CN106906378B - A kind of high-speed railway copper alloy for contact line and preparation method thereof - Google Patents
A kind of high-speed railway copper alloy for contact line and preparation method thereof Download PDFInfo
- Publication number
- CN106906378B CN106906378B CN201710218266.7A CN201710218266A CN106906378B CN 106906378 B CN106906378 B CN 106906378B CN 201710218266 A CN201710218266 A CN 201710218266A CN 106906378 B CN106906378 B CN 106906378B
- Authority
- CN
- China
- Prior art keywords
- copper alloy
- copper
- speed railway
- contact line
- alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/06—Alloys based on copper with nickel or cobalt as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/14—Plants for continuous casting
- B22D11/143—Plants for continuous casting for horizontal casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/18—Controlling or regulating processes or operations for pouring
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Conductive Materials (AREA)
Abstract
The invention discloses a kind of copper alloy of high-speed railway contact line, the copper alloy contains Co, Ti or Ta and Cu, and it is that 0.61% ~ 1.24% or Ti is 0.16% ~ 0.33%, be surplus is copper that wherein Co weight percent, which is 0.6% ~ 1.2%, Ta,；And Ta or Ti form Co3Ta Co3Ti compound in conjunction with Co；There are cube-on-cube orientation relationships for the compound and Cu matrix, and the phase interface of the two is full coherent interphase face.The present invention also provides the preparation methods of the copper alloy, carry out melt-casting by horizontal casting system and form casting rod, then progress hot extrusion, annealing, the copper alloy is made.Copper alloy produced by the present invention has the characteristics that high-strength highly-conductive, and intensity can reach 520 MPa or more, and the high-speed railway that may be used as speed per hour at 400 kilometers or more contacts wire material.
Description
Technical field
The present invention relates to a kind of Cu alloy and preparation method thereof, especially one kind can be used as high-speed railway especially speed per hour
The copper alloy and preparation method thereof of 400 kilometers or more high-speed railway contact wire materials.
Background technique
Substantive rapid development, Beijing-Tianjin are obtained from 2009 China Nian Qi high-speed electric railway (hereinafter referred to as high-speed rail)
Line, Jing-Hu Railway and Beijing-Guangzhou Railway are in succession open-minded, and high-speed rail stable operation speed is 300 kilometers/hour.The development of high-speed electric railway
To its critical component-huge market demand of contact line-generation and harsh performance requirement.It is required that being used as the material of contact line
It is provided simultaneously with following characteristic: high-intensitive, low line density, good electric conductivity, good abrasion resistance, good corrosion resistance
Deng especially intensity and conductivity are most crucial indexs.
The conductor material that high-speed rail contact line uses at present mainly has Cu-Mg, Cu-Sn, Cu-Ag, Cu-Sn-Ag, Cu-
The series Cu alloy such as Ag-Zr, Cu-Cr-Zr, wherein Cu-Cr-Zr shows more excellent intensity and conductivity comprehensive performance.
Patent CN200410060463.3 and CN200510124589.7 disclose Cu- (0.02 ~ 0.4) %Zr- (0.04 ~ 0.16) %Ag and
The technology of preparing of Cu- (0.2 ~ 0.72) %Cr- (0.07 ~ 0.15) two kinds of alloys of %Ag.By melting, casting, thermal deformation, solid solution,
Cold deformation, timeliness and the techniques such as cold deformation prepare finished product again.Patent CN03135758.X disclose using rapid solidification flour,
Green compact, sintering squeeze acquisition Cu- (0.01 ~ 2.5) %Cr- (0.01 ~ 2.0) %Zr- (0.01 ~ 2.0) % (Y, La, Sm) alloy bar
The preparation method of material or sheet material can obtain good conductive, thermally conductive, high-temperature temperature and softening resistant performance.Patent
CN200610017523.2 disclose Cu- (0.05 ~ 0.40) %Cr- (0.05 ~ 0.2) %Zr- < 0.20% (Ce+Y) alloying component and
Its technology of preparing, by melting, forging, solid solution, deformation, timeliness obtain high-strength highly-conductive comprehensive performance and preferable heat resistance and
Wearability.Patent CN02148648.4 discloses Cu- (0.01 ~ 1.0) %Cr- (0.01 ~ 0.6) %Zr- (0.05 ~ 1.0) %Zn-
(0.01 ~ 0.30) % (La+Ce) alloying component and technology of preparing, pass through the processes such as melting, hot rolling, solid solution, cold rolling, timeliness, finish to gauge
It can get higher intensity and conductivity.
