Cutter for processing new-generation high-temperature alloy GH4065A and preparation method thereof

Abstract

The invention relates to the field of machining tools, and discloses a new-generation high-temperature alloy GH4065A machining tool and a preparation method of the new-generation high-temperature alloy GH4065A machining tool. Multi-dimensional mixed-sequence structure metal ceramic with multi-element and multi-dimensional metal atoms which are arranged randomly and are high in confusion degree is formed through sintering; the surface of the metal ceramic is broken and lacks atoms through activation pretreatment to generate large-area metal atom vacancies, so that the atomic capturing force of the surface of the metal ceramic is increased, the nitride is more easily captured by the vacancies of the surface of the metal ceramic, and the binding force between the nitride coating and a metal ceramic matrix is enhanced; in addition, the multi-dimensional mixed-sequence layer part on the surface of the metal ceramic is changed from order to disorder through intermittent lattice high-energy laser induction treatment, and lattice disordered lattices are generated; due to the fact that a large number of potential dislocation sources exist in disordered crystal lattices, under the impact load, the dislocation sources are easily activated, dislocation can absorb and dissipate a large number of impact energy through movement and interaction, and therefore the impact resistance of the metal ceramic cutter is improved.

Description

Technical Field

[0001] The invention relates to the field of machining tools and discloses a new generation of machining tools for high-temperature alloy GH4065A and a preparation method thereof. Background Art

[0002] Turbine disks are core hot-end components of gas turbines and aircraft engines, operating in extremely harsh environments. GH4065A, a new-generation high-temperature alloy with a room-temperature tensile strength of up to 1634 MPa, has become a key material for turbine disk manufacturing.

[0003] Common tool wear during the machining of GH4065A turbine disks is primarily a combination of mechanical wear, plastic deformation, workpiece adhesion, and diffusion wear between the workpiece and the tool. Furthermore, in the actual production of high-temperature alloy turbine disks, high feed rates and deep cuts are often employed to achieve high machining efficiency. The high impact and extrusion between the tool and the workpiece cause rapid tool surface wear, coating loss, and premature tool failure, severely impacting the machining quality of the high-temperature alloy turbine disk workpiece and significantly increasing the machining cost of the high-temperature alloy. Summary of the Invention

[0004] The purpose of the present invention is to provide a new generation of high-temperature alloy GH4065A machining tools and a preparation method thereof, which can enhance the bonding force between the nitride coating and the metal ceramic substrate while further improving the impact resistance of the metal ceramic tool.

[0005] In order to achieve the above technical effects, the technical solution adopted by the present invention is:

[0006] The preparation method of cutting tools for machining the new generation high-temperature alloy GH4065A includes:

[0007] The surface of the sintered metal ceramic tool is pre-treated with chemical reagents to activate the surface of the metal ceramic so as to break the bonds on the surface of the metal ceramic, wherein the metal ceramic contains at least seven metal elements;

[0008] The laser-induced treatment is performed on the surface of the metal ceramic after activation pretreatment by intermittent lattice laser, thereby inducing lattice distortion in the lattice region of the metal ceramic, so that a lattice disordered lattice containing a dislocation source is generated in the laser-induced region on the surface of the metal ceramic;

[0009] The impact-resistant tool is obtained by coating the surface of the metal ceramic after laser induction treatment with a nitride coating at least once.

[0010] Furthermore, the nitride coating is at least two layers, and after one or more nitride coatings before the last nitride coating, laser induced treatment is performed on the surface of the metal ceramic containing the nitride coating.

[0011] Furthermore, when the surface of the metal ceramic after activation pretreatment is laser-induced by intermittent lattice laser, the average power density of the laser-induced treatment is 1.5×10E6~2.5×10E6W / cm 2 , the laser scanning speed is 3-5 mm / s, the scanning width is 50-80 μm, and the number of laser surface treatments is 3-5 times;

[0012] When laser induced treatment is performed on the surface of metal ceramics containing nitride coating, the laser pulse time is 100 to 300 fs, and the average power density of laser induced is 3×10E6 to 5×10E6 W / cm 2 , laser scanning speed 5~10mm / min, surface treatment times 1~3 times.

