A non-magnetic high-entropy alloy cermets and a preparation method thereof

Abstract

This invention discloses a non-magnetic high-entropy alloy-bonded cermet and its preparation method. The raw material composition includes: (Ti,W)C ceramic phase 50-84.5 wt.%, alloy binder 15-32 wt.%, Cr3C 20-8 wt.%, and Mo 0-12 wt.%. The alloy binder is at least one selected from FeCoCrNiMo, FeCoCrNi, and CrFeNiMo. The cermet prepared by this invention using a high-entropy alloy with good sinterability as the binder phase exhibits excellent room-temperature non-magnetic properties, good mechanical properties, good corrosion resistance, wear resistance, and long service life. It achieves a balance between high hardness and non-magnetism. It can be applied in multiple fields, such as wear-resistant parts in the electronics industry and generator retaining rings.

Description

Technical Field

[0001] This invention relates to the field of ceramic technology, specifically to a non-magnetic high-entropy alloy-bonded cermet and its preparation method. Background Technology

[0002] (Ti,W)C-based cermets possess high hardness, good wear resistance, and chemical stability, and have been widely used in cutting tools and wear-resistant parts. Cermets are mainly composed of a ceramic phase and a binder. The type and content of the binder phase largely determine the overall performance of the cermet. Commonly used binders in cermets include Ni, Co, or Ni-Co. However, Ni and Co are ferromagnetic at room temperature, and cermets using them as binders have certain shortcomings in terms of non-magnetism, corrosion resistance, and wear resistance, limiting their application in electronic components, magnetic powder processing, and other fields.

[0003] High-entropy alloys possess superior properties such as high strength, good corrosion resistance, and good wear resistance, and have a wide range of compositional designs, making them very suitable for replacing Ni, Co, or Ni-Co as binder phases. However, high-entropy alloys exhibit a slow diffusion effect, and the dissolution and diffusion behavior of cermets using them as binder phases during sintering is complex. Therefore, controlling the magnetic and mechanical properties of cermets is quite difficult. Summary of the Invention

[0004] The technical problem to be solved by this invention is that high-entropy alloys have a slow diffusion effect, and the dissolution and diffusion behavior of metal ceramics with them as binder phases during sintering is complex. Therefore, it is difficult to control the magnetic and mechanical properties of metal ceramics. This invention provides a non-magnetic high-entropy alloy-bonded metal ceramic and its preparation method to solve the above problems.

[0005] This invention is achieved through the following technical solution:

[0006] A non-magnetic high-entropy alloy-bonded metal-ceramic, comprising the following raw materials:

[0007] (Ti,W)C ceramic phase 50–84.5 wt.%, alloy binder 15–32 wt.%, Cr3C 20–8 wt.%, and Mo 0–12 wt.%.

[0008] The alloy adhesive is at least one of FeCoCrNiMo, FeCoCrNi, and CrFeNiMo.

[0009] This invention uses (Ti,W)C as the ceramic phase and at least one of CrFeNiMo, FeCoCrNiMo, and FeCoCrNi as the binder phase; more preferably, Mo can be added as the binder phase and Cr3C2 as an additive. Due to the weak interaction between the constituent elements, the high-entropy alloy exhibits good stability in corrosive environments and is not easily oxidized or rusted. High-entropy alloys can achieve excellent physical, chemical, and mechanical properties by adjusting their composition and structure. This invention utilizes the cocktail effect and the corrosion resistance, high hardness, and high strength properties of high-entropy alloys to adjust the comprehensive properties of cermets. During the sintering process of cermets, the large-scale solid solution of antiferromagnetic elements Cr, paramagnetic elements Ti, W, and / or Mo in the binder phase achieves the purpose of non-magnetism.

[0010] Further optionally, the raw material composition includes:

[0011] ((Ti,W)C ceramic phase 58–70 wt.), alloy binder 30 wt., Cr3C 20–5 wt., and Mo 0–10 wt.)

[0012] Further optionally, the raw material composition includes: 57-60 wt.% (Ti,W)C ceramic phase, 30 wt.% alloy binder, 2-5 wt.% Cr3C2, and 5-10 wt.% Mo;

[0013] The alloy adhesive used is FeCoCrNiMo.

[0014] A method for preparing a non-magnetic high-entropy alloy-bonded metal-ceramic, comprising the following steps:

[0015] The raw materials are wet-milled to obtain a slurry, which is then dried, shaped, and sintered to prepare a non-magnetic high-entropy alloy-bonded metal ceramic.

