CN1563446A - Technique for preparing high comductive wearable antifictional copper based composite material - Google Patents
Technique for preparing high comductive wearable antifictional copper based composite material Download PDFInfo
- Publication number
- CN1563446A CN1563446A CN 200410017686 CN200410017686A CN1563446A CN 1563446 A CN1563446 A CN 1563446A CN 200410017686 CN200410017686 CN 200410017686 CN 200410017686 A CN200410017686 A CN 200410017686A CN 1563446 A CN1563446 A CN 1563446A
- Authority
- CN
- China
- Prior art keywords
- powder
- pressed compact
- preheating
- cold
- copper
- 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.)
- Granted
Links
Abstract
A preparation technology for high electric conduction, abrasive resistance, antifriction copper base compound material takes electrolysis copper powder, nickel plating or SiC powders and copper plating graphite powder as the raw material to be dry mixed, humid mixed with a dispersant agent, cold pressure, sinter, hot extrusion or hot pressing to manufacture the high conduction abrasive resistance antifriction copper base compound material.
Description
Technical field
The present invention relates to a kind of preparation technology of metal-base composites, specifically is a kind of preparation technology of high conduction wear resistant friction reducing Cu-base composites.Be used for sliding and electrically contact technical field.
Background technology
Fast development along with industry such as electronics, machinery, Aeronautics and Astronautics, press for exploitation and have satisfactory electrical conductivity, thermal conductivity, wear resistance, and the functional materials that mechanical property is good, moderate is for example as electronic material, high-abrasive material, thermal resistance material, brush material and nozzle material etc.Cu-base composites can keep the good electrical and thermal conductivity performance of copper itself, simultaneously by adding single or miscellaneous strengthens body and can give higher mechanical property of material and good tribological property, so the field such as electrically contact in slip wide application prospect is arranged.The main technique of the discontinuous enhancing Cu-base composites of preparation has internal oxidation, vacuum to mix casting, mechanical alloying method etc. at present.Find Zheng Hui Chun etc. by retrieval; " novel resistance welding electrode material-dispersion-strengthened Cu " [publication: welding machine of delivering; 1997 (4): 38-41], this article is mentioned the ripe relatively of internal oxidation, and it is that Cu-Al solid solution alloy with melting is atomized into powder with high pressure gas with melt; and be encapsulated in the vacuum vessel after mixing by theoretical proportioning and oxygenant; be heated to high temperature then, make oxygenant decompose generation oxygen and be diffused in the Cu-Al alloying pellet, preferential and reactive aluminum generates tiny Al
2O
3Dispersoid particle.After alloy is all oxidized, place the reducing atmosphere heating to remove unnecessary oxygen in powder, adopt various common process the metal powder after handling can be made complete closely knit section bar then.Because these technology more complicated, quality of materials are difficult to control, appointed condition are had relatively high expectations, so the cost height, also have certain distance from scale production.Simultaneously, because the wettability of copper and most of potteries is relatively poor, density difference is bigger, is easy to generate the gathering of reinforce when adopting ordinary method to prepare, and causes size distribution inhomogeneous, and the enhancing body combines bad with the interface of matrix.
Summary of the invention
The objective of the invention is at deficiency of the prior art, a kind of preparation technology of high conduction wear resistant friction reducing Cu-base composites is provided, in required ratio metal-powder and discontinuous reinforce are mixed under the condition of doing mixed or wet mixing, the reinforce distribution problem that it has been solved, prepared Cu-base composites has favorable conductive, thermal conductivity height, wear resisting property, and the preparation supply is fairly simple, cost is lower.
The present invention realizes by following proposal, preparation technology of the present invention is a raw material with electrolytic copper powder, nickel plating or copper facing SiC powder and copper coated graphite powder, by driedly mix, add the dispersion agent wet mixing, cold pressing, sintering, hot extrusion or hot pressing makes high conduction wear resistant friction reducing Cu-base composites.
Below the present invention is further illustrated, processing step is:
(1) it is dried mixed that copper powder, nickel plating SiC powder and copper coated graphite powder stirring are separated in power taking, and adding weight percent (down together) is 0.1% dispersion agent, stirs, and mixing is 3-5 hour in the mixed powder device of the routine of packing into then.
(2) the blended powder is packed in the mould, under the pressure of 130-160Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, sintering temperature 800-850 ℃, sintering time 3 hours; Stove is cold.
