CN110408811B - Method for strengthening CuW alloy by in-situ autogenous tungsten boride - Google Patents
Method for strengthening CuW alloy by in-situ autogenous tungsten boride Download PDFInfo
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- CN110408811B CN110408811B CN201910651094.1A CN201910651094A CN110408811B CN 110408811 B CN110408811 B CN 110408811B CN 201910651094 A CN201910651094 A CN 201910651094A CN 110408811 B CN110408811 B CN 110408811B
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Abstract
The invention discloses a method for strengthening CuW alloy by in-situ autogenous tungsten boride, which comprises the following steps of mixing W powder and B powderUniformly mixing the powder and the induced copper powder, and pressing and forming to obtain a tungsten pressed blank; putting the tungsten pressed compact into an atmosphere sintering furnace for sintering to obtain a tungsten framework; and (3) placing the pure copper block above the tungsten framework into a graphite crucible paved with graphite paper, and carrying out infiltration in a sintering furnace to obtain the in-situ self-generated tungsten boride reinforced CuW alloy. The invention relates to a method for in-situ generation of tungsten boride reinforced CuW alloy, which adopts a sintering-infiltration method to generate a ceramic phase W in situ in a CuW material2And B, because the existence of the low work function ceramic phase enables electric arcs to be effectively dispersed, the electric arc ablation resistance of the CuW contact material is improved, and meanwhile, the CuW material is strengthened by adopting in-situ generated tungsten boride, so that the particle surface pollution of a reinforcing phase is avoided.
Description
Technical Field
The invention belongs to the technical field of electrical materials, and particularly relates to a method for strengthening CuW alloy by in-situ self-generated tungsten boride.
Background
The CuW material combines high melting point of tungsten, high hardness, high ablation resistance and fusion welding resistance, low thermal expansion coefficient, and high electrical conductivity, high thermal conductivity, and good plasticity of copper, and thus is widely used as an electrical contact in various high-voltage switches. With the implementation and construction of extra-high voltage power grids, CuW electrical contact materials are required to have higher current breaking capacity, higher voltage resistance and ultra-long service life. The contacts will be subject to erosion by the high voltage arc during the opening process. Especially when the high-voltage. Eventually leading to failure of the CuW electrical contact material to successfully open the circuit. Therefore, with the development of high-voltage switches, further improvement in arc ablation resistance is required.
The research shows that the strength of the tungsten matrix in the CuW alloy is obviously reduced along with the temperature rise, and the strength at 1000 ℃ is only 20-40% of the strength at room temperature. Therefore, in order to improve the high-temperature strength of the tungsten matrix, a small amount of second-phase particles are generally added into the tungsten matrix for dispersion strengthening to improve the high-temperature strength of the tungsten matrix, but the addition of the second-phase particles often produces particle surface pollution, and the method is complicated and has high cost.
Disclosure of Invention
The invention aims to provide a method for strengthening a CuW alloy by in-situ autogenous tungsten boride, which is used for improving the arc ablation resistance of the CuW material, and solves the problem of particle surface pollution caused by an external reinforcing phase through in-situ reaction.
The technical scheme adopted by the invention is that the method for strengthening the CuW alloy by in-situ self-generated tungsten boride is implemented according to the following steps:
uniformly mixing the W powder, the B powder and the induced copper powder, and performing compression molding to obtain a tungsten green compact;
step 2, sintering:
putting the tungsten pressed compact obtained in the step 1 into an atmosphere sintering furnace for sintering to obtain a tungsten framework;
and step 3, infiltration:
and (3) putting the clean pure copper block above the tungsten framework into a graphite crucible paved with graphite paper, and carrying out infiltration in a sintering furnace to obtain the in-situ synthesized tungsten boride reinforced CuW alloy.
The invention is also characterized in that:
in the step 1, the addition amount of the B powder is 0-1.0% of the mass of the W powder, and the addition amount of the induced copper powder is 5-10% of the mass of the W powder.
In the step 1, the particle size of the W powder is 1-50 mu m, the particle size of the B powder is 0.2-50 mu m, and the particle size of the induced copper powder is 5-100 mu m.
In the step 1, the pressing pressure is 150-500 MPa, and the pressure maintaining time is 30-90 s.