[0016] Further optionally, the wet grinding process involves bonding non-magnetic high-entropy alloys to metal ceramics using anhydrous ethanol as the process control agent; the wet abrasive ball ratio is 6:1 to 8:1, the rotation speed is 200 rpm to 220 rpm, and the wet grinding time is 36 h to 60 h.

[0017] Alternatively, a drying process may be performed: the drying temperature is 79℃~90℃, and the drying time is 8h~15h.

[0018] Further, optionally, sintering treatment: sintering temperature of 1420℃~1450℃, sintering time of 60min~80min, and maintaining the vacuum degree in the furnace at 10 -2 Pa~10 -1 Pa.

[0019] Alternatively, the alloy binder in the raw material is obtained by the following preparation method, which includes the following steps:

[0020] The desired metal element powders of Fe, Cr, and Ni, as well as at least one of Mo and Co, are mixed in an equimolar ratio, wet-milled under an inert atmosphere, and then dried under vacuum to obtain the final product.

[0021] Further optionally, wet milling is performed: 0.5% to 4% anhydrous ethanol is used as the process control agent; the ball-to-material ratio is 15:1, the rotation speed is 300 r / min to 350 r / min, and the wet milling time is 40 h to 60 h.

[0022] Alternatively, the vacuum drying temperature is 79℃~90℃, and the drying time is 8h~15h.

[0023] The present invention has the following advantages and beneficial effects:

[0024] 1. This invention produces a cermet using a high-entropy alloy with good sinterability as the binder phase. This cermet exhibits excellent room-temperature non-magnetic properties, good mechanical properties, good corrosion resistance, wear resistance, and a long service life. It achieves a balance between high hardness and non-magnetic properties. It can be applied in various fields, such as wear-resistant parts in the electronics industry and generator retaining rings.

[0025] 2. The high-entropy alloy powder prepared by high ball milling in this invention can improve the sintering properties of metal ceramics. The process is simple and suitable for mass production in industry.

[0026] 3. The non-magnetic high-entropy alloy-bonded metal ceramic provided by this invention can be applied in multiple fields, such as wear-resistant parts in the electronics industry and generator retaining rings. Attached Figure Description

[0027] The accompanying drawings, which are included to provide a further understanding of embodiments of the invention and form part of this application, do not constitute a limitation thereof. In the drawings:

[0028] Figure 1 This is a SEM image of the sample provided in Example 5 of the present invention.

[0029] Figure 2 The hysteresis loop diagram of the sample provided in Embodiment 5 of the present invention. Detailed Implementation

[0030] To make the objectives, technical solutions, and advantages of the present invention clearer, the present invention will be further described in detail below with reference to the embodiments and accompanying drawings. The illustrative embodiments and descriptions of the present invention are only used to explain the present invention and are not intended to limit the present invention.

[0031] Example 1

[0032] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0033] Fe, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 1% anhydrous ethanol was added as a process control agent, and the mixture was ball-milled for 50 hours under an argon atmosphere at a ball-to-material ratio of 15:1 and a rotation speed of 300 r / min. Then, the mixture was placed in an oven and dried at 80℃ for 12 hours. The FeCrNiMo high-entropy alloy powder was obtained by sieving.

[0034] 70 wt.% (Ti,W)C powder and 30 wt.% FeCrNiMo powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 36 h using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 8:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 79°C for 15 h to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 400 MPa for 1 min. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1420°C for 60 min, with the vacuum level maintained at 10°C. -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0035] The bending strength is 711 MPa, the hardness is 89 HRA, and the magnetic susceptibility is <10. -3 .

[0036] Example 2

[0037] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0038] Fe, Co, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 0.5% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 60 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 320 r / min. The powder was then dried in an oven at 79°C for 15 hours and sieved to obtain FeCoCrNiMo high-entropy alloy powder.

[0039] 60 wt.% (Ti,W)C powder, 30 wt.% FeCoCrNiMo powder, 2 wt.% Cr3C2, and 8 wt.% Mo powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 hours using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 7:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 90°C for 10 hours to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 minute. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 60 minutes, with the vacuum level maintained at 10 kJ / min. -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0040] The bending strength is 724 MPa, the hardness is 88.2 HRA, and the magnetic susceptibility is <10. -3 .

[0041] Example 3

[0042] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0043] Fe, Co, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 0.5% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 60 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 320 r / min. The powder was then dried in an oven at 79°C for 15 hours and sieved to obtain FeCoCrNiMo high-entropy alloy powder.

[0044] 63 wt.% (Ti,W)C powder, 30 wt.% FeCoCrNiMo powder, 2 wt.% Cr3C2, and 5 wt.% Mo powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 hours using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 7:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 90°C for 10 hours to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 minute. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 60 minutes, with the vacuum level maintained at 10 kJ / min. -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0045] The flexural strength is 756 MPa, the hardness is 88.7 HRA, and the magnetic susceptibility is <10. -3 .

[0046] Example 4

[0047] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0048] Fe, Co, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 0.5% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 60 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 320 r / min. The powder was then dried in an oven at 79°C for 15 hours and sieved to obtain FeCoCrNiMo high-entropy alloy powder.

[0049] Weigh out 58 wt.% (Ti,W)C powder, 30 wt.% FeCoCrNiMo powder, 2 wt.% Cr3C2, and 10 wt.% Mo powder, then mix them with anhydrous ethanol and wet-mill them using a planetary ball mill for 48 min to obtain a homogeneous slurry. WC-Co balls were used in the ball milling process at a ball-to-powder ratio of 7:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 90℃ for 10 h to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 min. The sintering process was carried out in a vacuum sintering furnace at a sintering temperature of 1450℃ for 60 min, with the vacuum level maintained at 10... -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0050] The bending strength is 827 MPa, the hardness is 89.1 HRA, and the magnetic susceptibility is <10. -3 .

[0051] Example 5

[0052] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0053] Fe, Co, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 0.5% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 60 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 320 r / min. The powder was then dried in an oven at 79°C for 15 hours and sieved to obtain FeCoCrNiMo high-entropy alloy powder.

[0054] 66 wt.% (Ti,W)C powder, 30 wt.% FeCoCrNiMo powder, and 4 wt.% Cr3C2 powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 min using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 7:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 90°C for 10 h to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 min. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 60 min, with the vacuum level maintained at 10°C. -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0055] The bending strength is 911 MPa, the hardness is 87.9 HRA, and the magnetic susceptibility is <10. -3 .

[0056] Example 6

[0057] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0058] Fe, Co, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 0.5% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 60 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 320 r / min. The powder was then dried in an oven at 79°C for 15 hours and sieved to obtain FeCoCrNiMo high-entropy alloy powder.

[0059] 57 wt.% (Ti,W)C powder, 30 wt.% FeCoCrNiMo powder, 5 wt.% Cr3C2, and 8 wt.% Mo powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 hours using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 7:1, and the milling speed was 200 rpm. The slurry was then dried in an oven at 90°C for 10 hours to remove the anhydrous ethanol, and the powder mixture was then separated through a sieve. Finally, the powder mixture was unidirectionally pressed into shape under a pressure of 300 MPa for 1 minute. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 60 minutes, with the vacuum level maintained at 10 kJ / min. -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0060] The flexural strength is 734 MPa, the hardness is 88.7 HRA, and the magnetic susceptibility is <10. -3 .

[0061] Example 7

[0062] This embodiment provides a non-magnetic high-entropy alloy-bonded metal ceramic, and the specific preparation method is as follows:

[0063] Fe, Co, Cr, and Ni elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 4% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 40 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 350 r / min. The powder was then dried in an oven at 90℃ for 8 hours and sieved to obtain FeCoCrNi high-entropy alloy powder.

[0064] 60 wt.% (Ti,W)C powder, 30 wt.% FeCoCrNi powder, and 10 wt.% Mo powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 60 h using a planetary ball mill to obtain a uniformly mixed slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 6:1, and the milling speed was 220 rpm. Next, the slurry was dried in an oven at 85°C for 12 h to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 400 MPa for 1 min. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 80 min, with the vacuum level maintained at 10°C. -2 ~10 -1 Pa. A room-temperature non-magnetic high-entropy alloy-bonded metal ceramic was prepared.

[0065] The flexural strength is 766 MPa, the hardness is 86.6 HRA, and the magnetic susceptibility is <10. -3 .

[0066] Comparative Example 1

[0067] This case study presents an alloy-bonded metal-ceramic, the specific preparation method of which is shown below:

[0068] Fe, Co, Cr, Ni, and Mo elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 1% anhydrous ethanol was added as a process control agent. The mixture was ball-milled for 50 hours under an argon atmosphere at a ball-to-material ratio of 15:1 and a rotation speed of 300 r / min. The powder was then dried in an oven at 80°C for 12 hours and sieved to obtain FeCoCrNiMo high-entropy alloy powder.

