CN108374103A - Cu-Fe-C-Ag alloys - Google Patents
Cu-Fe-C-Ag alloys Download PDFInfo
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- CN108374103A CN108374103A CN201810259079.8A CN201810259079A CN108374103A CN 108374103 A CN108374103 A CN 108374103A CN 201810259079 A CN201810259079 A CN 201810259079A CN 108374103 A CN108374103 A CN 108374103A
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- 229910001316 Ag alloy Inorganic materials 0.000 title claims abstract description 24
- 239000000843 powder Substances 0.000 claims abstract description 84
- 238000005245 sintering Methods 0.000 claims abstract description 51
- 239000002994 raw material Substances 0.000 claims abstract description 49
- 239000002131 composite material Substances 0.000 claims abstract description 19
- 238000002156 mixing Methods 0.000 claims abstract description 16
- 238000000498 ball milling Methods 0.000 claims abstract description 9
- 239000011812 mixed powder Substances 0.000 claims abstract 2
- 229910045601 alloy Inorganic materials 0.000 claims description 62
- 239000000956 alloy Substances 0.000 claims description 62
- 229910017112 Fe—C Inorganic materials 0.000 claims description 44
- 229910017770 Cu—Ag Inorganic materials 0.000 claims description 21
- 239000002245 particle Substances 0.000 claims description 13
- 238000009826 distribution Methods 0.000 claims description 8
- 229910000640 Fe alloy Inorganic materials 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 26
- 239000010949 copper Substances 0.000 description 23
- 229910052799 carbon Inorganic materials 0.000 description 21
- 230000000052 comparative effect Effects 0.000 description 12
- 229910017827 Cu—Fe Inorganic materials 0.000 description 10
- 238000000034 method Methods 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 229910000881 Cu alloy Inorganic materials 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 229910000906 Bronze Inorganic materials 0.000 description 3
- NIPNSKYNPDTRPC-UHFFFAOYSA-N N-[2-oxo-2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 NIPNSKYNPDTRPC-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 239000010974 bronze Substances 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 3
- 238000012805 post-processing Methods 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 229910052742 iron Inorganic materials 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
- 238000002360 preparation method Methods 0.000 description 2
- 229910052709 silver Inorganic materials 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 241000208340 Araliaceae Species 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 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 1
- 235000005035 Panax pseudoginseng ssp. pseudoginseng Nutrition 0.000 description 1
- 235000003140 Panax quinquefolius Nutrition 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
- 235000008434 ginseng Nutrition 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
- 238000000713 high-energy ball milling Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 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
- 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
- 230000001629 suppression Effects 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- 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 Ag alloys, is prepared by following steps：(1) prepare raw material：The raw material includes Cu Ag prealloy powder and Fe C prealloy powder, (2) ball milling mixing：Abrading-ball is added and carries out mixed powder, obtains 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 Ag 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-Ag 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.
Currently, high-strength highly-conductive Cu-Fe systems alloy mainly utilizes fusion casting to prepare just alloy, 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 the methods of deformation, heat treatment, high-intensity magnetic field, multi-element alloyed, but cannot all solve well
Certainly this problem.Such as：Ag is considered as damaging the minimum element of Cu alloy conductives effect, but utilize Ag to Cu-Fe alloys
The Cu-Fe-Ag alloys of alloying preparation are carried out, but are still dissolved 2.5% or more Fe 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
And it is 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 Cu-Fe-C-Ag alloys.
Invention content
The purpose of the present invention is to provide a kind of Cu-Fe-C-Ag alloys, can efficiently reduce the Fe being dissolved in Cu-, carry
The high 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,
The use temperature range of alloy is improved, and reduces the manufacturing cost of alloy.
To achieve the goals above, the present invention provides the following technical solutions：
A kind of Cu-Fe-C-Ag alloys, Cu-Fe-C-Ag alloys are prepared by following steps：
(1) prepare raw material：Raw material includes Cu-Ag prealloy powder and Fe-C prealloy powder,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree 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 be 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-Ag alloys of Fe-C even particle distributions.
The Cu-Fe-C-Ag alloys prepared by above-mentioned steps are a kind of novel high-strength highly-conductive Cu alloys, and C and Cu is utilized
Mutually exclusive effect in Fe-Cu-C ternary systems, therefore C is added into Cu, and in order to give full play to this work of C
With using Cu-Ag prealloy powder, Fe-C prealloy powder hot pressed sinterings preparation Cu-Fe-C-Ag alloys.Cu-Fe-C-Ag obtained
It is 54%~66%IACS that the tensile strength of alloy, which is more than 570MPa, conductivity,.