[0013] Furthermore, the method of applying at least one nitride coating to the surface of the metal ceramic after laser induced treatment includes:

[0014] The metal ceramic sample was placed in a coating furnace with a laser generator, the sample rotation speed was 2-5 r / min, and the furnace was evacuated to a vacuum degree of less than 3.0×10 -3 Pa, the temperature in the furnace is controlled at 350~550℃;

[0015] A metal target with a mismatch between the nitride crystal structure and the metal ceramic substrate of less than 6% is selected, and the metal target is opened to deposit a nitride coating on the metal ceramic; wherein, the negative bias voltage is controlled from -20V to -200V, the target current is gradually increased to 120A~160A, the frequency is 30kHz, the duty cycle is 75%, the initial nitrogen ion gas flow rate is 20~120sccm, and the deposition time is 5min.

[0016] Furthermore, the metal target material includes Hf, Ta, Zr, Ti, Nb, and Al, and the metal target material includes two groups of alloy targets, wherein the first group of alloy targets is a geometric alloy target formed by two metal materials among Hf, Zr, and Al metals, and the second group of alloy targets is a geometric alloy target formed by two metal materials among Ta, Ti, and Nb metals.

[0017] Furthermore, the metal ceramic is prepared by mixing material A and material B, ball milling, and pressing to form a green body, and sintering the green body to obtain the corresponding metal ceramic cutting tool; wherein, by weight:

[0018] Material A includes Ti: 15-52 parts, Ni: 5.0-15.0 parts, Co: 5.0-15.0 parts, Cr: 5.0-15.0 parts, Nb: 5.0-15.0 parts, Ta: 5.0-15.0 parts, Mo: 2.0-16.0 parts, W: 2.0-15.0 parts, C: 2.0-7.0 parts, N: 2.0-3.0 parts;

[0019] Material B includes Ti: 50-62 parts, Ni: 2.0-3.0 parts, Co: 2.0-3.0 parts, Cr: 2.0-3.0 parts, Nb: 2.0-3.0 parts, Ta: 2.0-3.0 parts, Mo: 11.0-16.0 parts, W: 7.0-15.0 parts, C: 7.0-11.0 parts, and N: 2-3.

[0020] Furthermore, after the pressing is completed, electric field assisted sintering is performed, wherein the sintering heating rate is 15-25°C / min, the holding temperature is 1400-1500°C, the holding time is 45min-90min, and the vacuum degree during the sintering process is lower than 0.1Pa.

[0021] Furthermore, the method of using chemical reagents to activate the surface of the sintered metal ceramic tool includes:

[0022] Surface treatment of the metal ceramic is performed using an alkaline solution, wherein the mass concentration of the alkaline solution is 1 to 3 mol / L and the treatment time is 20 to 90 seconds;

[0023] The metal ceramic treated with the alkaline solution is then treated with a fluorinated aqueous regia solution, wherein the solute concentration in the fluorinated aqueous regia solution is 1.2 to 3.5 mol / L, and the solutes include HNO3, HCl, and HF, wherein the molar concentration ratio is HNO3:HCl:HF=1:1:2, and the treatment time is 45s to 100s;

[0024] After being treated with a fluorine-based aqueous regia solution, the metal ceramic is then subjected to a high activation treatment using an acidified potassium permanganate solution, wherein the concentration of the potassium permanganate is 0.001 mol / L to 0.01 mol / L. After the treatment for 1 to 3 hours, the metal ceramic is cleaned with alcohol.

[0025] Furthermore, before chemical reagents are used to perform activation pretreatment on the surface of the sintered metal ceramic tool, surface finishing is performed on the metal ceramic surface in steps, and then ultrasonic cleaning is used to clean the metal ceramic after the finishing treatment.