With the sustainable development of high-speed electric railway, national " 13 " planning is clearly proposed when the year two thousand twenty need to be built up
High speed rail system of the speed at 400 kilometers or more.This means that matched contact line material property also must be further
Improve intensity and conductivity, it is necessary to develop novel high-performance alloy to adapt to the lasting speed-raising of high-speed railway development.
Summary of the invention
The purpose of the present invention is quasi- to provide a kind of copper alloy with high strength and high conductivity and preparation method thereof for high-speed railway contact line,
The copper alloy can be used as high-speed railway especially speed per hour and contact wire material in 400 kilometers or more of high-speed railway.
The design for preparing copper alloy with high strength and high conductivity of the invention is as follows: the nanometer of a large amount of Dispersed precipitates is introduced in Cu matrix
Precipitated phase, special emphasis be, there are cube-on-cube orientation relationship (namely precipitated phases for these nanometer precipitated phases and Cu matrix
<110>crystal orientation is parallel with<110>crystal orientation of Cu matrix and { 111 } crystal face of { 111 } crystal face of precipitated phase and Cu matrix is flat
Row), and the phase interface of these nanometer precipitated phases and Cu matrix is full coherent interphase face, and misfit dislocation is not present.These disperses point
The nanometer precipitated phase of cloth can effectively improve the dislocation motion resistance of Cu matrix, especially when dislocation cuts through these precipitated phases can be by
Back stress is generated in chemically-ordered effect and pulls dislocation line strongly, so that the intensity for significantly improving alloy realizes high-strength mesh
's；On the other hand, very big, right compared to lattice distortion at non-coherence in routine CuSn, CuCrZr system or half coherent interphase face
Electronics scattering of wave is serious, and the phase interface of nanometer precipitated phase of the invention and Cu matrix is full coherent interphase face, the dot matrix of interface
It distorts very small, it is faint to electron waves scattering process, to ensure quick conduction of the electron waves inside alloy, reaches height and lead
Purpose.It is based on precipitated phase crystal dots why nanometer precipitated phase of the invention can generate full coherent interphase face with Cu matrix
The big data of battle array structure calculates, and by science selection alloying element, reasonably combined element ratio and using scientific preparation process
It realizes.
For achieving the above object, its technical effect is realized, the present invention adopts the following technical scheme:
The present invention provides a kind of copper alloy of high-speed railway contact line, it is 0.6% which, which contains weight percent,
Perhaps 0.16% ~ 0.33% Ti and Co and the atomic ratio of Ta or Co and Ti are the Ta of ~ 1.2% Co and 0.61% ~ 1.24%
3:1, surplus are copper；The copper alloy has that wherein Ta or Ti form Co in conjunction with Co in the form of long stick perhaps line3Ta or
Co3Ti compound；And it is formed by Co3Ta or Co3Ti compound is embedded in Cu matrix, and the Co with form of nanoparticles3Ta
Or Co3The diameter distribution of Ti compound nano-particle is 1 ~ 50 nm, and grain spacing range is 5 ~ 100 nm；The chemical combination
There are cube-on-cube orientation relationships with Cu matrix for object nano particle, and the phase interface of the compound nano-particle and Cu matrix
For full coherent interphase face, misfit dislocation is not present.
The present invention also provides the method for preparing above-mentioned copper alloy, the preparation method included the following steps is made:
(1) it using simple substance and/or intermediate alloy as raw material, feeds intake according to required proportion, in horizontal casting system duplex furnace body
Smelting furnace fusing, be transferred to holding furnace later.Fusion temperature is 1200 ~ 1300oC, heat preservation furnace temperature are 1100 ~ 1200oC,
Smelting furnace and holding furnace surface cover one layer of charcoal；
Wherein the simple substance is Ni metal, Co, Ti or Ta；
The intermediate alloy is Cu-Co or Cu-Ta or Cu-Ti alloy；
It is described proportion for 0.6% ~ 1.2% Co and 0.61% ~ 1.24% Ta or 0.16% ~ 0.33% Ti, and Co with
The atomic ratio of Ta or Co and Ti is 3:1, and surplus is copper；
(2) casting rod is drawn using horizontal casting mode, casting rod diameter is 10 ~ 100 mm, and off speed is 60 ~ 600 mm/
Min, crystallizer is cooling using water-cooling pattern, and cooling length is 10 ~ 500 mm；
(3) casting rod is carried out Continuous Heat extruding and roll as diameter to be 15 ~ 20 mm poles, extrusion temperature for 800 ~
1000 oCAnd pass to inert gas shielding；
(4) by pole in 375 ~ 575 oCAnneal 1 ~ 100 h, obtains the copper alloy.