In the alloy of the present invention, the grain size of Cu-Ag prealloy powder is 10~50 μm as a preferred implementation manner,.
When the grain size of Cu-Ag prealloy powder is 10~50 μm, Fe-C particles can be more evenly distributed in Cu-Ag matrixes.Fe-C is closed in advance
The size of bronze is (such as 60nm, 70nm, 80nm, 90nm, 100nm, 50nm~80nm, 50nm~70nm, 60 50~120nm
~80nm, 60nm~110nm, 70~80nm, 80~100nm, 100~120nm).The Fe-C alloyed powders are commercial product, when
It so can also conventionally prepare, can be prepared by vacuum atomizing stove, by the raw material iron and carburant of required proportioning
It is atomized into powder particle after melting, is then prepared into the Fe-C alloyed powders of required granularity by high-energy ball milling again.Make in the present invention
Fe-C alloyed powder particle sizes are 50~120nm, Fe-C alloy powder particles it is oversized, can cause disperse and then to cause
Precipitation strength effect reduction；Fe-C alloy powder particles it is undersized, be easy that Fe is made to be dissolved in Cu, electric conductivity be deteriorated, but also
It is easy to happen reunion.
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 energy is bigger simultaneously, is dissolved in the easier matrix to Cu.
In the alloy of the present invention, raw material includes that Cu-Ag prealloy powder and Fe-C are closed in advance as a preferred implementation manner,
Bronze, the Cu-Ag prealloy powder account for the 85-90wt% (such as 86%, 87%, 88%, 89%) of the raw material, the Fe-C
Prealloy powder account for the raw material 10-15wt% such as 11%, 12%, 13%, 14%).
In the alloy of the present invention, the C in the Fe-C prealloy powder accounts for the pre- conjunction as a preferred implementation manner,
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, the Ag contents in the Cu-Ag prealloy powder are as a preferred implementation manner,
0.5~3wt% (such as：0.5wt%, 0.6wt%, 0.7wt%, 0.8wt%, 0.8~1.2wt%, 0.9wt%, 1.0wt%,
1.0~1.2wt%, 1.1wt%, 1.2wt%, 1.3wt%, 1.4wt%, 1.5wt%, 1.6wt%, 1.7wt%, 1.8wt%,
1.9wt%, 2.0wt%, 2.1wt%, 2.2wt%, 2.3wt%, 2.4wt%, 2.5wt%, 2.7wt%, 2.9wt%).Ag contains
Amount is up to 3wt%, effectively reduces the cost of raw material.
In the alloy of the present invention, C content is too low will to lead to have more Fe to dissolve in Cu-Ag matrixes, be led to alloy
Electrically unfavorable, C content is excessively high to form graphite or Fe3C etc..
Further include alloy post-processing step as a preferred implementation manner, in the step of preparing alloy of the present invention, it will
The Cu-Fe-C-Ag systems alloy that (3) the hot pressed sintering step obtains is post-processed, and Cu-Fe-C-Ag systems alloy finished product is obtained.
It is highly preferred that the post-processing is one or more in heat treatment, deformation process, magnetic field processing；The post-processing is conventional
Processing.
Analysis is it is found that a kind of Cu-Fe-C-Ag alloys disclosed by the invention, mainly realize following technique effect：Utilize C
With mutually exclusive effects of the Cu in Fe-Cu-C ternary systems, and Ag ratios Fe is utilized first to be dissolved in Cu, the suppression to Fe solid solutions
It makes and uses, therefore add C and Ag into Cu.And in order to give full play to this effect of C and Ag, using Cu-Ag prealloy powder,
Fe-C prealloy powder hot pressed sinterings prepare Cu-Fe-C-Ag alloys, have developed novel high-strength highly-conductive Cu alloys.
Ag ratios Fe is utilized first to be dissolved in Cu, to the inhibiting effect of Fe solid solutions, controls diffusions of the Fe into Cu matrixes, greatly
Width reduces the solid solution capacity of Fe in Cu-Ag matrixes.The method of the present invention can improve the conductivity and tensile strength of Cu-Fe alloys, obtain
The tensile strength of the alloy arrived is more than 570MPa, conductivity 54-66%IACS.
Specific implementation mode
Below in conjunction with embodiment, the present invention will be described in detail.The mode of the explanation of each example through the invention provide and
The unrestricted present invention.In fact, those skilled in the art will be clear that, the case where 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 include be included into appended claims and
Such modifications and variations in the range of its equivalent.