(4) heating of agglomerating pressed compact and preheating, the pressed compact of preheating is put into the extrusion mould extrusion molding then.
Described step (4), for not graphitiferous material: the agglomerating pressed compact is heated to 790-810 ℃, is incubated 5 minutes; Extrusion mould preheating under 350 ℃ temperature simultaneously, the pressed compact of preheating is put into the extrusion mould extrusion molding then, and extrusion ratio is 10: 1; For graphitiferous material: the agglomerating pressed compact is heated to 810-830 ℃, be incubated 5 minutes, hot pressing die preheating under 300 ℃ temperature is put into hot pressing die hot compacting under the pressure of 180Mpa with the pressed compact of preheating simultaneously, and the dwell time is 10 minutes.
The kind of choose reasonable matrix of the present invention and reinforce, and scientifically carried out the composition design, by adding good mechanical performance and low-cost SiC particle as reinforce, conduction, thermal conductivity height have been obtained, wear resisting property is good, and fairly simple, the lower-cost granule reinforced copper base composite material of preparation supply.Test result to material shows: reinforce is evenly distributed, the density of material＞98%, and Brinell hardness (HB) 78.1-88.9, specific conductivity does not coexist between the 69.9-82.6%IACS according to composition, and thermal conductivity reaches 248-313W/mK according to the composition difference; Test-results on MM200 ring-piece formula wear testing machine shows that the composite-material abrasive performance is good, in load is 100N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, wear rate is the 0.106-0.148 of fine copper, is the 0.424-0.589 of cold-drawn Cu-0.65%Cr-0.08%Zr (weight percent) alloy; Under the 0.42m/s abrasive conditions, the load of matrix material generation heavy wear is 220-300N, is much higher than the 100N of matrix; Use the wearing and tearing of sem observation material to show pattern, SiC particle reinforce can reduce adhesive wear, helps improving the life-span of whole friction pair.
Embodiment
Provide following examples in conjunction with content of the present invention:
Embodiment 1:
(1) copper powder 384.6g is separated in power taking, and mean particle size is the nickel plating SiC powder 15.4g of 14 μ m, stirs to do and mixes, and adds 0.52g20# machine oil then, stirs, and reinstalls conventional mixing in the powder device and mixes 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 130Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 800 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 790 ℃, is incubated 5 minutes; Extrusion mould preheating under 350 ℃ temperature simultaneously.The pressed compact of preheating is put into the extrusion mould extrusion molding, and extrusion ratio is 10: 1.
Test result shows: reinforce is evenly distributed, and the density of material is 98.6%, Brinell hardness (HB) 78.1, specific conductivity 82.6%IACS, thermal conductivity 313W/mK; Dry wear test result on MM200 ring-piece formula wear testing machine shows that at load 100N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 14.8% of a fine copper, is 58.9% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; Under the 0.42m/s abrasive conditions, the load of matrix material generation heavy wear is 220N; The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces.
Embodiment 2:
(1) copper powder 384.6g is separated in power taking, and mean particle size is the nickel plating SiC powder 15.4g of 20 μ m, stirs to do and mixes, and adds 0.52g20# machine oil then, stirs, and reinstalls conventional mixing in the powder device and mixes 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 140Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 820 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 800 ℃, is incubated 5 minutes; Extrusion mould preheating under 350 ℃ temperature simultaneously.The pressed compact of preheating is put into the extrusion mould extrusion molding, and extrusion ratio is 10: 1.
Test result shows: reinforce is evenly distributed, and the density of material is 98.5%, Brinell hardness (HB) 74.2, specific conductivity 83.7%IACS, thermal conductivity 310W/mK; Dry wear test result on MM200 ring-piece formula wear testing machine shows that at load 100N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 14.6% of a fine copper, is 58.0% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces.
Embodiment 3:
(1) copper powder 376.2g is separated in power taking, and mean particle size is the nickel plating SiC powder 23.8/g of 14 μ m, stirs to do and mixes, and adds 0.6g20# machine oil dispersion agent then, stirs, and reinstalls conventional mixing in the powder device and mixes 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 150Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 810 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 800 ℃, is incubated 5 minutes; Extrusion mould preheating under 350 ℃ temperature simultaneously.The pressed compact of preheating is put into the extrusion mould extrusion molding, and extrusion ratio is 10: 1.
Test result shows: reinforce is evenly distributed, and the density of material is 98.4%, Brinell hardness (HB) 82.4, specific conductivity 77.6%IACS, thermal conductivity 272W/mK; Dry wear test result on MM200 ring-piece formula wear testing machine shows that at load 100N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 12.1% of a fine copper, is 47.8% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces.
Embodiment 4:
(1) electrolytic copper powder 367.1g, mean particle size is the nickel plating SiC powder 32.9g of 14 μ m, stirs to do and mixes, and adds 0.6g20# machine oil then, stirs, and reinstalls conventional mixing in the powder device and mixes 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 160Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 820 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 800 ℃, is incubated 5 minutes; Extrusion mould preheating under 350 ℃ temperature simultaneously.The pressed compact of preheating is put into the extrusion mould extrusion molding, and extrusion ratio is 10: 1.
Test result shows: reinforce is evenly distributed, and the density of material is 98.1%, Brinell hardness (HB) 88.4, specific conductivity 69.9%IACS, thermal conductivity 248W/mK; Dry wear test result on M200 ring-piece formula wear testing machine shows that at load 100N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 10.6% of a fine copper, is 42.4% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; Under the 0.42m/s abrasive conditions, the load of matrix material generation heavy wear is 300N; The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces.
Embodiment 5:
(1) copper powder 366.5g is separated in power taking, and mean particle size is the nickel plating SiC powder 16.4g of 14 μ m, stirs to do and mixes; Add 0.72g20# machine oil then, stir; Add copper coated graphite powder 17.1g again, make it to be stirred to the each several part solid colour with aforementioned mixed powder, conventional the mixing in the powder device of packing into then mixed 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 130Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 850 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 810 ℃, is incubated 5 minutes; Hot pressing die preheating under 300 ℃ temperature simultaneously.The pressed compact of preheating is put into hot pressing die hot compacting under the pressure of 180Mpa, and the dwell time is 10 minutes.
Test result shows: SiC and graphite granule are evenly distributed, and the density of material is 99.1%, Brinell hardness (HB) 68.8, specific conductivity 74.6%IACS; Dry wear test result on M200 ring-piece formula wear testing machine shows that at load 40N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 44.7% of a fine copper, is 52.3% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; Frictional coefficient 0.39 is 81.1% of fine copper, is 76.5% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy.The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces; Graphite can effectively improve the wear resistance of matrix material, reduces frictional coefficient, also reduces the wearing and tearing to mating part, has greatly improved the life-span of whole friction system.
Embodiment 6:
(1) copper powder 356.7g is separated in power taking, and mean particle size is the nickel plating SiC powder 25.5g of 14 μ m, stirs to do and mixes; Add 0.72g20# machine oil then, stir; Add copper coated graphite powder 17.8g again, make it to be stirred to the each several part solid colour with aforementioned mixed powder, conventional the mixing in the powder device of packing into then mixed 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 130Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 850 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 830 ℃, is incubated 5 minutes; Hot pressing die preheating under 300 ℃ temperature simultaneously.The pressed compact of preheating is put into hot pressing die hot compacting under the pressure of 180Mpa, and the dwell time is 10 minutes.
Test result shows: SiC and graphite granule are evenly distributed, and the density of material is 98.9%, Brinell hardness (HB) 74.2, specific conductivity 71.2%IACS; Dry wear test result on M200 ring-piece formula wear testing machine shows that at load 40N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 35.5% of a fine copper, is 41.5% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; Frictional coefficient 0.42 is 87.3% of fine copper, is 82.4% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy.The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces; Graphite can effectively improve the wear resistance of matrix material, reduces frictional coefficient, also reduces the wearing and tearing to mating part, has greatly improved the life-span of whole friction system.
Embodiment 7:
(1) electrolytic copper powder 361.6g, mean particle size is the nickel plating SiC powder 20.3g of 14 μ m, stirs to do and mixes; Add 0.72g20# machine oil then, stir; Add copper coated graphite powder 18.1g again, make it to be stirred to the each several part solid colour with aforementioned mixed powder, conventional the mixing in the powder device of packing into then mixed 4 hours.
(2) the blended powder is packed in the mould, under the pressure of 130Mpa, be cold-pressed into base, pressurize 5 minutes.
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, 840 ℃ of sintering temperatures, sintering time 3 hours; Stove is cold.
(4) the agglomerating pressed compact is heated to 820 ℃, is incubated 5 minutes; Hot pressing die preheating under 300 ℃ temperature simultaneously.The pressed compact of preheating is put into hot pressing die hot compacting under the pressure of 180Mpa, and the dwell time is 10 minutes.
