CN104372196A - In situ reaction method for generating TiC dispersion strengthened Cu alloy - Google Patents
In situ reaction method for generating TiC dispersion strengthened Cu alloy Download PDFInfo
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Abstract
The invention relates to an in situ reaction method for generating TiC dispersion strengthened Cu alloy. The method is as below: (1) weighing copper powder, titanium powder and carbon powder according to a certain proportion, mixing evenly and pressing the mixture into a precast block by using a tablet machine; (2) placing the electrolytic copper and the precast block obtained in the step (1) into a vacuum induction melting furnace, vacuumizing and heating to melt the electrolytic copper; when temperature reaches 1350-1450 DEG C, adding the precast block into the melt, insulating, conducting cooling casting and naturally cooling to obtain the TiC dispersion strengthened copper alloy with average particle diameter of 0.5-1 mum and content of 1-2 wt%. The test shows that the 1% TiC as cast condition has microhardness of 92.8HV and conductivity of 76.5%IACS. The method provided by the invention has simple preparation process, TiC particles generated in situ are in micro-agglomeration uniform distribution, have fine particles, and good combination property with the matrix; titanium and carbon react completely without generating impurity phase; and the material has good performance.
Description
Technical field
The present invention relates to a kind of method that reaction in－situ generates TiC dispersion-strengthened Cu alloy, belong to non-ferrous alloy processing technique field.
Background technology
Copper alloy is the structure function material that a class has excellent combination physicals and mechanical property, is widely used as electric railway osculatory material.Osculatory also claims contact line, as the important medium in electric railway pantograph contact line relation, its effect is exactly can obtain electric energy continuously from tractive power supply system when guaranteeing train high-speed cruising, it needs to withstand shocks in normal work, shake, high temperature, severe cold, burn into friction and tension force greatly, therefore its over-all properties (intensity, electroconductibility, solidity to corrosion, wear resistance etc.) directly affect locomotive be subject to flow stability and security.Along with the high speed development of electric railway, the travelling speed of train is more and more faster, therefore also more and more higher to the performance requriements of electric railway osculatory material.Copper alloy contact wire rod conventional at present has: copper silver, copper tin, copper magnesium and copper chromium zirconium.Copper silver, copper tin and copper magnesium belong to solution strengthening type copper alloy, and this kind of alloy strength is high, but the scattering process of solid solution atom pairs electronics is strong, and therefore the electroconductibility of alloy is lower.Copper chromium zirconium belongs to precipitation strength type copper alloy, and this kind of alloy can take into account high strength and high conductivity, but needs the heat treatment such as solid solution and timeliness, and this exacerbates the complicacy of technique undoubtedly, improves production cost, therefore constrains its application greatly.Conductivity theory is pointed out, weak many of the scattering process of lattice distortion to electronics that the scattering process of the second opposing electronic causes than solid solution atom, therefore second-phase obviously can not reduce the electroconductibility of Copper substrate, thus reaches the better combination of high strength and high conductivity.So, how can avoid the heat treatment such as solid solution, timeliness, second-phase can be generated in copper base again, be worth further research.
Adopt in-situ reactive synthesis (compound) method, in Copper substrate, directly can generate Second Phase Particle, without the need to the heat treatment such as solid solution, timeliness, can reinforced effects be reached, more and more come into one's own in recent years.React in position in recombination process, the normal Second Phase Particle introduced has SiC, WC, TiN, TiB
2, Al
2o
3, TiC etc.Wherein TiC particle has fusing point and the characteristic such as hardness is high, wear resistance is good, compare with other enhanced granule, the metallic conductivity caused and thermal conductivity slippage less, thus be expected to obtain the characteristic such as high strength, high rigidity, high conductivity and high softening temperature, TiC dispersion-strengthened Cu alloy will one of the focus becoming future studies.Reaction in－situ matrix material method mainly comprises: mechanical alloying method, self-propagating high-temperature synthesis, hot pressing sintering method, internal oxidation and contact reaction method.Contact reaction method and smelting process, compared to front four kinds of methods, the method technique is simple, and cost is lower, is easy to large-scale production.Generate TiC particle comparative maturity by hot pressing sintering method, self-propagating high-temperature synthesis and machine-alloying at Copper substrate situ, but utilize smelting process, the research of titanium valve and carbon dust direct in-situ reaction preparation TiC dispersion-strengthened Cu alloy be have not been reported.