Embodiment 1
(1) prepare raw material：Raw material includes 10~50 μm of Cu-Ag prealloy powder and the Fe- that size is 70~120nm
1.2wt%C prealloy powder, the mass percent of C is 1.2wt% in Fe-C alloy powders, and Cu accounts for the 88.5wt% of the raw material,
Ag accounts for the 0.5wt% of the raw material, and Fe-C prealloy powder accounts for the 11wt% of the raw material,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree is 900 DEG C, sintering pressure 50MPa, sintering time 30min,
Cu-11wt% (Fe-C) -0.5wt%Ag alloys 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 603MPa, and conductivity is
62.8%IACS.
Embodiment 2
(1) prepare raw material：Raw material includes 10~50 μm of Cu-Ag prealloy powder and the Fe- that size is 70~120nm
1.0wt%C prealloy powder, the mass percent of C is 1.0wt% in Fe-C alloy powders, and Cu accounts for the 84.5wt% of the raw material,
Ag accounts for the 0.5wt% of the raw material, and Fe-C prealloy powder accounts for the 15wt% of the raw material,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree is 800 DEG C, sintering pressure 50MPa, sintering time 30min,
Cu-15wt% (Fe-C) -0.5wt%Ag alloys 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 678MPa, and conductivity is
57.6%IACS.
Embodiment 3
(1) prepare raw material：Raw material includes 10~50 μm of Cu-Ag prealloy powder and the Fe- that size is 50~80nm
1.1wt%C prealloy powder, the mass percent of C is 1.1wt% in Fe-C alloy powders, and Cu accounts for the 86.5wt% of the raw material,
Ag accounts for the 0.5wt% of the raw material, and Fe-C prealloy powder accounts for the 13wt% of the raw material,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree is 820 DEG C, sintering pressure 50MPa, sintering time 30min,
Cu-13wt% (Fe-C) -0.5wt%Ag alloys 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 664MPa, and conductivity is
58.6%IACS.
Embodiment 4
(1) prepare raw material：Raw material includes 10~50 μm of Cu-Ag prealloy powder and the Fe- that size is 50~80nm
1.1wt%C prealloy powder, the mass percent of C is 1.1wt% in Fe-C alloy powders, and Cu accounts for the 89.5wt% of the raw material,
Ag accounts for the 0.5wt% of the raw material, and Fe-C prealloy powder accounts for the 10wt% of the raw material,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree is 820 DEG C, sintering pressure 50MPa, sintering time 30min,
Cu-10wt% (Fe-C) -0.5wt%Ag alloys 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 605MPa, and conductivity is
60.5%IACS.
Embodiment 5
(1) prepare raw material：Raw material includes 10~50 μm of Cu-Ag prealloy powder and the Fe- that size is 50~80nm
1.1wt%C prealloy powder, the mass percent of C is 1.1wt% in Fe-C alloy powders, and Cu accounts for the 88.5wt% of the raw material,
Ag accounts for the 0.5wt% of the raw material, and Fe-C prealloy powder accounts for the 11wt% of the raw material,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree is 820 DEG C, sintering pressure 50MPa, sintering time 30min,
Cu-11wt% (Fe-C) -0.5wt%Ag alloys that Fe-1.1wt%C even particle distributions must have been prepared, that is, exist
The content of Fe-C is 11wt% in alloy.
The alloy prepared to the embodiment is tested for the property, and the tensile strength of alloy is 618MPa, conductivity 64%
IACS。
Embodiment 6
(1) prepare raw material：Raw material includes 10~50 μm of Cu-Ag prealloy powder and the Fe- that size is 60~80nm
1.1wt%C prealloy powder, the mass percent of C is 1.1wt% in Fe-C alloy powders, and Cu accounts for the 87.5wt% of the raw material,
Ag accounts for the 0.5wt% of the raw material, and Fe-C prealloy powder accounts for the 12wt% of the raw material,
(2) ball milling mixing：Abrading-ball is added and carries out powder mixing machine, obtains 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
Degree is 820 DEG C, sintering pressure 50MPa, sintering time 30min,
Cu-12wt% (Fe-C) -0.5wt%Ag alloys 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 642MPa, conductivity 58%
IACS。
Embodiment 7-11 and comparative example 1-2
Embodiment 7-11 and comparative example 1-3 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 7-11 and comparative example 1-3 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, the performance of embodiment 7,8,9,10,11
(tensile strength and conductivity) is significantly better than comparative example 1,2 and 3.
