CN108193077A - Cu-Fe-C alloys - Google Patents
Cu-Fe-C alloys Download PDFInfo
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- CN108193077A CN108193077A CN201810259093.8A CN201810259093A CN108193077A CN 108193077 A CN108193077 A CN 108193077A CN 201810259093 A CN201810259093 A CN 201810259093A CN 108193077 A CN108193077 A CN 108193077A
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- 229910045601 alloy Inorganic materials 0.000 title claims description 78
- 239000000956 alloy Substances 0.000 title claims description 78
- 229910017112 Fe—C Inorganic materials 0.000 title claims description 62
- 239000000843 powder Substances 0.000 claims abstract description 87
- 238000005245 sintering Methods 0.000 claims abstract description 50
- 239000002994 raw material Substances 0.000 claims abstract description 42
- 239000002131 composite material Substances 0.000 claims abstract description 19
- 238000002156 mixing Methods 0.000 claims abstract description 17
- 238000000498 ball milling Methods 0.000 claims abstract description 10
- 239000002245 particle Substances 0.000 claims description 13
- 238000009826 distribution Methods 0.000 claims description 8
- 229910001339 C alloy Inorganic materials 0.000 abstract description 3
- 229910000640 Fe alloy Inorganic materials 0.000 abstract 1
- 239000011812 mixed powder Substances 0.000 abstract 1
- 239000010949 copper Substances 0.000 description 37
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 22
- 229910052799 carbon Inorganic materials 0.000 description 19
- 229910017827 Cu—Fe Inorganic materials 0.000 description 10
- 229910000906 Bronze Inorganic materials 0.000 description 7
- 239000010974 bronze Substances 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 7
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 229910000881 Cu alloy Inorganic materials 0.000 description 5
- AFCARXCZXQIEQB-UHFFFAOYSA-N N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CCNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 AFCARXCZXQIEQB-UHFFFAOYSA-N 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000012805 post-processing Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 229910001316 Ag alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000013065 commercial product Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
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
-
- 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0425—Copper-based alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
The present invention provides a kind of Cu Fe C alloys, is prepared by following steps：(1) prepare raw material：The raw material includes pure Cu powder and Fe C prealloy powder, (2) ball milling mixing：It adds in abrading-ball and carries out mixed powder, obtain composite powder, (3) hot pressed sintering：The composite powder obtained in the step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature is 800~1000 DEG C, and sintering pressure is 45~55MPa, and sintering time is 30min~45min, obtains Cu Fe C alloys.The present invention can improve the conductivity and tensile strength of Cu Fe alloys.
Description
Technical field
The present invention relates to composite materials to lead field, more particularly to a kind of Cu-Fe-C alloys.
Background technology
Compared with the copper alloy with high strength and high conductivity of other systems, the fusing point of alloying element Fe is relatively low in Cu-Fe systems, is easier to
Melting, and non-miscible gap of Fe and Cu is small, the deformability of alloy is preferable, and machinability is preferable, so being closed about Cu-Fe systems
The research of gold receives attention, becomes one of the important directions of copper alloy with high strength and high conductivity development.
At present, high-strength highly-conductive Cu-Fe systems alloy mainly prepares just alloy using fusion casting, then first alloy is carried out follow-up
The processing such as heat treatment, deformation, obtain the Cu-Fe systems alloy of final use state.When founding prepares just alloy, due to solidification
Cooling velocity is very fast, it is easy to cause to be dissolved a large amount of Fe elements in Cu matrixes, the serious electric conductivity for reducing Cu-Fe alloys.Though
So oversaturated Fe is constantly precipitated during subsequent heat treatment, thermomechanical treatment etc., but under low temperature Fe diffusion velocity it is very slow,
It is difficult to the Fe being dissolved in Cu is precipitated completely, and solid solutions of the Fe in Cu is to reduce the main influence factor of Cu-Fe alloys.Institute
In order to improve the electric conductivity of Cu-Fe alloys, to need to reduce solid solution capacities of the Fe in Cu.