The present invention is by selecting copper alloy to contain Co, and perhaps the atomic ratio of Ti element and control Co and Ta or Ti are Ta
3:1, making being capable of Co by the process parameter controls Co such as temperature and Ta or Co and Ti formation in subsequent technique engineering3Ta or
Co3Ti.Wherein, Cu, Co3Ta and Co3Ti is centroid cubic crystal system, and the lattice constant of three be respectively 0.3615 nm,
0.3647 nm and 0.3614 nm, difference are no more than 1%, reach the basic condition that can form full coherent interphase face, to pass through shape
At technology controlling and process key process parameter, make alloy formed cube-on-cube to corresponding full coherent interphase face, realize
The technical purpose of invention.
In order to avoid Co3Ta or Co3Ti is precipitated in advance in the hot extrusion stage, and the present invention controls extrusion temperature, preferably exists
800~1000 oC, to ensure Co3Ta or Co3Ti disperse point controllably in the form of nanometer precipitated phase in subsequent ag(e)ing process
Cloth obtains excellent strengthening effect in Cu matrix.And in order to avoid the sample surfaces severe oxidation at a high temperature of hot extrusion stage,
It is protected using inert gas.
Compared with prior art, copper alloy provided by the invention and preparation method thereof has the advantages that
1), the present invention uses horizontal casting mode, can obtain the Copper alloy bar of big anchor segment length；
2), copper alloy produced by the present invention has unique micro-structure and high intensity and high conductivity performance:
3), the present invention forms Co using Co and Ta or Ti3Ta or Co3Ti compound effectively purifies Cu matrix, ensures
The good electric conductivity of Cu matrix；And utilize Co3Ta or Co3Ti compound and Cu matrix form full coherent interphase face, avoid
The big lattice distortion of phase interface in conventional copper alloy ensures that electron waves, by faint scattering, make alloy have high electricity in phase interface
Conductance；
4) pinning effect of dislocation line is imitated with the back stress of its chemically-ordered generation using high density nanometer precipitated phase
Fruit promotes alloy integral strength level, copper alloy intensity is enabled to reach 520 MPa or more, can be applied to speed per hour in 400 public affairs
In above high-speed railway contact wire material.
Detailed description of the invention
Fig. 1 is the Co obtained of embodiment 13The nanometer precipitated phase transmission electron microscope center dark field image of Ta.
Fig. 2 is the Co obtained of embodiment 23The nanometer precipitated phase transmission electron microscope center dark field image of Ti.
Fig. 3 is the Co obtained of embodiment 23The nanometer precipitated phase high-resolution-ration transmission electric-lens image of Ti.
Specific embodiment
With specific embodiment, the present invention is described further below.
Embodiment 1:
(1) using catholyte copper, Co simple substance and Cu-Ta intermediate alloy as raw material, the Co for being 0.6% according to weight percent,
0.61% Ta, remaining feeds intake for the proportion of copper, horizontal casting system duplex furnace body smelting furnace with 1300oC fusing, later
It is transferred to holding furnace, heat preservation furnace temperature is 1200oC, smelting furnace and holding furnace surface cover one layer of charcoal；
(2) casting rod is drawn using horizontal casting mode, casting rod diameter is 10 mm, and off speed is 600 mm/min, crystallization
Device is cooling using water-cooling pattern, and cooling length is 500 mm；
(3) casting rod is carried out Continuous Heat extruding and rolled as diameter to be 15 mm poles, extrusion temperature 800oC simultaneously leads to
With inert gas shielding；
(4) pole is obtained into the copper alloy in 375 DEG C of 100 h of annealing.
Embodiment 2
The difference from embodiment 1 is that Ta element is the replacement of Ti element in step (1), Ti element mass fraction is 0.16%,
Smelting temperature is 1200oC, holding temperature 1100oC, other parameters are identical.