The raw material dosage relationship and raw material granularity and corresponding product performance table of table 1 embodiment 7-11 and comparative example 1-3
Embodiment 12-16
For embodiment 12-16 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 12-16 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 12,13,14 is significantly better than embodiment 15,16.
The hot pressed sintering condition and properties of product table of 2 embodiment 12-16 of table
Embodiment 17-18 and comparative example 4
Embodiment 17-18 and comparative example 4 are other than the content of Ag simple substance in alloy is different from embodiment 1, other techniques
Parameter is the same as embodiment 1.The content of Ag simple substance and the performance of obtained alloy ginseng in embodiment 17-18 and the alloy of comparative example 4
It is shown in Table 3.As can be seen from Table 3, as the ratio of Ag increases in comparative example 4, tensile strength and conductivity all obviously do not improve.
The technological parameter and results of property of table 3 embodiment 17-18 and comparative example 4
Claims (10)
1. a kind of Cu-Fe-C-Ag alloys, which is characterized in that the Cu-Fe-C-Ag alloys are prepared by following steps：
(1) prepare raw material：The raw material includes Cu-Ag prealloy powder and Fe-C prealloy powder,
(2) ball milling mixing：Abrading-ball is added and carries out mixed powder, obtains 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
Degree is 800~1000 DEG C, and sintering pressure is 45~55MPa, and sintering time is 30min~45min,
Obtain the Cu-Fe-C-Ag alloys of Fe-C even particle distributions.
2. alloy according to claim 1, which is characterized in that the grain size of the Cu-Ag prealloy 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 50~80nm.
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 Cu-Ag prealloy powder accounts for the 85- of the raw material
90wt%, the Fe-C prealloy powder account for the 10-15wt% of the raw material.
8. alloy according to claim 1, which is characterized in that C content in the Fe-C prealloy powder is 0.8~
1.2wt%.
9. alloy according to claim 1, which is characterized in that C content in the Fe-C prealloy powder is 1.0~
1.2wt%.
10. alloy according to claim 1, which is characterized in that Ag contents in the Cu-Ag prealloy powder are 0.5~
3wt%.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810259079.8A CN108374103B (en) | 2018-03-27 | 2018-03-27 | Cu-Fe-C-Ag alloy |
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| Application Number | Priority Date | Filing Date | Title |
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| CN201810259079.8A CN108374103B (en) | 2018-03-27 | 2018-03-27 | Cu-Fe-C-Ag alloy |
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| CN108374103A true CN108374103A (en) | 2018-08-07 |
| CN108374103B CN108374103B (en) | 2019-10-29 |
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| US3401024A (en) * | 1965-10-04 | 1968-09-10 | Mallory & Co Inc P R | Electrical contact material |
| CN1687479A (en) * | 2005-06-09 | 2005-10-26 | 上海交通大学 | Method for preparing composite Cu-Fe-Ag nano material at original position with high intensity and high conductance |
| CN104263985A (en) * | 2014-09-24 | 2015-01-07 | 西安理工大学 | Preparation method of self-hard reinforced Cu-FeC composite material |
| CN105839038A (en) * | 2016-04-08 | 2016-08-10 | 东北大学 | Preparation method for high-strength high-conductivity Cu-Ag-Fe alloy |
| CN107267802A (en) * | 2016-03-31 | 2017-10-20 | Ｊｘ金属株式会社 | The manufacture method of copper alloy plate and copper alloy plate |
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2018
- 2018-03-27 CN CN201810259079.8A patent/CN108374103B/en not_active Expired - Fee Related
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| US3401024A (en) * | 1965-10-04 | 1968-09-10 | Mallory & Co Inc P R | Electrical contact material |
| CN1687479A (en) * | 2005-06-09 | 2005-10-26 | 上海交通大学 | Method for preparing composite Cu-Fe-Ag nano material at original position with high intensity and high conductance |
| CN104263985A (en) * | 2014-09-24 | 2015-01-07 | 西安理工大学 | Preparation method of self-hard reinforced Cu-FeC composite material |
| CN107267802A (en) * | 2016-03-31 | 2017-10-20 | Ｊｘ金属株式会社 | The manufacture method of copper alloy plate and copper alloy plate |
| CN105839038A (en) * | 2016-04-08 | 2016-08-10 | 东北大学 | Preparation method for high-strength high-conductivity Cu-Ag-Fe alloy |
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| Title |
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| ZHIXIONG XIE,ET AL.: "Effect of Ag addition on the as-cast microstructure of Cu–8 wt.% Fe in situ composites", 《JOURNAL OF ALLOYS AND COMPOUNDS》 * |
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