In the sintering process in the step 2, the sintering temperature is 800-1200 ℃, and the heat preservation time is 1-3 h.
And (2) introducing hydrogen into the atmosphere sintering furnace in the step 2.
In the sintering process of the step 2, the temperature is increased to 600-1000 ℃ at the temperature increasing speed of 5-20 ℃/min, the temperature is maintained for 0.5-2 h, the temperature is increased to 800-1200 ℃ at the speed of 10-30 ℃/min, and the temperature is maintained for 1-3 h.
And 3, in the infiltration process, the infiltration temperature is 1200-1400 ℃, and the heat preservation time is 1-3 h.
And 3, in the infiltration process, heating to 800-1200 ℃ at a heating rate of 5-20 ℃/min, preserving heat for 1-3 h, then heating to 1200-1400 ℃, and preserving heat for 1-3 h.
The invention has the beneficial effects that: according to the method for strengthening the CuW alloy by in-situ self-generated tungsten boride, the in-situ generated tungsten boride is adopted to strengthen the CuW material, so that the surface pollution of reinforced phase particles is avoided, the preparation process is more convenient, and the process of adding and mixing is reduced, so that the time and the cost are saved.
Drawings
FIG. 1 is a process flow diagram of a method for strengthening CuW alloy by in-situ autogenetic tungsten boride according to the invention;
FIG. 2 is a graph of hardness and conductivity test results for CuW alloys with different B additions;
FIG. 3 is an XRD analysis of a sample prepared according to the present invention;
FIG. 4 is for different W2SEM ablation edge morphology of CuW alloy with B content after 50 times of electrical breakdown, wherein a is CuW alloy, and B is W generated in situ with 0.6% B content2CuW alloy of B.
Detailed Description
The present invention will be described in detail below with reference to the accompanying drawings and specific embodiments.
The invention discloses a method for strengthening CuW alloy by in-situ autogenous tungsten boride, which has a flow shown in figure 1 and is specifically implemented according to the following steps:
putting W powder with the particle size of 1-50 mu m, B powder with the particle size of 0.2-50 mu m and induced copper powder with the particle size of 5-100 mu m into a V-shaped mixer, mixing for 4-8 hours at the speed of 50 r-80 r/min, and uniformly mixing.
Wherein the addition amount of the B powder is 0-1.0% of the weight of the W powder, the purity is more than 99.9%, and the addition amount of the induced copper powder is 5-10% of the weight of the W powder;
step 2, compression molding:
filling the powder mixed in the step 1 into a rigid mold, and performing compression molding by using a hydraulic press, wherein the compression pressure is 150-500 MPa, and the pressure maintaining time is 30-90 s, so as to obtain a tungsten green compact;
and 3, sintering:
putting the tungsten pressed blank pressed in the step 2 into an atmosphere sintering furnace, introducing hydrogen for 40min, then checking the purity of the hydrogen, igniting the hydrogen after safety is confirmed, opening cooling water, then starting heating, heating to 600-1000 ℃ at a heating speed of 5-20 ℃/min, preserving heat for 0.5-2 h, heating to 800-1200 ℃ at a heating speed of 10-30 ℃/min, preserving heat for 1-3 h, and cooling to room temperature along with the furnace to obtain a tungsten framework;
and 4, infiltration:
polishing and drying a pure copper block, putting the polished pure copper block above a tungsten framework into a graphite crucible paved with graphite paper in advance, putting the graphite crucible into a sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting a power supply to heat, heating to 800-1200 ℃ at the heating rate of 5-20 ℃/min, preserving heat for 1-3 h, then heating to 1200-1400 ℃, preserving heat for 1-2 h, and finally cooling to room temperature at the cooling rate of 5-30 ℃/min to obtain the in-situ generated W2CuW alloy of B.
The invention adopts a sintering infiltration method to prepare the in-situ authigenic W2The CuW material of B avoids the surface pollution of reinforced phase particles, reduces the process of adding and mixing, thereby saving time and cost due to the W with low work function2B, effectively dispersing electric arcs, thereby improving the electric arc ablation resistance of the CuW contact material, and meanwhile, the CuW contact material also has higher hardness.