Summary of the invention
Technical problem to be solved by this invention is: existing original position prepares the shortcomings such as Cu-base composites apparatus expensive, complicated operation, cost of material be higher, turn avoid the heat treatment such as the solid solution needed for precipitation strength, timeliness.There is provided a kind of reaction in－situ to generate the method for TiC dispersion-strengthened Cu alloy, adopt vacuum melting technology, utilize the heat of copper melts, make the titanium valve in prefabricated section and carbon dust direct in-situ generate superfine Ti C enhanced granule phase, prepare TiC dispersion-strengthened Cu alloy with this.
Technical scheme:
Reaction in－situ generates a method for TiC dispersion-strengthened Cu alloy, comprises the steps:
1st step, get copper powder, titanium valve and carbon dust, carry out ball milling with ball mill, then be pressed into prefabricated section;
2nd step, the prefabricated section of copper and the 1st step gained is put into vacuum induction melting furnace, vacuumize, heat fused copper; Again prefabricated section is put in copper melts, insulation, then casting after cooling, cooling, obtains TiC dispersion-strengthened Cu alloy.
In the 1st described step, the weight of copper powder: the weight sum of titanium valve and carbon dust is (1.1 ~ 1.3): 1; Titanium valve: the mol ratio of carbon dust is (1.8 ~ 2.2): 1.
In the 1st described step, copper powder particle size < 45 μm, purity > 99.9%; Titanium valve particle size is 45 ~ 75 μm, purity > 99.9%; Carbon powder particle size < 45 μm, purity > 99.9%.
In the 1st described step, the pressure of compacting is 25 ~ 35MPa.
In the 2nd described step, in heat fused copper, when temperature reaches 1350 ~ 1450 DEG C, prefabricated section is put into melt when among.
In the 2nd described step, soaking time 15 ~ 20min.
In the 2nd described step, pouring temperature is 1250 ~ 1300 DEG C.
Median size 0.5 ~ 1 μm, the content 1 ~ 2wt% of the middle TiC of described TiC dispersion-strengthened Cu alloy.
beneficial effect
(1) adopt smelting technique, direct in-situ generates particulates reinforcements, and without the need to the heat treatment such as solid solution, timeliness, technique is simple, and cost is lower, is easy to large-scale production;
(2) melting technology is passed through, titanium and carbon react completely, the generation of inclusion-free phase, generated in-situ TiC size distribution is comparatively even, particle is tiny and be combined well with matrix, and material property is better, the as cast condition microhardness after tested containing 1%TiC (weight percent) is 92.8HV, and electric conductivity is 76.5%IACS;
The temperature of reaction of (3) 1350 ~ 1450 DEG C ensure that fully carrying out of reaction, and it is too high that the pouring temperature of 1250 ~ 1300 DEG C had both avoided pouring temperature, and TiC particle is reunited in a large number, turn avoid pouring temperature too low, and melt has little time feeding, produces pore;
(4) in prefabricated section, rational grain diameter is selected and proportioning raw materials, both ensure that the abundant reaction of titanium valve and carbon dust, excessive titanium elements can not be made again to produce considerable influence to electroconductibility.
Accompanying drawing explanation
The scanning electron microscope (SEM) photograph of Fig. 1 as cast condition Cu alloy (containing 1wt%TiC), observes multiple lower
The scanning electron microscope (SEM) photograph of Fig. 2 as cast condition Cu alloy (containing 1wt%TiC), observes multiple higher
The XRD figure spectrum of Fig. 3 as cast condition Cu alloy (containing 1wt%TiC)
The metallographic structure figure of Fig. 4 as cast condition Cu alloy (containing 1.8wt%TiC)
Embodiment
Below by embodiment, the present invention is described in further detail.But it will be understood to those of skill in the art that the following example only for illustration of the present invention, and should not be considered as limiting scope of the present invention.Unreceipted concrete technology or condition person in embodiment, according to the technology described by the document in this area or condition or carry out according to product description.Agents useful for same or the unreceipted production firm person of instrument, being can by the conventional products of commercial acquisition.
The numerical value as range limit not only comprising and clearly listing should be interpreted as in a flexible way using the value that range format is expressed, but also comprise and be encompassed in all single numerical value within the scope of this or sub-range, be expressly recited out just as each numerical value and sub-range.Such as, the concentration range of " about 0.1% to about 5% " should be understood to the concentration not only comprising about 0.1% to about 5% clearly listed, also include single concentration in institute's how (as, 1%, 2%, 3% and 4%) and sub-range (such as, 0.1% to 0.5%, 1% to 2.2%, 3.3% to 4.4%).
The present invention mainly adopts first by after copper powder, titanium valve and carbon dust by a certain percentage ball milling, be pressed into prefabricated section again, the generation situation of proportioning to final TiC of the copper powder in prefabricated section, titanium valve and carbon dust is very crucial, the present invention obtains a proportioning raw materials scope, words not within this scope, have two kinds of adverse consequencess, one is very difficult in-situ formation of TiC enhanced granule, and two is that the electroconductibility of TiC dispersion-strengthened Cu alloy of preparation is very low.In a preferred embodiment, copper powder: (titanium valve+carbon dust) weight ratio=1.1 ~ 1.3:1, wherein titanium valve: carbon dust mol ratio=1.8 ~ 2.2:1.In addition, prefabricated section is just through ball milling, it is cold pressure procedure, object makes powder become block exactly, and be unlikely to dispersion, this process does not exist any reaction, the object of only carrying out colding pressing makes powder become block exactly, be unlikely to dispersion, if powder is not drop in melt with the form of block, the powder so disperseed will be ablated off by melt.
Next, then copper is carried out heat fused, the copper adopted here can be electrolytic copper, after fusing, then adds prefabricated section and is incubated, can realize the reaction in－situ of Ti and C, generates TiC.In this step, first make copper melt, then add prefabricated section, its objective is and utilize the temperature of melt directly to make Ti and C reaction in－situ generate TiC particle, relative to heating simultaneously, its advantage is the ablation of the ablation especially titanium elements reducing raw material, ensures the abundant reaction of Ti and C with this.In this step, heating the temperature optimum that copper is melted is reach 1350 ~ 1450 DEG C, be in the reason of this temperature range: the too low generation being unfavorable for TiC of temperature, temperature is too high, can cause higher energy consumption, wherein through lot of experiments optimal selection 1400 DEG C, and this temperature is the direct reaction temperature spot of Ti and C, lower than this temperature, reaction is difficult to carry out).In addition, vacuum melting in this step, and not adopting melting in air, reason is: one is that copper is at high temperature easy to oxidation, if adopt melting in air, understand in the very thick zone of oxidation of Surface Creation one deck of copper melts, such prefabricated section just can not join among melt again, if adopt graphite bell jar in prefabricated section press-in melt, can find that melt temperature can decline immediately in actually operating, and then solidify, be extremely unfavorable for the direct reaction of Ti and C; Two is adopt vacuum melting, can weaken the ablation of titanium valve and avoid being mixed into of impurity, being conducive to electroconductibility.
After generation TiC, need to cast, pouring temperature is preferably 1250 ~ 1300 DEG C, and it is too high that pouring temperature of the present invention had both avoided pouring temperature, and TiC particle is reunited in a large number, turn avoid pouring temperature too low, and melt has little time feeding, produces pore.
embodiment 1
Preparation is containing the dispersion-strengthened Cu alloy of 1wt%TiC.With copper powder (45 μm, 99.9%), titanium valve (75 μm, 99.9%), carbon dust (45 μm, 99.9%) and T2 electrolytic copper be raw material, first by three kinds of powder by copper powder: (titanium valve+carbon dust) weight ratio=1.2:1 (wherein titanium valve: carbon dust mol ratio=2:1) accurately takes, amount to 118.8g, (its medium speed is 120r/min to utilize planetary ball mill that the powder taken is mixed, time is 15h), with tabletting machine, mixed powder is pressed into the prefabricated section of Φ 8mm subsequently, pressure is 30MPa; Then (wherein electrolytic copper is placed in crucible the T2 electrolytic copper of 2.88kg and obtained prefabricated section to be put into vacuum induction furnace above, prefabricated section is placed in hopper), vacuumize post-heating fusing electrolytic copper, when temperature reaches 1400 DEG C, prefabricated section is put into melt when among, cooling casting is carried out after insulation 20min, pouring temperature is 1280 DEG C, naturally cooling, finally obtains the dispersion-strengthened Cu alloy (see Fig. 1,2 and 3) that TiC median size is 0.5 ~ 1 μm, content is about 1wt%.As cast condition microhardness is 92.8HV after tested, and electric conductivity is 76.5%IACS.