Embodiment 3
The difference from embodiment 1 is that it is 1.24% that Co element weight percent, which is 1.2%, Ta element, in step (1), other
Parameter is identical.
Embodiment 4
The difference from embodiment 1 is that Co element weight percent is that 0.9%, Ta element replaces with Ti member in step (1)
Element, and Ti element weight percent is 0.25%, smelting temperature 1200oC, holding temperature 1100oC, other parameters are identical.
Embodiment 5
The difference from embodiment 1 is that casting rod diameter is 100 mm in step (2), off speed is 60 mm/min, other
Parameter is identical.
Embodiment 6
The difference from embodiment 1 is that casting rod diameter is 20 mm in step (2), off speed is 120 mm/min, cooling
Length is 10 mm, and other parameters are identical.
Embodiment 7
The difference from embodiment 1 is that rolling diameter is 20 mm, extrusion temperature 1000 in step (3)oC, other
Parameter is identical.
Embodiment 8
The difference from embodiment 1 is that annealing temperature is 575 in step (4)oC, time are 1 h, and other parameters are identical.
Comparative example 1
The difference from embodiment 1 is that Co element weight percent is 1.2% in step (1), other parameters are identical.
Comparative example 2
The difference from embodiment 1 is that Co element weight percent is 0.2% in step (1), other parameters are identical.
Comparative example 3
The difference from embodiment 1 is that smelting temperature is 1100 in step (1)oC, holding temperature 1000oC, other ginsengs
Number is identical.
Comparative example 4
The difference from embodiment 1 is that extrusion temperature is 600 in step (3)oC, other parameters are identical.
Comparative example 5
The difference from embodiment 1 is that annealing temperature is 650 in step (4)oC, other parameters are identical.
Using the microstructure of transmission electron microscope observation above-described embodiment and the obtained sample of comparative example, and in use
Heart dark field image shoots and measures precipitate size and spacing, using the position of selective electron diffraction pattern analysis precipitated phase and Cu matrix
Full coherence is judged whether it is using the interfacial structure of high-resolution-ration transmission electric-lens technology observation precipitated phase and Cu matrix to relationship
Phase interface.Referring additionally to national standard GB/T228.1-2010 " metal material stretching test part 1: room temperature test method " test specimens
The tensile strength of product；With reference to the room-temperature conductivity of GB/T 351-1995 " metal material resistivity measurement method " measurement sample.
Such as the Co obtained of Fig. 1 embodiment 13The nanometer precipitated phase transmission electron microscope center dark field image of Ta, Fig. 2 are that embodiment 2 is obtained
Co3The nanometer precipitated phase transmission electron microscope center dark field image of Ti, Fig. 3 are the Co obtained of embodiment 23The nanometer precipitated phase high score of Ti
Distinguish images of transmissive electron microscope；It can see Co3Ta or Co3The diameter distribution of Ti compound nano-particle is 1 ~ 50 nm, and
The grain spacing range is 5 ~ 100 nm.Such as table 1 is described in detail in the result of specific all of above test.
The microstructure features and performance of copper alloy made from 1 embodiment and comparative example of table
| Precipitated phase average diameter (nm) | Precipitated phase average headway (nm) | Precipitated phase and Cu matrix orientation relationship | Precipitated phase and Cu basal body interface structure | Tensile strength (MPa) | Conductivity (%IACS) | |
| Embodiment 1 | 8.3 | 52 | Cube-on-cube | Full coherence | 530 | 85 |
| Embodiment 2 | 9.1 | 60 | Cube-on-cube | Full coherence | 550 | 83 |
| Embodiment 3 | 7.6 | 21 | Cube-on-cube | Full coherence | 620 | 78 |
| Embodiment 4 | 8.1 | 32 | Cube-on-cube | Full coherence | 580 | 80 |
| Embodiment 5 | 8.5 | 55 | Cube-on-cube | Full coherence | 540 | 84 |
| Embodiment 6 | 8.3 | 55 | Cube-on-cube | Full coherence | 530 | 84 |
| Embodiment 7 | 8.5 | 51 | Cube-on-cube | Full coherence | 540 | 83 |
| Embodiment 8 | 9.8 | 60 | Cube-on-cube | Full coherence | 520 | 86 |
| Comparative example 1 | 6.2 | 102 | Cube-on-cube | Full coherence | 550 | 68 |
| Comparative example 2 | 6.5 | 153 | Cube-on-cube | Full coherence | 460 | 62 |
| Comparative example 3 | / | / | / | / | 450 | 80 |
| Comparative example 4 | 87 | 125 | / | / | 480 | 79 |
| Comparative example 5 | 205 | 320 | / | / | 420 | 88 |
It can be seen that the sample obtained of embodiment 1 ~ 8 embodies good intensity and conductivity from upper table result
Match, basic reason is in sample that there are the nanometer precipitated phases of a large amount of Dispersed precipitates, and nanometer precipitated phase and Cu matrix exist
Cube-on-cube orientation relationship, phase interface are full coherent boundary, and dot matrix mispairing is small, weak to electron scattering.
