40-120 min above the eutectic temperature of the alloy system.

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