[0026] To achieve the above technical effects, the present invention also provides a new generation of high-temperature alloy GH4065A processing tool. The new generation of high-temperature alloy GH4065A processing tool is prepared by the preparation method of the new generation of high-temperature alloy GH4065A processing tool.

[0027] Compared with the prior art, the present invention has the following beneficial effects:

[0028] 1. The present invention forms a multi-dimensional mixed structure metal ceramic with multi-dimensional and multi-dimensional metal atoms randomly arranged with high disorder by sintering, and causes large-area metal atom vacancies to appear on the surface of the metal ceramic due to broken bonds and missing atoms through activation pretreatment, thereby increasing the ability of the metal ceramic surface to capture atoms, making it easier for nitrides to be captured by the vacancies on the surface of the metal ceramic, and enhancing the bonding force between the nitride coating and the metal ceramic substrate.

[0029] 2. The present invention further transforms the multi-dimensional mixed-order layer on the surface of the metal ceramic from ordered to disordered through discontinuous lattice high-energy laser induced treatment, thereby generating a lattice disordered lattice; utilizing the large number of potential dislocation sources in the disordered lattice to absorb and dissipate a large amount of impact energy under impact load, thereby improving the impact resistance of the metal ceramic tool. BRIEF DESCRIPTION OF THE DRAWINGS

[0030] Figure 1 This is a cross-sectional morphology of the substrate and coating of the multi-dimensional mixed order metal ceramic tool in Example 3;

[0031] Figure 2 This is a morphology image of the cross-section nanostructure of the multi-dimensional mixed-order metal ceramic tool coating in Example 3;

[0032] Figure 3 This is a dark field image of the internal columnar structure of the multi-dimensional mixed-order metal ceramic tool nano-multilayer coating in Example 3;

[0033] Figure 4 This is a comparison chart of the flank wear of the multi-dimensional mixed-sequence metal ceramic tool in Example 3 and the flank wear of the same type of commercial tool; DETAILED DESCRIPTION

[0034] The present invention will be described in further detail below with reference to the embodiments and accompanying drawings. However, this should not be construed as limiting the scope of the present invention to the following embodiments, as all technologies implemented based on the present invention fall within the scope of the present invention.

[0035] Example 1

[0036] The preparation method of cutting tools for machining the new generation high-temperature alloy GH4065A includes:

[0037] The surface of the sintered metal ceramic tool is pre-treated with chemical reagents to activate the surface of the metal ceramic so as to break the bonds on the surface of the metal ceramic, wherein the metal ceramic contains at least seven metal elements;

[0038] The laser-induced treatment is performed on the surface of the metal ceramic after activation pretreatment by intermittent lattice laser, thereby inducing lattice distortion in the lattice region of the metal ceramic, so that a lattice disordered lattice containing a dislocation source is generated in the laser-induced region on the surface of the metal ceramic;

[0039] The impact-resistant tool is obtained by coating the surface of the metal ceramic after laser induction treatment with a nitride coating at least once.

[0040] In this embodiment, since there are at least seven types of metal atoms in the metal ceramic, the atomic radius and the types of chemical bonds formed by atoms in the metal ceramic can be greatly different. During rapid sintering, a multi-dimensional mixed structure metal ceramic with a high degree of disorder and a random arrangement of multi-dimensional and multi-dimensional metal atoms is formed. Then, the surface of the metal ceramic rich in multi-dimensional mixed order metal phase is activated and pre-treated with chemical reagents, so that a multi-dimensional mixed order alloy phase with severe lattice distortion is formed in the surface rich in multi-dimensional mixed order alloy layer, resulting in broken bonds and missing atoms on the surface of the metal ceramic and the appearance of large-area metal atom vacancies, thereby increasing the ability of the metal ceramic surface to capture atoms, making it easier for nitrides to be captured by the vacancies on the surface of the metal ceramic, and enhancing the bonding between the nitride coating and the metal ceramic substrate. The bonding force between the bodies is enhanced by discontinuous lattice high-energy laser induction treatment, so that the multi-dimensional and multi-type metal atoms on the surface of the multi-dimensional mixed-order metal ceramic, which has been activated by surface lattice bond breaking treatment, produce a sharp high-energy change in the micron-level micro-region, the vibration between atoms is enhanced, the lattice expands rapidly, and some chemical bonds are broken, inducing the multi-dimensional mixed-order layer on the surface of the metal ceramic with high lattice distortion to partially transform from order to disorder, and produce a lattice disordered lattice; due to the presence of a large number of potential dislocation sources in the disordered lattice, the dislocation sources are easily activated under impact load, and the dislocations can absorb and dissipate a large amount of impact energy through movement and interaction, thereby improving the impact resistance of the metal ceramic tool.