embodiment 2
Preparation is containing the dispersion-strengthened Cu alloy of 1.8wt%TiC.With copper powder (45 μm, 99.9%), titanium valve (45 μm, 99.9%), carbon dust (45 μm, 99.9%) and T2 electrolytic copper be raw material, first by three kinds of powder by copper powder: (titanium valve+carbon dust) weight ratio=1.3:1 (wherein titanium valve: carbon dust mol ratio=1.8:1) accurately takes, amount to 203.7g, (its medium speed is 120r/min to utilize planetary ball mill that the powder taken is mixed, time is 15h), with tabletting machine, mixed powder is pressed into the prefabricated section of Φ 8mm subsequently, pressure is 30MPa, then (wherein electrolytic copper is placed in crucible the T2 electrolytic copper of 2.77kg and obtained prefabricated section to be put into vacuum induction furnace above, prefabricated section is placed in hopper), vacuumize post-heating fusing electrolytic copper, when temperature reaches 1450 DEG C, prefabricated section is put into melt when among, cooling casting is carried out after insulation 15min, pouring temperature is 1250 DEG C, naturally cooling, finally obtain TiC median size < 1 μm, content is about the dispersion-strengthened Cu alloy (see figure 4) of 1.8wt%, cast alloy alloy microhardness is 104.6HV after tested, tensile strength is 347.4MPa, electric conductivity is 61.3%IACS.
reference examples 1
This reference examples is for illustration of the impact (melt temperature becomes 1250 DEG C from 1400 DEG C) of melt temperature.To prepare the dispersion-strengthened Cu alloy of theoretical content 1wt%TiC.With copper powder (45 μm, 99.9%), titanium valve (45 μm, 99.9%), carbon dust (75 μm, 99.9%) and T2 electrolytic copper be raw material, first by three kinds of powder by copper powder: (titanium valve+carbon dust) weight ratio=1.2:1 (wherein titanium valve: carbon dust mol ratio=1.5:1) accurately takes, amount to 118.8g, (its medium speed is 120r/min to utilize planetary ball mill that the powder taken is mixed, time is 15h), with tabletting machine, mixed powder is pressed into the prefabricated section of Φ 8mm subsequently, pressure is 30MPa; Then (wherein electrolytic copper is placed in crucible the T2 electrolytic copper of 2.88kg and obtained prefabricated section to be put into vacuum induction furnace above, prefabricated section is placed in hopper), vacuumize post-heating fusing electrolytic copper, when temperature reaches 1250 DEG C, prefabricated section is put into melt when among, cooling casting is carried out after insulation 20min, pouring temperature is 1280 DEG C, naturally cooling, finally obtains the TiC dispersion-strengthened Cu alloy that theoretical content is about 1wt%.As cast condition microhardness is 82.5HV after tested, and electric conductivity is 55.8%IACS.
reference examples 2
This reference examples for illustration of the impact of copper, titanium and carbon ratio example, by titanium valve in technical solution of the present invention: carbon dust mol ratio is that 1.8 ~ 2.2:1 becomes titanium valve: carbon dust mol ratio is 1.5:1.Still to prepare the dispersion-strengthened Cu alloy of theoretical content 1wt%TiC.With copper powder (45 μm, 99.9%), titanium valve (45 μm, 99.9%), carbon dust (45 μm, 99.9%) and T2 electrolytic copper be raw material, first by three kinds of powder by copper powder: (titanium valve+carbon dust) weight ratio=1.2:1 (wherein titanium valve: carbon dust mol ratio=1.5:1) accurately takes, amount to 96.6g, (its medium speed is 120r/min to utilize planetary ball mill that the powder taken is mixed, time is 15h), with tabletting machine, mixed powder is pressed into the prefabricated section of Φ 8mm subsequently, pressure is 30MPa; Then (wherein electrolytic copper is placed in crucible the T2 electrolytic copper of 2.9kg and obtained prefabricated section to be put into vacuum induction furnace above, prefabricated section is placed in hopper), vacuumize post-heating fusing electrolytic copper, when temperature reaches 1400 DEG C, prefabricated section is put into melt when among, cooling casting is carried out after insulation 20min, pouring temperature is 1250 DEG C, naturally cooling, finally obtains the TiC dispersion-strengthened Cu alloy that theoretical content is about 1wt%.As cast condition microhardness is 74.4.HV after tested, and electric conductivity is 59.8.%IACS.
Claims (8)
1. reaction in－situ generates a method for TiC dispersion-strengthened Cu alloy, it is characterized in that, comprises the steps:
1st step, get copper powder, titanium valve and carbon dust, carry out ball milling with ball mill, then be pressed into prefabricated section;
2nd step, the prefabricated section of copper and the 1st step gained is put into vacuum induction melting furnace, vacuumize, heat fused copper; Again prefabricated section is put in copper melts, insulation, then casting after cooling, cooling, obtains TiC dispersion-strengthened Cu alloy.
2. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, it is characterized in that: in the 1st described step, the weight of copper powder: the weight sum of titanium valve and carbon dust is 1.1 ~ 1.3:1; Wherein titanium valve: carbon dust mol ratio is 1.8 ~ 2.2:1.
3. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, it is characterized in that: in the 1st described step, copper powder particle size < 45 μm, purity > 99.9%; Titanium valve particle size is 45 ~ 75 μm, purity > 99.9%; Carbon powder particle size < 45 μm, purity > 99.9%.
4. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, and it is characterized in that: in the 1st described step, the pressure of compacting is 25 ~ 35MPa.
5. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, it is characterized in that: in the 2nd described step, in heat fused copper, when temperature reaches 1350 ~ 1450 DEG C, prefabricated section is put into melt when among.
6. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, it is characterized in that: in the 2nd described step, soaking time 15 ~ 20min.
7. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, it is characterized in that: in the 2nd described step, pouring temperature is 1250 ~ 1300 DEG C.
8. reaction in－situ according to claim 1 generates the method for TiC dispersion-strengthened Cu alloy, it is characterized in that: median size 0.5 ~ 1 μm, the content 1 ~ 2wt% of the middle TiC of described TiC dispersion-strengthened Cu alloy.
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| CN105154711A (en) * | 2015-08-31 | 2015-12-16 | 苏州莱特复合材料有限公司 | Carbon nano tube reinforcement aluminum-bronze-based composite material and preparation method thereof |
| CN105177348A (en) * | 2015-10-30 | 2015-12-23 | 苏州列治埃盟新材料技术转移有限公司 | High-strength titanium carbide copper-based composite material and preparation method thereof |
| CN105177349A (en) * | 2015-10-30 | 2015-12-23 | 苏州列治埃盟新材料技术转移有限公司 | High-strength nano titanium carbide copper-based corrosion-resisting alloy material and preparation method thereof |
| CN105220011A (en) * | 2015-10-30 | 2016-01-06 | 苏州列治埃盟新材料技术转移有限公司 | A kind of high strength carbonizing titanium particle enhanced copper base alloy material and preparation method thereof |
| CN105296794A (en) * | 2015-10-30 | 2016-02-03 | 苏州列治埃盟新材料技术转移有限公司 | Titanium-carbide-enhanced lead-free tin-copper alloy bar and preparation method thereof |
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| CN107119207A (en) * | 2017-05-02 | 2017-09-01 | 江西理工大学 | It is a kind of non-metering than TiC enhancing Cu-base composites and preparation method thereof |
| CN108149059A (en) * | 2018-02-06 | 2018-06-12 | 国网河北能源技术服务有限公司 | A kind of TiC enhances the preparation method of copper-based electric contact composite material |
| CN108165798A (en) * | 2017-12-27 | 2018-06-15 | 洛阳神佳窑业有限公司 | A kind of preparation method of aluminium carbide dispersion strengthening copper alloy |
| CN111961907A (en) * | 2020-08-14 | 2020-11-20 | 江苏吕泰合金有限公司 | Processing method of high-strength, high-toughness and high-conductivity copper alloy wire |