Example 1
W powder and B powder (average particle size: 0.2 μm) were weighed out to give an average particle size of 1 μm. And the addition amount of the B powder is 0.2 percent of the mass of the W powder, and the inducing copper powder (the average particle size is 5 mu m) accounts for 5 percent of the mass of the W powder, mixing the materials for 4 hours on a V-shaped mixer at the speed of 80r/min, and pressing and molding the mixed materials by adopting a hydraulic press to obtain a W green compact. The pressing pressure is 350MPa, and the dwell time is 50 s. Placing W pressed compact in graphite crucible, placing the crucible in an atmosphere sintering furnace, introducing hydrogen for 40min, checking hydrogen purity, and determining safetyIgniting hydrogen, starting heating after opening cooling water, raising the temperature at the temperature rising speed of 8 ℃/min, keeping the temperature for 1.5h when the sintering temperature is 600 ℃, then raising the temperature to 1000 ℃ at the speed of 10 ℃/min, and keeping the temperature for 1 h. And naturally cooling to room temperature along with the furnace to obtain the W framework. Stacking the cleaned surface pure copper blocks above the W framework, then placing the crucible into an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, raising the temperature at the temperature raising speed of 5 ℃/min, keeping the temperature for 3h when the infiltration temperature is 900 ℃, then heating to 1200 ℃, keeping the temperature for 3h, and finally cooling to the room temperature at the temperature lowering speed of 5 ℃/min to obtain the W-containing copper2A CuW alloy of phase B.
Example 2
W powder and B powder (average particle size: 25 μm) having an average particle size of 15 μm were weighed. And the addition amount of the B powder is 0.4 percent of the mass of the W powder, and the induction copper powder (the average particle size is 60 mu m) accounts for 8 percent of the mass of the W powder, and the materials are mixed for 8 hours on a V-shaped mixer at 50r/min, and then are pressed and formed by a hydraulic press to obtain a W green compact. The pressing pressure is 400MPa, and the dwell time is 50 s. Placing the W pressed compact in a graphite crucible, then placing the crucible in an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, opening cooling water, starting heating, heating at the heating rate of 20 ℃/min, keeping the temperature for 1h when the sintering temperature is 800 ℃, then heating to 950 ℃ at the heating rate of 15 ℃/min, keeping the temperature for 2h, and naturally cooling to the room temperature along with the furnace to obtain the W framework. Stacking the cleaned pure copper blocks on the W framework, putting the crucible into an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, raising the temperature at the temperature raising speed of 10 ℃/min, preserving the temperature for 1.5h when the infiltration temperature is 950 ℃, then heating to 1250 ℃, preserving the temperature for 2h, and finally reducing the temperature to room temperature at the temperature lowering speed of 20 ℃/min to obtain the in-situ self-generated W2CuW alloy of B.
Example 3
W powder and B powder (average particle size: 30 μm) having an average particle size of 15 μm were weighed. The addition amount of the B powder is 0.6 percent of the mass of the W powder, and the induction of the W powder is 7 percentCopper powder (with the average particle size of 30 mu m) is mixed for 6 hours on a V-shaped mixer at 60r/min, and the mixture is pressed and formed by a hydraulic press to obtain a W pressed compact. The pressing pressure is 150MPa, and the dwell time is 90 s. Placing the W pressed compact in a graphite crucible, then placing the crucible in an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, heating at the heating rate of 10 ℃/min, preserving heat for 1.5h when the sintering temperature is 1000 ℃, then heating to 1200 ℃ at the heating rate of 20 ℃/min, preserving heat for 1h, and naturally cooling to room temperature along with the furnace to obtain the W framework. Stacking the cleaned pure copper blocks on the upper part of the W framework, then placing the crucible into an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, raising the temperature at a temperature raising speed of 15 ℃/min, keeping the temperature for 2h when the infiltration temperature is 1200 ℃, heating to 1400 ℃, keeping the temperature for 1h, and finally reducing the temperature to room temperature at a temperature lowering speed of 30 ℃/min to obtain the in-situ self-generated W2CuW alloy of B.