Test result shows: SiC and graphite granule are evenly distributed, and the density of material is 99.1%, Brinell hardness (HB) 70.3, specific conductivity 73.1%IACS; Dry wear test result on M200 ring-piece formula wear testing machine shows that at load 40N, relative sliding velocity is under the DRY SLIDING of 0.42m/s, and wear rate is 39.3% of a fine copper, is 46.6% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy; Frictional coefficient 0.40 is 83.6% of fine copper, is 79.8% of cold-drawn Cu-0.65%Cr-0.08%Zr alloy.The sem observation of worn surface finds that with fine copper and cold-drawn Cu-0.65%Cr-0.08%Zr alloy phase ratio, the adhesive wear of matrix material obviously reduces; Graphite can effectively improve the wear resistance of matrix material, reduces frictional coefficient, also reduces the wearing and tearing to mating part, has greatly improved the life-span of whole friction system.
Claims (4)
1. the preparation technology of one kind high conduction wear resistant friction reducing Cu-base composites, it is characterized in that, with electrolytic copper powder, nickel plating or copper facing SiC powder and copper coated graphite powder is raw material, by driedly mix, add the dispersion agent wet mixing, cold pressing, sintering, hot extrusion or hot pressing makes high conduction wear resistant friction reducing Cu-base composites.
2. the preparation technology of high conduction wear resistant friction reducing Cu-base composites according to claim 1 is characterized in that, below the present invention is done further qualification, and processing step is:
(1) it is dried mixed that copper powder, SiC powder and Graphite Powder 99 stirring are separated in power taking, and the adding weight percent is 0.1% dispersion agent, stirs, and mixing is 3-5 hour in the conventional mixed powder device of packing into then;
(2) the blended powder is packed in the mould, under the pressure of 130-160Mpa, be cold-pressed into base, pressurize 5 minutes;
(3) above-mentioned pressed compact is placed the ammonia destruction furnace sintering, sintering temperature 800-850 ℃, sintering time 3 hours, stove is cold;
(4) heating of agglomerating pressed compact and preheating, the pressed compact of preheating is put into the extrusion mould extrusion molding then.
3. the preparation technology of high conduction wear resistant friction reducing Cu-base composites according to claim 2 is characterized in that, described step (4) is specific as follows:
For the single reinforced composite of SiC particle: the agglomerating pressed compact is heated to 790-810 ℃, be incubated 5 minutes, and extrusion mould preheating under 350 ℃ temperature is simultaneously incited somebody to action the pressed compact of preheating then and put into the extrusion mould extrusion molding, and extrusion ratio is 10: 1;
For graphitiferous material, the agglomerating pressed compact is heated to 810-830 ℃, is incubated 5 minutes, simultaneously hot pressing die preheating under 300 ℃ temperature, the pressed compact of preheating is put into hot pressing die hot compacting under the pressure of 180Mpa, and the dwell time is 10 minutes.
4. the preparation technology of high conduction wear resistant friction reducing Cu-base composites according to claim 1 and 2 is characterized in that described dispersion agent is a 20# machine oil.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 200410017686 CN1252301C (en) | 2004-04-15 | 2004-04-15 | Technique for preparing high comductive wearable antifictional copper based composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 200410017686 CN1252301C (en) | 2004-04-15 | 2004-04-15 | Technique for preparing high comductive wearable antifictional copper based composite material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1563446A true CN1563446A (en) | 2005-01-12 |
| CN1252301C CN1252301C (en) | 2006-04-19 |
Family
ID=34479097
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 200410017686 Expired - Fee Related CN1252301C (en) | 2004-04-15 | 2004-04-15 | Technique for preparing high comductive wearable antifictional copper based composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1252301C (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101982552A (en) * | 2010-10-21 | 2011-03-02 | 哈尔滨工业大学 | Copper coated graphite and nano-silicon carbide mixed reinforced copper-based composite material and preparation method thereof |
| CN102031410A (en) * | 2010-11-12 | 2011-04-27 | 哈尔滨工业大学 | High-strength wear-resisting self-lubricating copper-base composite material |
| CN102206816A (en) * | 2011-05-04 | 2011-10-05 | 天津大学 | Method for chemically and orderly plating copper and plating tin on graphite flake and application of plated graphite flake |