| CN113981263A (en) * | 2021-10-26 | 2022-01-28 | 北京科技大学 | Method for preparing copper-based titanium carbide composite material through in-situ reaction |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1094451A (en) * | 1993-04-28 | 1994-11-02 | 航空航天工业部第六二一研究所 | Directly contact reaction method is produced the method for metal-base composites |
| CN1804077A (en) * | 2005-01-12 | 2006-07-19 | 中国科学院金属研究所 | In-situ produced titanium carbide dispersion strengthening copper based composite material and method for preparing the same |
| JP2009185319A (en) * | 2008-02-05 | 2009-08-20 | Sumitomo Electric Ind Ltd | Dispersion-strengthening copper and producing method thereof |
| CN101709398A (en) * | 2009-11-11 | 2010-05-19 | 昆明理工大学 | Self-propagating high temperature synthesis preparation method of titanium carbide dispersion strengthening copper-based composite material |
-
2014
- 2014-10-09 CN CN201410528841.XA patent/CN104372196B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1094451A (en) * | 1993-04-28 | 1994-11-02 | 航空航天工业部第六二一研究所 | Directly contact reaction method is produced the method for metal-base composites |
| CN1804077A (en) * | 2005-01-12 | 2006-07-19 | 中国科学院金属研究所 | In-situ produced titanium carbide dispersion strengthening copper based composite material and method for preparing the same |
| JP2009185319A (en) * | 2008-02-05 | 2009-08-20 | Sumitomo Electric Ind Ltd | Dispersion-strengthening copper and producing method thereof |
| CN101709398A (en) * | 2009-11-11 | 2010-05-19 | 昆明理工大学 | Self-propagating high temperature synthesis preparation method of titanium carbide dispersion strengthening copper-based composite material |
Cited By (13)
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| CN105154711A (en) * | 2015-08-31 | 2015-12-16 | 苏州莱特复合材料有限公司 | Carbon nano tube reinforcement aluminum-bronze-based composite material and preparation method thereof |
| CN105177348A (en) * | 2015-10-30 | 2015-12-23 | 苏州列治埃盟新材料技术转移有限公司 | High-strength titanium carbide copper-based composite material and preparation method thereof |
| CN105177349A (en) * | 2015-10-30 | 2015-12-23 | 苏州列治埃盟新材料技术转移有限公司 | High-strength nano titanium carbide copper-based corrosion-resisting alloy material and preparation method thereof |
| CN105220011A (en) * | 2015-10-30 | 2016-01-06 | 苏州列治埃盟新材料技术转移有限公司 | A kind of high strength carbonizing titanium particle enhanced copper base alloy material and preparation method thereof |
| CN105296794A (en) * | 2015-10-30 | 2016-02-03 | 苏州列治埃盟新材料技术转移有限公司 | Titanium-carbide-enhanced lead-free tin-copper alloy bar and preparation method thereof |
| CN105441712B (en) * | 2015-11-02 | 2017-06-16 | 苏州金仓合金新材料有限公司 | A kind of Nuclear steam pipeline titanium diboride particle enhanced copper-based composite alloy new material of high intensity |
| CN105441712A (en) * | 2015-11-02 | 2016-03-30 | 苏州金仓合金新材料有限公司 | Novel high-strength titanium diboride particle-reinforced copper-based composite alloy material for nuclear energy steam pipeline |
| CN107119207A (en) * | 2017-05-02 | 2017-09-01 | 江西理工大学 | It is a kind of non-metering than TiC enhancing Cu-base composites and preparation method thereof |
| CN107119207B (en) * | 2017-05-02 | 2019-02-22 | 江西理工大学 | It is a kind of non-metering than TiC enhancing Cu-base composites and preparation method thereof |
| CN108165798A (en) * | 2017-12-27 | 2018-06-15 | 洛阳神佳窑业有限公司 | A kind of preparation method of aluminium carbide dispersion strengthening copper alloy |
| CN108149059A (en) * | 2018-02-06 | 2018-06-12 | 国网河北能源技术服务有限公司 | A kind of TiC enhances the preparation method of copper-based electric contact composite material |
| CN111961907A (en) * | 2020-08-14 | 2020-11-20 | 江苏吕泰合金有限公司 | Processing method of high-strength, high-toughness and high-conductivity copper alloy wire |
| CN113981263A (en) * | 2021-10-26 | 2022-01-28 | 北京科技大学 | Method for preparing copper-based titanium carbide composite material through in-situ reaction |
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