In the prior art frequently with deformation, heat treatment, high-intensity magnetic field, it is multi-element alloyed the methods of, but cannot all solve well
Certainly this problem.Such as：Ag is considered as to damage the minimum element of Cu alloy conductives effect, but utilizes Ag to Cu-Fe alloys
The Cu-Fe-Ag alloys of alloying preparation are carried out, but more than 2.5% Fe is still dissolved in its as cast condition Cu matrixes；And Ag also drops
The low stability of Fe phase fibers, causes Fe phases to be roughened at 350 DEG C or more, reduces the use temperature range for limiting alloy；And
It is and higher using Ag alloying costs.The Fe being dissolved in Cu can not be equally reduced to very low state by other methods.
In order to more effectively reduce the Fe being dissolved in Cu, it is necessary to provide a kind of Fe-Cu-C alloys.
Invention content
The purpose of the present invention is to provide a kind of Cu-Fe-C alloys, can efficiently reduce the Fe being dissolved in Cu-, improve
The electric conductivity of Cu-Fe alloys, also improves the stability of Fe phase fibers, Fe phases will not be caused to be roughened at 350 DEG C or more, carried
The high use temperature range of alloy, and reduce the manufacturing cost of alloy.
To achieve these goals, the present invention provides following technical solution：
A kind of Cu-Fe-C alloys, Cu-Fe-C alloys are prepared by following steps：
(1) prepare raw material：Raw material includes pure Cu powder and Fe-C prealloy powder,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
Spend for 800~1000 DEG C (such as 820 DEG C, 830 DEG C, 840 DEG C, 850 DEG C, 860 DEG C, 870 DEG C, 880 DEG C, 890 DEG C, 900 DEG C, 910
DEG C, 920 DEG C, 930 DEG C, 940 DEG C, 950 DEG C, 960 DEG C, 970 DEG C, 980 DEG C, 990 DEG C), sintering pressure for 45~55MPa (such as
46MPa, 47MPa, 48MPa, 49MPa, 50MPa, 51MPa, 52MPa, 53MPa, 54MPa), sintering time is 30min~45min
(such as 31min, 32min, 33min, 34min, 35min, 36min, 37min, 38min, 39min, 40min, 41min, 42min,
43min, 44min),
Obtain the Cu-Fe-C alloys of Fe-C even particle distributions.
The Cu-Fe-C alloys prepared by above-mentioned steps are a kind of novel high-strength highly-conductive Cu alloys, and C is utilized and Cu exists
Mutually exclusive effect in Fe-Cu-C ternary systems, therefore C is added into Cu, and for this effect for giving full play to C,
Cu-Fe-C alloys are prepared using Cu powder, Fe-C prealloy powder hot pressed sintering.The tensile strength of Cu-Fe-C alloys obtained is 560
~640MPa, conductivity are 54~62%IACS.
In the alloy of the present invention, as a kind of preferred embodiment, the grain size of pure Cu powder is 10~50 μm.Pure Cu powder
When grain size is 10~50 μm, Fe-C particles can be more evenly distributed in Cu matrixes.The size of Fe-C prealloy powder for 50~
120nm (such as 60nm, 70nm, 80nm, 90nm, 100nm, 50nm~70nm, 60~80nm, 70~80nm, 80~100nm,
100~120nm).The Fe-C alloyed powders are commercial product, naturally it is also possible to conventionally prepare, it can be by true
Prepared by empty atomizing furnace, will be atomized into powder particle after the pure iron as raw material of required proportioning and carburant melting, then pass through high energy again
Ball milling is prepared into the Fe-C alloyed powders of required granularity.The Fe-C alloyed powders particle size used in the present invention is 50~120nm,
Fe-C alloy powder particles it is oversized, disperse can be caused so cause precipitation strength effect reduction；Fe-C alloy powder particles
It is undersized, easily Fe is made to be dissolved in Cu, electric conductivity is deteriorated, and is also easy to reunite.