Comparative analysis embodiment 1 and the ratio of the visible Co and Ta of comparative example 1 and 2 have great influence for alloy property,
When Co and Ta do not meet 3:1 relationship, Co element will occurs or Ta element is remaining, generated solid solution effect is consumingly damaged
Alloy conductive.
Comparative analysis embodiment 1 and the visible melting of comparative example 3 and the selection of holding temperature are very crucial, when temperature used is relatively low
When be difficult to sufficiently melt dystectic Ta element, can not obtain perspec-tive Co and Ta or Ti formed compound solid solution,
Namely it is difficult to obtain superperformance.
The control of comparative analysis embodiment 1 and the visible extrusion temperature of comparative example 4 is very crucial, although carrying out to extrusion process
Preheating is technology commonly used in the art, if however preheating temperature is relatively low, the compound that will lead to Co and Ta or Ti is precipitated in advance, can not
Obtain reasonable microstructure and performance of the invention.
The selection of comparative analysis embodiment 1 and the visible final annealing temperature and time of comparative example 5 is very crucial, if higher
Temperature long term annealing, will be that precipitated phase is acutely grown up, and loses the symbiosis and epibiosis with Cu matrix, formedness can not be obtained
Energy.
Claims (5)
1. a kind of copper alloy of high-speed railway contact line, it is characterised in that: it is 0.6% that the copper alloy, which contains weight percent,
The Ta of~1.2% Co and 0.61%~1.24%, and the atomic ratio of Co and Ta is 3:1, surplus is copper；And Ta and Co is tied
Conjunction forms Co3Ta compound, the Co3Ta compound is embedded in Copper substrate with form of nanoparticles；And the Co3Ta compound
Nano particle and Copper substrate form cube-on-cube orientation relationship, the Co3The nano particle of Ta compound and Copper substrate
Phase interface is full coherent interphase face.
2. a kind of copper alloy of high-speed railway contact line according to claim 1, it is characterised in that: the Co3Ta chemical combination
The diameter of the nano particle of object is 1~50nm, and nano particle spacing range is 5~100nm.
3. a kind of preparation method of the copper alloy of high-speed railway contact line according to claim 1 or claim 2, it is characterised in that packet
Include following steps:
1) it using simple substance and/or intermediate alloy as raw material, feeds intake according to a certain ratio, in the melting of horizontal casting system duplex furnace body
Furnace fusing, is transferred to holding furnace later, and smelting furnace and holding furnace surface cover one layer of charcoal；Wherein fusion temperature be 1200~
1300 DEG C, heat preservation furnace temperature is 1100~1200 DEG C；
Wherein the simple substance is Ni metal, Co, Ta；
The intermediate alloy is Cu-Co or Cu-Ta alloy；
And the proportion is satisfaction: the atomic ratio of 0.6%~1.2% Co and 0.61%~1.24% Ta and Co and Ta
For 3:1, surplus is copper；
2) casting rod is drawn using horizontal casting mode；
3) casting rod is subjected to Continuous Heat extruding and rolled as pole；And extrusion temperature is 800~1000 DEG C, while passing to inertia
Gas shield；
4) pole is annealed, wherein annealing temperature is 375~575 DEG C, and annealing time is 1~100 hour, and the copper is made and closes
Gold.
4. a kind of preparation method of the copper alloy of high-speed railway contact line according to claim 3, it is characterised in that: described
Off speed is 60~600mm/min in step 2), and the diameter of the casting rod is 10~100mm.