| CN106435248A (en) * | 2016-10-13 | 2017-02-22 | 龙岩学院 | Method for preparing high-performance copper alloy with silicon wafer cutting mortar |
| CN107346853A (en) * | 2017-09-05 | 2017-11-14 | 湖南锴博新材料科技有限公司 | A kind of conductive wear-resisting combined type brush and preparation method thereof that cools certainly |
-
2004
- 2004-04-15 CN CN 200410017686 patent/CN1252301C/en not_active Expired - Fee Related
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101982552A (en) * | 2010-10-21 | 2011-03-02 | 哈尔滨工业大学 | Copper coated graphite and nano-silicon carbide mixed reinforced copper-based composite material and preparation method thereof |
| CN101982552B (en) * | 2010-10-21 | 2012-06-06 | 哈尔滨工业大学 | Preparation method of copper coated graphite and nano-silicon carbide mixed reinforced copper-based composite material |
| CN102031410A (en) * | 2010-11-12 | 2011-04-27 | 哈尔滨工业大学 | High-strength wear-resisting self-lubricating copper-base composite material |
| CN102206816A (en) * | 2011-05-04 | 2011-10-05 | 天津大学 | Method for chemically and orderly plating copper and plating tin on graphite flake and application of plated graphite flake |
| CN106435248A (en) * | 2016-10-13 | 2017-02-22 | 龙岩学院 | Method for preparing high-performance copper alloy with silicon wafer cutting mortar |
| CN107346853A (en) * | 2017-09-05 | 2017-11-14 | 湖南锴博新材料科技有限公司 | A kind of conductive wear-resisting combined type brush and preparation method thereof that cools certainly |
| CN107346853B (en) * | 2017-09-05 | 2019-08-13 | 湖南中南智造新材料协同创新有限公司 | A kind of conductive wear-resisting combined type brush and preparation method thereof that cools down certainly |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1252301C (en) | 2006-04-19 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1047805C (en) | High-strnegth self-lubricating composite material for high-temperature use and process for producing the same | |
| CN1068909C (en) | Tungsten-copper composite powder | |
| CN104711443B (en) | A kind of graphene/copper composite material and preparation method thereof | |
| CN109182833B (en) | Copper-based powder metallurgy pantograph pan material taking spherical chromium powder as strengthening phase and preparation method thereof | |
| CN110436950B (en) | Preparation method of carbon/carbon composite pantograph sliding plate material with high-component carbon fibers | |
| JPH10168502A (en) | Composite material with high thermal conductivity | |
| CN105803236A (en) | Amorphous alloy reinforced aluminum matrix composite and preparation method thereof | |
| CN1447729A (en) | Method for producing composite components by powder injection molding and composite powder appropriate for use in said method | |
| CN106868335B (en) | A kind of automobile starter carbon brush material and preparation method thereof | |
| CN109554565A (en) | A kind of interface optimization method of carbon nanotube enhanced aluminium-based composite material | |
| CN1932067A (en) | Copper-base graphite and sintered zirconium composite material and its prepn process and use | |
| Queipo et al. | Preparation of pitch-based carbon–copper composites for electrical applications | |
| CN1252301C (en) | Technique for preparing high comductive wearable antifictional copper based composite material | |
| CN100418923C (en) | Compact Ti2AlC-TiB2 composite material and preparation method therefor | |
| CN114427049B (en) | Cu-TiC x Composite material and method for producing the same | |
| CN1167820C (en) | Tin titanium carbide granule reinforced copper base composite material and its preparation method | |
| CN1425784A (en) | High wear resistant/friction reducing tin bronze base composite material | |
| JP2001500567A (en) | Molding materials, especially materials for the powder metallurgical production of highly wear-resistant valve seat rings or valve guides | |
| CN102931560A (en) | Brush material with excellent performance, and preparation method and application thereof | |
| CN110079710B (en) | In-situ nano TiC particle reinforced Al-Si-based composite material and preparation method thereof | |
| CN111390160A (en) | Preparation method of high-friction-coefficient brake material | |
| CN101898245A (en) | Production process of carbon fiber copper matrix composite powder metallurgy bearing | |
| CN101880814B (en) | Abrasion-resistant electricity and heat conducting material and preparation method thereof | |
| CN109136605B (en) | Self-propagating synthesis of copper-based composite powder and application thereof | |
| CN100448572C (en) | Method for preparing copper based composite material reinforced by surface modified granules for spot welding electrode |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20060419 Termination date: 20100415 |