Further, the size of Fe-C prealloy powder is 60~80nm.In the reasonable scope, the size of Fe-C prealloy powder
Smaller, dispersion-strengthened action is bigger, but its surface can be bigger simultaneously, is dissolved in the easier matrix to Cu.
In the alloy of the present invention, as a kind of preferred embodiment, raw material includes pure Cu powder and Fe-C prealloy powder, institute
The 85-90wt% (such as 86%, 87%, 88%, 89%) that pure Cu powder accounts for the raw material is stated, the Fe-C prealloy powder accounts for described
The 10-15wt% of raw material such as 11%, 12%, 13%, 14%).
In the alloy of the present invention, as a kind of preferred embodiment, the C in the Fe-C prealloy powder accounts for the pre- conjunction
Bronze 0.8-1.8wt% (such as：0.9wt%, 1.0wt%, 1.1wt%, 1.2wt%, 1.3wt%, 1.4wt%,
1.5wt%, 1.6wt%, 1.7wt%).
In the alloy of the present invention, C content is too low will to lead to have more Fe to dissolve in Cu, to the electric conductivity of alloy not
Profit, C content is excessively high to form graphite or Fe3C。
In the step of preparing alloy of the present invention, as a kind of preferred embodiment, alloy post-processing step is further included, it will
The Cu-Fe-C systems alloy that (3) the hot pressed sintering step obtains is post-processed, and obtains Cu-Fe-C systems alloy finished product.More preferably
Ground, the post processing are one or more in heat treatment, deformation process, magnetic field processing；The post processing is conventional treatment.
Analysis is it is found that a kind of Cu-Fe-C alloys disclosed by the invention, mainly realize following technique effect：Utilize C and Cu
Mutually exclusive effect in Fe-Cu-C ternary systems, therefore C is added into Cu, and for this work for giving full play to C
With, using Cu powder, Fe-C prealloy powder hot pressed sintering prepare Cu-Fe-C alloys, have developed novel high-strength highly-conductive Cu alloys.
Diffusions of the Fe into Cu matrixes is controlled, the solid solution capacity of Fe in Cu matrixes is greatly reduced.The method of the present invention can improve
The conductivity and tensile strength of Cu-Fe alloys, the tensile strength of obtained alloy are more than 560MPa, conductivity 54-62%
IACS。
Specific embodiment
Below in conjunction with embodiment, the present invention will be described in detail.Each example the present invention explanation by way of provide and
The unrestricted present invention.In fact, those skilled in the art will be clear that, in the situation for not departing from the scope or spirit of the invention
Under, it can modify in the present invention and modification.For example, the feature for being illustrated or described as the part of one embodiment can be used for
Another embodiment, to generate another embodiment.Thus, it may be desirable to the present invention comprising be included into appended claims and
Such modifications and variations in the range of its equivalent.
Embodiment 1
(1) prepare raw material：The Fe-1.2wt%C that raw material includes 10~50 μm of pure Cu powder and size is 70~120nm is pre-
Alloyed powder, the mass percent of C is 1.2wt% in Fe-C alloy powders, and pure Cu powder accounts for the 89wt% of the raw material, and Fe-C is closed in advance
Bronze accounts for the 11wt% of the raw material,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 900 DEG C, sintering pressure 50MPa, sintering time 30min to spend,
Cu-11wt% (Fe-C) alloy of Fe-1.2wt%C even particle distributions must have been prepared.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 580MPa, and conductivity is
60.8%IACS.