Example 4
W powder and B powder (average particle size: 30 μm) having an average particle size of 20 μm were weighed. And the addition amount of the B powder is 0.8 percent of the mass of the W powder, and the weight of the W powder is 9 percent of the induced copper powder (the average particle size is 40 mu m), the materials are mixed for 7 hours on a V-shaped mixer at 55r/min, and the mixture is pressed and formed by a hydraulic press to obtain a W green compact. The pressing pressure is 500MPa, and the dwell time is 30 s. Placing the W pressed compact in a graphite crucible, then placing the crucible in an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, opening cooling water, starting heating, heating at the heating rate of 18 ℃/min, preserving heat for 1.5h when the sintering temperature is 850 ℃, then heating to 1000 ℃ at the heating rate of 30 ℃/min, preserving heat for 3h, and naturally cooling to room temperature along with the furnace to obtain the W framework. Stacking the cleaned pure copper blocks above the W framework, putting the crucible into an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, raising the temperature at the temperature raising speed of 18 ℃/min, keeping the temperature for 2h when the infiltration temperature is 800 ℃, and heating to 1350 DEG CKeeping the temperature for 1.5 hours, and finally cooling to room temperature at a cooling rate of 15 ℃/min to obtain the in-situ authigenic W2CuW alloy of B.
Example 5
W powder and B powder (average particle size 50 μm) were weighed out to an average particle size of 50 μm. And the addition amount of the B powder is 1.0 percent of the mass of the W powder, and the inducing copper powder (the average particle size is 100 mu m) accounts for 10 percent of the mass of the W powder, the materials are mixed for 6 hours on a V-shaped mixer at 70r/min, and the mixture is pressed and formed by a hydraulic press to obtain a W green compact. The pressing pressure is 350MPa, and the dwell time is 30 s. Placing the W pressed compact in a graphite crucible, then placing the crucible in an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, raising the temperature at the temperature raising speed of 20 ℃/min, preserving the temperature for 2h when the sintering temperature is 700 ℃, then raising the temperature to 1200 ℃ at the speed of 20 ℃/min, preserving the temperature for 2h, and naturally cooling to the room temperature along with the furnace to obtain the W framework. Stacking the cleaned pure copper blocks above the W framework, putting the crucible into an atmosphere sintering furnace, introducing hydrogen for 40min, checking the purity of the hydrogen, igniting the hydrogen after confirming safety, starting heating after opening cooling water, raising the temperature at the temperature raising speed of 20 ℃/min, preserving the temperature for 1.5h when the infiltration temperature is 1000 ℃, then heating to 1200 ℃, preserving the temperature for 2h, and finally reducing the temperature to room temperature at the temperature lowering speed of 15 ℃/min to obtain the in-situ self-generated W2CuW alloy of B.
The in situ authigenic W prepared in the above examples2The CuW alloy of B is subjected to a vacuum electric breakdown experiment in a modified TDR-40A single crystal furnace. Tests prove that all samples of the embodiment added with the B element realize effective dispersion of electric arcs, and the electric arc ablation resistance of the material is improved.
Figure 2 is a graph of hardness and conductivity test results for materials with different B additions. It can be seen that a CuW alloy having a certain hardness and conductivity can be obtained by infiltrating a W skeleton containing B element with a pure copper block, but an excessive amount of W2B generation affects material conductivity.
FIG. 3 is an XRD analysis of samples prepared according to the present invention, and it can be seen that the CuW alloy is obtained by sintering infiltration after adding B elementIn situ generate W2And (B) phase.
FIG. 4 is an SEM ablation profile after 50 electrical breakdowns for the CuW alloy and the 0.6% B content in-situ grown CuW alloy. The ablation of the anode tungsten needle directly facing the CuW alloy (shown in figure B) added with 0.6 percent of B is slight, the ablation surface is generally flat, the distribution area of ablation pits is large, and the electric arc has a tendency of moving randomly around, because of the W2B, the arc is dispersed to some extent.