[0041] In addition, in the metal ceramic cutting tool obtained by the preparation method of this embodiment, there is a multi-dimensional mixed-order structure with full order and disorder alternatingly arranged, and there are also secondary nanolayers in each nanolayer. The multi-dimensional mixed-order effect of the multi-dimensional mixed-order structure, the superlattice effect of the nanolayer, and the super-strong energy release ability of the disordered lattice can be fully utilized, which can significantly improve the ability to inhibit crack initiation and expansion in the coating while improving the bonding strength between the coating and the tool.

[0042] Example 2

[0043] The preparation method of cutting tools for machining the new generation high-temperature alloy GH4065A includes:

[0044] S1: Preparation of multidimensional mixed-order metal ceramics;

[0045] In this embodiment, a multi-dimensional mixed-order metal ceramic with stable structure can be achieved through lamination + microwave sintering. The preparation process of the metal ceramic mainly includes four stages: batching, ball milling, pressing, and sintering.

[0046] During the batching process, two different components, A and B, were selected for preparation. By weight, A includes 40% Ti, 5.0% Ni, 5.0% Co, 5.0% Cr, 5.0% Nb, 5.0% Ta, 12.0% Mo, 12.0% W, 9.0% C, and 2.0% N. The total weight percentages of these elements total 100%. B includes 62% Ti, 2.0% Ni, 2.0% Co, 2.0% Cr, 2.0% Nb, 2.0% Ta, 11.0% Mo, 7.0% W, 7.0% C, and 3.0% N. The total weight percentages of these elements total 100%.

[0047] The powders were weighed according to the above formula and loaded into different ball mills together with cemented carbide balls. Alcohol was added and the mixture was ball milled for 72 hours. The forming agent was added and the mixture was sieved and granulated.

[0048] The powder of material B after granulation is filled into the required mold. The required weight is 4 / 5 of the actual weight of the metal ceramic tool sample. Pre-compression is achieved under a pressure of 10T. Then, the powder of material A after granulation is filled into the required mold and covered on the pre-embrane of material B. The required weight of material A is 1 / 5 of the actual weight of the metal ceramic tool. After pre-compression under a pressure of 10T, the entire sample is finally compressed with a pressure of 100T to form a gradient laminated structure with good tool performance.

[0049] After the pressing is completed, microwave rapid sintering is performed to obtain a multidimensional mixed order metal ceramic, wherein the sintering heating rate is 15°C / min, the holding temperature is 1520°C, the holding time is 45min, and the vacuum degree during the sintering process is less than 0.1Pa.

[0050] S2: Surface activation treatment of multi-dimensional mixed order metal ceramics;

[0051] In this embodiment, the surface of the multi-dimensional mixed order metal ceramic is ground and polished step by step until it is smooth. After polishing, the sample is ultrasonically cleaned and then surface treated with a solution containing 1 mol / L NaOH for 20 seconds.

[0052] The metal ceramics after alkaline solution treatment are treated with HNO3, HCl, and HF solutions containing an acid concentration of 1.2 mol / L, where the concentration ratio of the three acids is 1:1:2, and the treatment time is 45 s; after the surface of the multi-dimensional mixed-order metal ceramics after the above treatment changes color (black), they are then subjected to high activation treatment with an acidic potassium permanganate solution, where the concentration of the acidic potassium permanganate solution is 0.001 mol / L, and the treatment time is 1 h. The treated metal ceramics are then cleaned with alcohol again.