Embodiment 2
(1) prepare raw material：The Fe-1.0wt%C that raw material includes 10~50 μm of pure Cu powder and size is 70~120nm is pre-
Alloyed powder, the mass percent of C is 1.0wt% in Fe-C alloy powders, and pure Cu powder accounts for the 85wt% of the raw material, and Fe-C is closed in advance
Bronze accounts for the 15wt% of the raw material,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 800 DEG C, sintering pressure 50MPa, sintering time 30min to spend,
Cu-15wt% (Fe-C) alloy of Fe-1.0wt%C even particle distributions must have been prepared.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 636MPa, and conductivity is
54.1%IACS.
Embodiment 3
(1) prepare raw material：The Fe-1.1wt%C that raw material includes 10~50 μm of pure Cu powder and size is 50~80nm is closed in advance
Bronze, the mass percent of C is 1.1wt% in Fe-C alloy powders, and pure Cu powder accounts for the 87wt% of the raw material, Fe-C prealloys
Powder accounts for the 13wt% of the raw material,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 820 DEG C, sintering pressure 50MPa, sintering time 30min to spend,
Cu-13wt% (Fe-C) alloy of Fe-1.1wt%C even particle distributions must have been prepared.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 628MPa, and conductivity is
55.6%IACS.
Embodiment 4
(1) prepare raw material：The Fe-1.1wt%C that raw material includes 10~50 μm of pure Cu powder and size is 50~80nm is closed in advance
Bronze, the mass percent of C is 1.1wt% in Fe-C alloy powders, and pure Cu powder accounts for the 90wt% of the raw material, Fe-C prealloys
Powder accounts for the 10wt% of the raw material,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 820 DEG C, sintering pressure 50MPa, sintering time 30min to spend,
Cu-10wt% (Fe-C) alloy of Fe-1.1wt%C even particle distributions must have been prepared.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 573MPa, and conductivity is
57.2%IACS.
Embodiment 5
(1) prepare raw material：The Fe-1.1wt%C that raw material includes 10~50 μm of pure Cu powder and size is 50~80nm is closed in advance
Bronze, the mass percent of C is 1.1wt% in Fe-C alloy powders, and pure Cu powder accounts for the 89wt% of the raw material, Fe-C prealloys
Powder accounts for the 11wt% of the raw material,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 820 DEG C, sintering pressure 50MPa, sintering time 30min to spend,
Cu-11wt% (Fe-C) alloy of Fe-1.1wt%C even particle distributions, i.e., Fe-C in the alloy must have been prepared
Content be 11wt%.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 585MPa, conductivity 61%
IACS。
Embodiment 6
(1) prepare raw material：The Fe-1.1wt%C that raw material includes 10~50 μm of pure Cu powder and size is 60~80nm is closed in advance
Bronze, the mass percent of C is 1.1wt% in Fe-C alloy powders, and pure Cu powder accounts for the 88wt% of the raw material, Fe-C prealloys
Powder accounts for the 12wt% of the raw material,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 820 DEG C, sintering pressure 50MPa, sintering time 30min to spend,
Cu-12wt% (Fe-C) alloy of Fe-1.1wt%C even particle distributions must have been prepared.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 615MPa, and conductivity is
54.8%IACS.
Embodiment 7-12 and comparative example 1-2
Embodiment 7-12 and comparative example 1-2 in addition to raw material proportioning and raw material granularity are different from embodiment 1, other techniques with
Embodiment 1 is identical.The raw material dosage relationship of embodiment 7-12 and comparative example 1-2 and raw material granularity referring to table 1, corresponding embodiment and
The performance test results of alloy prepared by comparative example are referring to table 1.As can be seen from Table 1, (tension is strong for the performance of embodiment 8,9,10
Degree and conductivity) significantly better than comparative example 1,2 and embodiment 7,11,12.
The raw material dosage relationship and raw material granularity of table 1 embodiment 7-12 and comparative example 1-2 and corresponding product performance table
Embodiment 13-17
For embodiment 13-17 in addition to hot pressed sintering is different from embodiment 1, other techniques are same as Example 1.Embodiment
The performance test results for the alloy product that the hot pressed sintering of 13-17 is obtained referring to table 2, corresponding embodiment and comparative example are referring to table 2.