[0069] 70 wt.% (Ti,W)C powder and 30 wt.% FeCoCrNiMo powder were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 hours using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 7:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 80°C to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 minute. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 60 minutes, with the vacuum level maintained at 10°C. -2 ~10 -1 The high-entropy alloy-bonded cermet prepared by Pa exhibits ferromagnetism at room temperature.

[0070] The bending strength is 656 MPa, the hardness is 89 HRA, and the magnetic susceptibility is >10. -3 .

[0071] Comparative Example 2

[0072] This case study presents an alloy-bonded metal-ceramic, the specific preparation method of which is shown below:

[0073] Fe, Co, Cr, Ni, and Mn elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 4% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 40 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 350 r / min. The powder was then dried in an oven at 90℃ for 8 hours and sieved to obtain FeCoCrNiMn high-entropy alloy powder.

[0074] 70 wt.% (Ti,W)C powder and 30 wt.% FeCoCrNiMn were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 h using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 6:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 85°C for 12 h to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 min. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1550°C for 60 min, with the vacuum level maintained at 10 kJ / min. -2 ~10 -1 Pa. A high-entropy alloy-bonded cermet exhibiting ferromagnetism at room temperature was prepared.

[0075] The bending strength is 456 MPa, the hardness is 91.4 HRA, and the magnetic susceptibility is >10. -3 .

[0076] Comparative Example 3

[0077] This case study presents an alloy-bonded metal-ceramic, the specific preparation method of which is shown below:

[0078] Fe, Co, Cr, Ni, and Al elemental powders with a purity of 99.9% were weighed in an equimolar ratio and placed in a stainless steel ball mill jar. 4% anhydrous ethanol was added as a process control agent. The powder was ball-milled for 40 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 350 r / min. The powder was then dried in an oven at 90℃ for 8 hours and sieved to obtain FeCoCrNiAl high-entropy alloy powder.

[0079] 70 wt.% (Ti,W)C powder and 30 wt.% FeCoCrNiAl were weighed and mixed with anhydrous ethanol. The mixture was then wet-milled for 48 h using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-powder ratio of 6:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 85°C for 12 h to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 min. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1450°C for 60 min, with the vacuum level maintained at 10°C. -2 ~10 -1 The high-entropy alloy-bonded cermet prepared by Pa exhibits ferromagnetism at room temperature.

[0080] The bending strength is 552 MPa, the hardness is 88 HRA, and the magnetic susceptibility is >10. -3 .

[0081] Comparative Example 4

[0082] This case study presents an alloy-bonded metal-ceramic, the specific preparation method of which is shown below:

[0083] Co, Cr, Fe, Ni, and Mo elemental powders with a purity of 99.9% were weighed at a molar ratio of 1:0.2:1:1:0.8 and placed in a stainless steel ball mill jar. 4% anhydrous ethanol was added as a process control agent. The mixture was ball-milled for 40 hours under an argon atmosphere at a ball-to-powder ratio of 15:1 and a rotation speed of 350 r / min. The mixture was then dried in an oven at 90℃ for 8 hours and sieved to obtain FeCo. 0.2 CrNiMo 0.8 High-entropy alloy powder.

[0084] Weigh out 70 wt.% (Ti,W)C powder and 30 wt.% FeCo 0.2 CrNiMo 0.8The mixture was then mixed with anhydrous ethanol and wet-milled for 48 hours using a planetary ball mill to obtain a homogeneous slurry. WC-Co balls were used in the milling process at a ball-to-material ratio of 7:1, and the milling speed was 200 rpm. Next, the slurry was dried in an oven at 80°C for 12 hours to remove the anhydrous ethanol, and then the mixed powder was separated through a sieve. Finally, the mixed powder was unidirectionally pressed into shape under a pressure of 300 MPa for 1 minute. The sintering process was carried out in a vacuum sintering furnace at a temperature of 1420°C for 60 minutes, with the vacuum level maintained at 10 kJ / min. -2 ~10 -1 The high-entropy alloy-bonded cermet prepared by Pa exhibits ferromagnetism at room temperature.

[0085] The flexural strength is 793 MPa, the hardness is 88.5 HRA, and the magnetic susceptibility is >10. -3 .

[0086] Performance testing

[0087] 1. Testing Method

[0088] (1) Bending strength: The universal testing machine is used to test the three-point bending strength of the metal ceramic specimen. The specimen is placed on the two support columns (span: 14.5 mm) on the testing machine fixture, and pressure is applied to the center of the specimen until the specimen breaks. The bending strength of the specimen is then measured.

[0089] (2) Hardness: The hardness of the metal ceramic sample was tested using a Rockwell hardness tester with a load of 60 kg and a loading time of 5 s.

[0090] (3) Magnetic properties: The MH curve of the metal ceramic sample was tested at room temperature (300K) in an external magnetic field range of -20kOe to 20kOe using a comprehensive physical property testing system (PPMS).

[0091] 2. Test Results

[0092] (1) The test results of strength and flexural strength of the samples provided in Examples 1-7 and Comparative Examples 1-2 are shown in Table 1.

[0093] Table 1. Strength and flexural strength test results of the samples provided in Examples 1-7 and Comparative Example 1

[0094]

[0095]

[0096] (2) Magnetic test results are as follows Figure 1 and Figure 2 As shown.

[0097] like Figure 1As shown, the cermet samples prepared using this method exhibit uniform microstructure. Ball milling ensures uniform dispersion of the high-entropy alloy powder and ceramic phase powder, and vacuum sintering technology further homogenizes the microstructure of the sintered cermet body. Under vacuum conditions, the material surface is subjected to high-energy thermal radiation and electron bombardment, causing a change in the growth direction of the internal grains, thus forming a more uniform microstructure.

[0098] like Figure 2 As shown, the cermet prepared by this invention is non-magnetic at room temperature and has low magnetic susceptibility. By using a FeCoCrNiMo high-entropy alloy as a binder phase and Cr3C2 as an additive, the magnetism of the cermet is weakened by the solid solution of antiferromagnetic Cr and paramagnetic elements such as Ti and W in the binder phase.

[0099] The specific embodiments described above further illustrate the purpose, technical solution, and beneficial effects of the present invention. It should be understood that the above description is only a specific embodiment of the present invention and is not intended to limit the scope of protection of the present invention. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. A non-magnetic high-entropy alloy-bonded metal-ceramic, characterized in that, The raw material composition is as follows: (Ti,W)C ceramic phase 58~70 wt.%, alloy binder 15~32 wt.%, Cr3C 22~5 wt.%, and Mo 5~10 wt.%; The alloy adhesive is at least one of FeCoCrNiMo, FeCoCrNi and CrFeNiMo; Its preparation process includes the following steps: The raw materials were wet-milled to obtain a slurry, which was then dried, shaped, and sintered to prepare a non-magnetic high-entropy alloy-bonded metal ceramic. The sintering process involved a sintering temperature of 1420 ℃~1450 ℃, a sintering time of 60 min~80 min, and a furnace vacuum maintained at 10... -2 Pa~10 -1 Pa.

2. The non-magnetic high-entropy alloy-bonded metal ceramic according to claim 1, characterized in that, Wet milling: Anhydrous ethanol was used as the process control agent; the wet abrasive ball ratio was 6:1 to 8:1, the rotation speed was 200 rpm to 220 rpm, and the wet milling time was 36 h to 60 h.

3. The non-magnetic high-entropy alloy-bonded metal ceramic according to claim 2, characterized in that, Drying process: The drying temperature is 79 ℃~90 ℃, and the drying time is 8 h~15 h.

4. A non-magnetic high-entropy alloy-bonded metal ceramic according to any one of claims 2 to 3, characterized in that, The alloy binder in the raw material is obtained by the following preparation method, which includes the following steps: The desired metal element powders of Fe, Cr, and Ni, as well as at least one of Mo and Co, are mixed in an equimolar ratio, wet-milled under an inert atmosphere, and then dried under vacuum to obtain the final product.

5. The non-magnetic high-entropy alloy-bonded metal ceramic according to claim 4, characterized in that, Wet milling process in the preparation of alloy binder: 0.5%~4% anhydrous ethanol is used as process control agent; ball-to-material ratio is 15:1, rotation speed is 300r / min~350r / min, and wet milling time is 40h~60h.

6. The non-magnetic high-entropy alloy-bonded metal ceramic according to claim 5, characterized in that, The vacuum drying temperature is 79 ℃~90 ℃, and the drying time is 8 h~15 h.

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