[0053] S3: Femtosecond Laser Induced Processing of Multidimensional Mixed Order Metal Ceramics

[0054] In this embodiment, the average power density of the laser is 1.5×10E6 W / cm 2 The laser scanning speed is 3mm / s, the scanning width is 50μm, and the surface is laser treated 3 times; through the rapid high-energy changes in the micron-level micro-area, the vibration between atoms is enhanced, the lattice expands rapidly, and some chemical bonds are broken, inducing the multi-dimensional mixed-order layer on the surface of the metal ceramic with high lattice distortion to partially transform from ordered to disordered.

[0055] S4: Nano multi-dimensional mixed order nitride coating;

[0056] In this embodiment, the sample after femtosecond laser induction treatment was placed in a coating furnace with a laser generator. The sample rotation speed was 2-5 r / min. The furnace was evacuated using a mechanical pump and a molecular pump. The vacuum degree was less than 3.0×10 -3 Pa, the temperature in the furnace is controlled at 350℃, heated for 60min, and two groups of alloy targets are opened to deposit metal ceramics, where the purity of the alloy targets is greater than 99%. The first group of targets are Hf and Zr metal equiproportional alloy targets, and the second group of targets are Ta and Nb equiproportional alloy targets; the negative bias voltage is gradually increased from -20V to -200V, the target current is 120A, the frequency is 30kHz, the duty cycle is 75%, the nitrogen flow rate is 60sccm, and the deposition time is 5min.

[0057] S5: Laser-induced processing of lattice-shaped multi-dimensional mixed-order nitride coatings

[0058] In this embodiment, after the sample is coated with a nano multi-dimensional mixed order coating, a laser generator is used to perform femtosecond laser induced treatment on the tool with the multi-dimensional mixed order coating. The laser pulse time is 100fs and the power is 3×10E6W / cm 2 , laser scanning speed 5mm / min, surface treatment times 1 time; through the nano-scale micro-area point energy instantaneously increased in 10-15 seconds, forming a nano-scale disordered micro-area in the interface layer.

[0059] S6: Multilayer nitride coating

[0060] In this embodiment, the metal ceramic is deposited by alternately opening the Hf, Zr metal alloy target and the Ta, Nb alloy target, the negative bias voltage is increased from -100V to -150V, the target current is gradually increased to 80A~120A, the frequency is 30kHz, the duty cycle is 75%, the nitrogen flow rate is 60sccm, and the deposition time is 60min, thereby obtaining the impact-resistant tool.

[0061] The fracture toughness of the metal ceramic tool matrix prepared in this embodiment is 7.6 MPa·m 1 / 2, hardness 1638HV30, coating hardness at room temperature is 41.3GPa, high temperature hardness at 1000℃ is 36.3GPa, coating bonding force is 135N, which can meet cutting speed Vc=3m / min, tooth lift 0.2mm, stable cutting distance ≥15m.

[0062] Example 3

[0063] The preparation method of cutting tools for machining the new generation high-temperature alloy GH4065A includes:

[0064] S1: Preparation of multidimensional mixed-order metal ceramics;

[0065] In this embodiment, a multi-dimensional mixed-order metal ceramic with stable structure can be achieved by lamination + microwave sintering. The preparation process of the metal ceramic mainly includes four stages: batching, ball milling, pressing, and sintering.

[0066] During the batching process, two different components, A and B, were selected and prepared. By weight, A includes Ti:17, Ni:15.0, Co:15.0, Cr:15.0, Nb:15.0, Ta:15.0, Mo:2.0, W:2.0, C:2.0, and N:2.0, with the total weight percentage of the different elements being 100%. B includes Ti:50, Ni:3.0, Co:3.0, Cr:3.0, Nb:3.0, Ta:3.0, Mo:12.0, W:12.0, C:8.0, and N:3, with the total weight percentage of the different elements being 100%.

[0067] The powders were weighed according to the above formula and loaded into different ball mills together with cemented carbide balls. Alcohol was added and the mixture was ball milled for 72 hours. The forming agent was added and the mixture was sieved and granulated.

[0068] The powder of material B after granulation is filled into the required mold. The required weight is 4 / 5 of the actual weight of the metal ceramic tool sample. Pre-compression is achieved under a pressure of 10T. Then the powder of material A after granulation is filled into the required mold and covered on the pre-embrane of material B. The required weight of material A is 1 / 5 of the actual weight of the metal ceramic tool. After pre-compression under a pressure of 10T, the entire sample is finally compressed using a pressure of 100T.

[0069] After the pressing is completed, microwave rapid sintering is performed to obtain a multidimensional mixed-order metal ceramic, wherein the sintering heating rate is 25°C / min, the holding temperature is 1500°C, the holding time is 90min, and the vacuum degree during the sintering process is less than 0.1Pa.

[0070] S2: Surface activation treatment of multi-dimensional mixed order metal ceramics;

[0071] In this embodiment, the surface of the multi-dimensional mixed order metal ceramic is ground and polished step by step until it is smooth by grinding and polishing. After polishing, the sample is ultrasonically cleaned and then surface treated with a solution containing 3 mol / L NaOH for 90 seconds.

[0072] The metal ceramics after alkaline solution treatment are treated with HNO3, HCl, and HF solutions containing an acid concentration of 3.5 mol / L, where the concentration ratio of the three acids is 1:1:2, and the treatment time is 100 s; after the surface of the multi-dimensional mixed-order metal ceramics after the above treatment changes color (black), they are then subjected to high activation treatment with an acidic potassium permanganate solution, where the concentration of the acidic potassium permanganate solution is 0.001 mol / L, and the treatment time is 3 h. The treated metal ceramics are then cleaned with alcohol again.

[0073] S3: Femtosecond Laser Induced Processing of Multidimensional Mixed Order Metal Ceramics

[0074] In this embodiment, the average power density of the laser is 2.5×10E6 W / cm 2 The laser scanning speed is 5mm / s, the scanning width is 80μm, and the number of laser surface treatments is 5 times; through the rapid high-energy changes in micron-level micro-areas, the vibration between atoms is enhanced, the lattice expands rapidly, and some chemical bonds are broken, inducing the multi-dimensional mixed-order layer on the surface of the metal ceramic with high lattice distortion to partially transform from ordered to disordered.

[0075] S4: Nano multi-dimensional mixed order nitride coating;

[0076] In this embodiment, the sample after femtosecond laser induction treatment was placed in a coating furnace with a laser generator. The sample rotation speed was 2-5 r / min. The furnace was evacuated using a mechanical pump and a molecular pump. The vacuum degree was less than 3.0×10 -3 Pa, the temperature in the furnace is controlled at 550℃, heated for 60min, and two groups of alloy targets are opened to deposit metal ceramics, where the purity of the alloy targets is greater than 99%. The first group of targets are Hf and Zr metal alloy targets, and the second group of targets are Ta and Nb alloy targets. The negative bias voltage is gradually increased from -20V to -200V, and the target current is 160A, the frequency is 30kHz, the duty cycle is 75%, the nitrogen flow rate is 80sccm, and the deposition time is 5min.

[0077] S5: Laser-induced processing of lattice-shaped multi-dimensional mixed-order nitride coatings

[0078] In this embodiment, after the sample is coated with a nano multi-dimensional mixed order coating, a laser generator is used to perform femtosecond laser induced treatment on the tool with the multi-dimensional mixed order coating. The laser pulse time is 100fs and the power is 5×10E6W / cm 2, laser scanning speed 10mm / min, surface treatment times 3 times.

[0079] S6: Multilayer nitride coating

[0080] In this embodiment, the sample cleaned by ultrasonic cleaning was placed in the coating furnace, the sample rotation speed was 2 r / min, and the furnace was evacuated using a mechanical pump and a molecular pump, and the vacuum degree was less than 3.0×10 -3 Pa, the furnace temperature is controlled at 350°C, heated for 20 minutes, and alloy targets are alternately opened to deposit metal ceramics. The alloy targets have a purity greater than 99% and are composed of two isomeric alloy targets of metals such as Hf and Al, with a second set of targets made of Ta and Ti. The negative bias voltage is increased from -20V to -200V, the target current is gradually increased from 120A to 160A, the frequency is 30kHz, the duty cycle is 75%, the nitrogen flow rate is 80sccm, and the deposition time is 60 minutes. After the coating process is completed, the furnace temperature is allowed to cool to room temperature to obtain a multi-dimensional mixed-order metal ceramic tool.

[0081] The fracture toughness of the metal ceramic tool matrix prepared in this embodiment is 13.8 MPa·m 1 / 2 , hardness 1423HV 30 The coating has a room temperature hardness of 40.4GPa and a high temperature hardness of 34.9GPa at 1000℃. The coating bonding force is 135N, which can meet the cutting speed Vc=5m / min, tooth lift 0.4mm, and stable cutting distance ≥9m.

[0082] By testing the cross-sectional morphology of the multi-dimensional mixed order metal ceramic tool of this embodiment, the cross-sectional morphology of the matrix and coating of the multi-dimensional mixed order metal ceramic tool is obtained. Figure 1 As shown; the nano-layer structure morphology of the coating cross section is as follows Figure 2 As shown; dark field image of the columnar structure inside the nano multilayer coating (i.e. Figure 2 The morphology corresponding to the dark field phase mode is as follows Figure 3 As shown. Figure 2 It can be seen that sub-nano layers are formed between the nano-layer structures in the coating cross section.

[0083] In addition, the multi-dimensional mixed order metal ceramic tool of this embodiment was compared with the existing commercial tool of the same type under the same cutting parameters (cutting speed Vc = 5m / min, cutting depth ap = 0.4mm) to cut the high-temperature alloy GH4065A turbine disk. After the test, the comparison of the flank wear of the same type of commercial tool and the multi-dimensional mixed order metal ceramic tool of this embodiment was collected as shown in the figure. Figure 4 As shown, it can be seen that the flank wear of the multi-dimensional mixed-sequence metal ceramic tool in this embodiment is significantly lower than the flank wear of the commercial tool of the same model.

[0084] The above are only preferred embodiments of the present invention and are not intended to limit the present invention. Any modifications, equivalent substitutions and improvements made within the spirit and principles of the present invention should be included in the scope of protection of the present invention.

Claims

1. A method for preparing a cutting tool for machining a new generation of high-temperature alloy GH4065A, characterized in that: include: The surface of the sintered metal ceramic tool is pre-treated with chemical reagents to activate the surface of the metal ceramic so as to break the bonds on the surface of the metal ceramic, wherein the metal ceramic contains at least seven metal elements; The laser-induced treatment is performed on the surface of the metal ceramic after activation pretreatment by intermittent lattice laser, thereby inducing lattice distortion in the lattice region of the metal ceramic, so that a lattice disordered lattice containing a dislocation source is generated in the laser-induced region on the surface of the metal ceramic; The impact-resistant tool is obtained by coating the surface of the metal ceramic after laser induction treatment with a nitride coating at least once.

2. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 1, characterized in that: The nitride coating is at least two layers, and after one or more nitride coatings before the last nitride coating, laser induced treatment is performed on the surface of the metal ceramic containing the nitride coating.

3. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 2, characterized in that: When the surface of the metal ceramic after activation pretreatment is laser-induced by intermittent dotted laser, the average power density of the laser is 1.5×10E6~2.5×10E6W / cm 2 , the laser scanning speed is 3-5 mm / s, the scanning width is 50-80 μm, and the number of laser surface treatments is 3-5 times; When laser induced treatment is performed on the surface of metal ceramics containing nitride coating, the laser pulse time is 100 to 300 fs, and the average power density of laser induced is 3×10E6 to 5×10E6 W / cm 2 , laser scanning speed 5~10mm / min, surface treatment times 1~3 times.

4. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 2, characterized in that: The method of applying at least one nitride coating to a metal-ceramic surface after laser induced treatment comprises: The metal ceramic sample was placed in a coating furnace with a laser generator, the sample rotation speed was 2-5 r / min, and the furnace was evacuated to a vacuum degree of less than 3.0×10 -3 Pa, the temperature in the furnace is controlled at 350~550℃; A metal target with a mismatch between the nitride crystal structure and the metal ceramic substrate of less than 6% is selected, and the metal target is opened to deposit a nitride coating on the metal ceramic; wherein, the negative bias voltage is controlled from -20V to -200V, the target current is gradually increased to 120A~160A, the frequency is 30kHz, the duty cycle is 75%, the initial nitrogen ion gas flow rate is 20~120sccm, and the deposition time is 5min.

5. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 4, characterized in that: The metal target materials include Hf, Ta, Zr, Ti, Nb, and Al, and the metal target materials include two groups of alloy targets, wherein the first group of alloy targets is a geometric alloy target formed by two metal materials among Hf, Zr, and Al metals, and the second group of alloy targets is a geometric alloy target formed by two metal materials among Ta, Ti, and Nb metals.

6. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 1, characterized in that: The metal ceramic is prepared by mixing material A and material B, ball milling, and pressing to form a green body, and sintering the green body to obtain the corresponding metal ceramic cutting tool; wherein, by weight: Material A includes Ti: 15-52 parts, Ni: 5.0-15.0 parts, Co: 5.0-15.0 parts, Cr: 5.0-15.0 parts, Nb: 5.0-15.0 parts, Ta: 5.0-15.0 parts, Mo: 2.0-16.0 parts, W: 2.0-15.0 parts, C: 2.0-7.0 parts, N: 2.0-3.0 parts; Material B includes Ti: 50-62 parts, Ni: 2.0-3.0 parts, Co: 2.0-3.0 parts, Cr: 2.0-3.0 parts, Nb: 2.0-3.0 parts, Ta: 2.0-3.0 parts, Mo: 11.0-16.0 parts, W: 7.0-15.0 parts, C: 7.0-11.0 parts, and N: 2-3.

7. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 6, characterized in that: After the pressing is completed, electric field assisted sintering is performed, wherein the sintering heating rate is 15-25°C / min, the holding temperature is 1400-1500°C, the holding time is 45min-90min, and the vacuum degree is lower than 0.1Pa during the sintering process.

8. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 1, characterized in that: The method of using chemical reagents to activate the surface of sintered metal ceramic tool pretreatment includes: Surface treatment of the metal ceramic is performed using an alkaline solution, wherein the mass concentration of the alkaline solution is 1 to 3 mol / L and the treatment time is 20 to 90 seconds; The metal ceramic treated with the alkaline solution is then treated with a fluorinated aqueous regia solution, wherein the solute concentration in the fluorinated aqueous regia solution is 1.2 to 3.5 mol / L, and the solutes include HNO3, HCl, and HF, wherein the molar concentration ratio is HNO3:HCl:HF=1:1:2, and the treatment time is 45s to 100s; After being treated with a fluorine-based aqueous regia solution, the metal ceramic is then subjected to a high activation treatment using an acidified potassium permanganate solution, wherein the concentration of the potassium permanganate is 0.001 mol / L to 0.01 mol / L. After the treatment for 1 to 3 hours, the metal ceramic is cleaned with alcohol.

9. The method for preparing a cutting tool for machining the new generation high-temperature alloy GH4065A according to claim 1, characterized in that: Before chemical reagents are used to activate the surface of the sintered metal ceramic tool, the surface of the metal ceramic is pre-finished step by step by surface finishing processing, and then the metal ceramic after the finishing treatment is cleaned by ultrasonic wave.

10. A new generation of high temperature alloy GH4065A processing tools, characterized by: The new generation high temperature alloy GH4065A machining tool is prepared by the preparation method of the new generation high temperature alloy GH4065A machining tool according to any one of claims 1 to 9.

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