As can be seen from Table 2, the performance (tensile strength and conductivity) of embodiment 13,14,15 is significantly better than embodiment 16,17.
The stirring condition and properties of product table of 2 embodiment 13-17 of table
Claims (10)
1. a kind of Cu-Fe-C alloys, which is characterized in that the Cu-Fe-C alloys are prepared by following steps：
(1) prepare raw material：The raw material includes pure Cu powder and Fe-C prealloy powder,
(2) ball milling mixing：It adds in abrading-ball and carries out powder mixing machine, obtain composite powder,
(3) hot pressed sintering：The composite powder obtained in the step (2) is put into hot-pressed sintering furnace and is sintered, sintering temperature
It is 800~1000 DEG C to spend, and sintering pressure is 45~55MPa, and sintering time is 30min~45min,
Obtain the Cu-Fe-C alloys of Fe-C even particle distributions.
2. alloy according to claim 1, which is characterized in that the grain size of the pure Cu powder is 10~50 μm.
3. alloy according to claim 1, which is characterized in that the size of the Fe-C prealloy powder is 50~120nm.
4. alloy according to claim 1, which is characterized in that the size of the Fe-C prealloy powder is 60~110nm.
5. alloy according to claim 1, which is characterized in that the size of the Fe-C prealloy powder is 60~80nm.
6. alloy according to claim 1, which is characterized in that the C content in the Fe-C prealloy powder is 0.8-
1.8wt%.
7. alloy according to claim 1, which is characterized in that the pure Cu powder accounts for the 85-90wt% of the raw material, described
Fe-C prealloy powder accounts for the 10-15wt% of the raw material.
8. alloy according to claim 1, which is characterized in that the C in the Fe-C prealloy powder accounts for the prealloy powder
0.8~1.2wt%.
9. alloy according to claim 1, which is characterized in that C content in the Fe-C prealloy powder for 1.0~
1.2wt%.
10. alloy according to claim 1, which is characterized in that C content in the Fe-C prealloy powder for 1.2~
1.6wt%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810259093.8A CN108193077B (en) | 2018-03-27 | 2018-03-27 | Cu-Fe-C alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810259093.8A CN108193077B (en) | 2018-03-27 | 2018-03-27 | Cu-Fe-C alloy |
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| CN108193077B CN108193077B (en) | 2019-11-19 |
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ID=62596205
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117604301A (en) * | 2023-11-24 | 2024-02-27 | 河南理工大学 | Preparation method of elastic refrigeration alloy |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01259103A (en) * | 1988-04-08 | 1989-10-16 | Toyota Motor Corp | Method for sintering fe-c-cu series multi-component alloy powder |
| CN104263985A (en) * | 2014-09-24 | 2015-01-07 | 西安理工大学 | Preparation method of self-hard reinforced Cu-FeC composite material |
| CN105543534A (en) * | 2015-12-18 | 2016-05-04 | 中国科学院兰州化学物理研究所 | Copper-based pantograph sliding plate material and preparation method thereof |
-
2018
- 2018-03-27 CN CN201810259093.8A patent/CN108193077B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01259103A (en) * | 1988-04-08 | 1989-10-16 | Toyota Motor Corp | Method for sintering fe-c-cu series multi-component alloy powder |
| CN104263985A (en) * | 2014-09-24 | 2015-01-07 | 西安理工大学 | Preparation method of self-hard reinforced Cu-FeC composite material |
| CN105543534A (en) * | 2015-12-18 | 2016-05-04 | 中国科学院兰州化学物理研究所 | Copper-based pantograph sliding plate material and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 刘宇龙 等: "添加球磨铁碳粉对Fe-2Cu-0.8C材料性能的影响", 《粉末冶金技术》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117604301A (en) * | 2023-11-24 | 2024-02-27 | 河南理工大学 | Preparation method of elastic refrigeration alloy |
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