Claims (6)
1. A method for strengthening CuW alloy by in-situ autogenous tungsten boride is characterized by comprising the following steps:
step 1, mixing powder and compacting:
uniformly mixing the W powder, the B powder and the induced copper powder, and performing compression molding to obtain a tungsten green compact;
step 2, sintering:
putting the tungsten pressed compact obtained in the step 1 into an atmosphere sintering furnace for sintering to obtain a tungsten framework;
and step 3, infiltration:
putting a clean pure copper block above a tungsten framework, putting the pure copper block into a graphite crucible paved with graphite paper, and carrying out infiltration in a sintering furnace to obtain an in-situ self-generated tungsten boride reinforced CuW alloy;
in the step 1, the addition amount of the B powder is 0.6-1.0% of the weight of the W powder, and the addition amount of the induced copper powder is 8-10% of the weight of the W powder;
in the step 1, the particle size of the W powder is 1-50 mu m, the particle size of the B powder is 0.2-50 mu m, and the particle size of the induced copper powder is 5-100 mu m;
in the step 1, the pressing pressure is 150-500 MPa, and the pressure maintaining time is 30-90 s.
2. The method for strengthening CuW alloy by in-situ autogenous tungsten boride according to claim 1, wherein in the sintering process in the step 2, the sintering temperature is 800-1200 ℃, and the heat preservation time is 1-3 h.
3. The method for strengthening CuW alloy by in-situ autobiogenic tungsten boride according to claim 1, wherein hydrogen is introduced into the atmosphere sintering furnace in the step 2.
4. The method for strengthening CuW alloy by in-situ self-generated tungsten boride according to claim 1, wherein in the sintering process of the step 2, the temperature is raised to 600-1000 ℃ at a temperature raising speed of 5-20 ℃/min, the temperature is maintained for 0.5-2 h, then the temperature is raised to 800-1200 ℃ at a speed of 10-30 ℃/min, and the temperature is maintained for 1-3 h.
5. The method for strengthening CuW alloy by in-situ autogenetic tungsten boride according to claim 1, wherein in the infiltration process of step 3, the infiltration temperature is 1200-1400 ℃, and the holding time is 1-3 h.
6. The method for strengthening CuW alloy by in-situ autogenetic tungsten boride according to claim 1, wherein in the infiltration process of the step 3, the temperature is raised to 800-1200 ℃ at a temperature rise speed of 5-20 ℃/min, the temperature is maintained for 1-3 h, then the temperature is raised to 1200-1400 ℃, and the temperature is maintained for 1-3 h.
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| CN111451492B (en) * | 2020-03-23 | 2021-09-07 | 陕西斯瑞新材料股份有限公司 | Method for preparing CuW90 material by using spherical tungsten powder |
| CN111961901B (en) * | 2020-08-12 | 2021-12-17 | 西安理工大学 | Preparation method of in-situ authigenic WC reinforced WCu dual-gradient-structure composite material |
| CN112086307B (en) * | 2020-08-12 | 2022-11-18 | 西安理工大学 | Preparation method of in-situ synthesized WC reinforced WCu moving arc contact surface layer |
| CN113151706A (en) * | 2021-03-17 | 2021-07-23 | 西安理工大学 | Low friction coefficient WB2Preparation method of/CuSn 10 composite material |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1167992A (en) * | 1997-05-05 | 1997-12-17 | 冶金工业部钢铁研究总院 | Vacuum load switch contact material and its mfg. method |
| US20140271318A1 (en) * | 2013-03-15 | 2014-09-18 | Kennametal Inc. | Methods of making metal matrix composite and alloy articles |
| CN105220004A (en) * | 2015-09-29 | 2016-01-06 | 河南科技大学 | A kind of copper base electric contact composite material and preparation method thereof |
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| CN102747239B (en) * | 2012-07-06 | 2014-04-16 | 中国西电电气股份有限公司 | Manufacturing method for copper-tungsten alloy of a tungsten framework |
| CN109207764B (en) * | 2018-09-26 | 2020-10-27 | 西安理工大学 | Method for strengthening CuW alloy by in-situ autogenous titanium diboride |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1167992A (en) * | 1997-05-05 | 1997-12-17 | 冶金工业部钢铁研究总院 | Vacuum load switch contact material and its mfg. method |
| US20140271318A1 (en) * | 2013-03-15 | 2014-09-18 | Kennametal Inc. | Methods of making metal matrix composite and alloy articles |
| CN105220004A (en) * | 2015-09-29 | 2016-01-06 | 河南科技大学 | A kind of copper base electric contact composite material and preparation method thereof |
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