5. a kind of preparation method of the copper alloy of high-speed railway contact line according to claim 3, it is characterised in that: described
The diameter for the pole for squeezing and rolling by Continuous Heat in step 3) is 15~20mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710218266.7A CN106906378B (en) | 2017-04-05 | 2017-04-05 | A kind of high-speed railway copper alloy for contact line and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710218266.7A CN106906378B (en) | 2017-04-05 | 2017-04-05 | A kind of high-speed railway copper alloy for contact line and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106906378A CN106906378A (en) | 2017-06-30 |
| CN106906378B true CN106906378B (en) | 2019-01-11 |
Family
ID=59195250
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710218266.7A Active CN106906378B (en) | 2017-04-05 | 2017-04-05 | A kind of high-speed railway copper alloy for contact line and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106906378B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116555625A (en) * | 2023-05-08 | 2023-08-08 | 大连理工大学 | Multi-scale multiphase coherent precipitation strengthening Cu-Ni-Al-Co-Cr-Ti high-temperature-resistant copper alloy and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4734255A (en) * | 1985-04-02 | 1988-03-29 | Wieland-Werke Ag | Use of a copper-titanium-cobalt alloy as the material for electronic components |
-
2017
- 2017-04-05 CN CN201710218266.7A patent/CN106906378B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4734255A (en) * | 1985-04-02 | 1988-03-29 | Wieland-Werke Ag | Use of a copper-titanium-cobalt alloy as the material for electronic components |
Non-Patent Citations (1)
| Title |
|---|
| Precipitation in Cu-Rich Co-Ti Ternary Alloys;L.Mineau et al.;《Phys. stat. sol.》;19921231;第134卷(第93期);第93-105页 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN106906378A (en) | 2017-06-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106916997B (en) | A kind of copper alloy and preparation method thereof for high-speed railway contact line | |
| CN106011517B (en) | Copper alloy with high strength and high conductivity and its application that wire material is contacted as more than 400 kilometers high-speed railways of speed per hour | |
| Huang et al. | Optimizing the strength, ductility and electrical conductivity of a Cu-Cr-Zr alloy by rotary swaging and aging treatment | |
| CN103328665B (en) | The manufacture method of copper alloy and copper alloy | |
| US10801087B2 (en) | High-strength and high-conductivity copper alloy and applications of alloy as material of contact line of high-speed railway allowing speed higher than 400 kilometers per hour | |
| CN104700961A (en) | Graphene/silver composite material and preparation method thereof | |
| CN102888525B (en) | Processing method of high-obdurability and high-conductivity copper magnesium alloy | |
| CN107012356B (en) | A kind of high-intensity high-conductivity copper based alloy blank of graphene-containing and preparation method thereof | |
| CN101386925A (en) | Cu-Cr-Zr alloy preparation technology for contact wire | |
| CN105839038A (en) | Preparation method for high-strength high-conductivity Cu-Ag-Fe alloy | |
| Wang et al. | Synchronous improvement of electrical and mechanical performance of A356 alloy reinforced by boron coupling nano-AlNp | |
| CN105925923B (en) | The preparation method of copper alloy with high strength and high conductivity as more than 400 kilometers high-speed railway contact wire materials of speed per hour | |
| CN112030030B (en) | High-strength high-conductivity copper alloy wire and preparation method thereof | |
| CN106591610B (en) | A kind of method that discharge plasma sintering prepares copper alloy with high strength and high conductivity | |
| CN109576529A (en) | High-performance disperse copper alloy and preparation method thereof | |
| CN106906378B (en) | A kind of high-speed railway copper alloy for contact line and preparation method thereof | |
| Tang et al. | Evolution of microstructure and properties of Cu-4.5 wt.% Ag alloy prepared by vacuum horizontal continuous casting in solid solution and aging treatment | |
| CN102400007B (en) | Eutectic strengthening reinforced Cu-Ag alloy and preparation method thereof | |
| CN106987739B (en) | Copper alloy and preparation method thereof for high ferro contact line | |
| CN106086505B (en) | A kind of preparation method of superpower high-conductivity copper alloy as more than 400 kilometers high-speed railway contact line materials applications of speed per hour | |
| CN109722561A (en) | High-performance Cu-Cr alloy and preparation method | |
| CN102021359B (en) | Cu-Ni-Si alloy with high Ni and Si content and preparation method thereof | |
| CN108456801A (en) | A kind of original position Ni3The copper alloy and preparation method thereof of Ti enhancings | |
| CN115044800B (en) | High-strength high-conductivity copper alloy and preparation method thereof | |
| CN114990376B (en) | Ternary high-strength high-conductivity copper alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |