CN107739883A - Cu Ni Be alloy thermo-mechanical processi reinforcement process - Google Patents
Cu Ni Be alloy thermo-mechanical processi reinforcement process Download PDFInfo
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- 238000000034 method Methods 0.000 title claims abstract description 56
- 229910000952 Be alloy Inorganic materials 0.000 title claims abstract description 51
- 230000002787 reinforcement Effects 0.000 title claims abstract description 34
- 230000000930 thermomechanical effect Effects 0.000 title claims abstract description 14
- 239000000956 alloy Substances 0.000 claims abstract description 33
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 32
- 238000001816 cooling Methods 0.000 claims abstract description 23
- 238000001192 hot extrusion Methods 0.000 claims abstract description 20
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 18
- 230000032683 aging Effects 0.000 claims abstract description 17
- 238000007731 hot pressing Methods 0.000 claims abstract description 9
- 238000011282 treatment Methods 0.000 claims abstract description 8
- JEGUKCSWCFPDGT-UHFFFAOYSA-N h2o hydrate Chemical compound O.O JEGUKCSWCFPDGT-UHFFFAOYSA-N 0.000 claims abstract description 6
- 238000010438 heat treatment Methods 0.000 claims abstract description 5
- 238000005242 forging Methods 0.000 claims description 15
- 238000005266 casting Methods 0.000 claims description 10
- 238000009740 moulding (composite fabrication) Methods 0.000 claims description 6
- 229910017532 Cu-Be Inorganic materials 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 238000001556 precipitation Methods 0.000 abstract description 6
- 230000003014 reinforcing effect Effects 0.000 abstract description 4
- 239000010949 copper Substances 0.000 description 14
- 238000003483 aging Methods 0.000 description 10
- 239000011159 matrix material Substances 0.000 description 10
- 229910000881 Cu alloy Inorganic materials 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 239000000047 product Substances 0.000 description 7
- 239000006104 solid solution Substances 0.000 description 5
- 230000007547 defect Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 230000003321 amplification Effects 0.000 description 3
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- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000003199 nucleic acid amplification method Methods 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000004807 desolvation Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002524 electron diffraction data Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000012010 growth Effects 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000000101 transmission high energy electron diffraction Methods 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000009194 climbing Effects 0.000 description 1
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- 238000005260 corrosion Methods 0.000 description 1
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- 230000005307 ferromagnetism Effects 0.000 description 1
- 238000000024 high-resolution transmission electron micrograph Methods 0.000 description 1
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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
-
- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- 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
Abstract
The invention discloses a kind of Cu Ni Be alloy thermo-mechanical processi reinforcement process：Cu Ni Be alloy cast ingots are heated to 960~980 DEG C, are incubated 60~180min；30~60% hot-pressed, hot extrusion 0.05~1m/s of speed are carried out again, then water cooling, billet enters coolant-temperature gage not less than 950 DEG C after hot extrusion, and circulating water water temperature is no more than 30 DEG C；470 DEG C × 3h Ageing Treatments are finally carried out, then air cooling, you can.It is an advantage of the invention that：According to the reinforcing general principle of Cu Ni Be alloy products, design heating, hot extrusion or hot pressing, water cooling, the integrated processing technique of timeliness, the further precipitation of alloy aging precipitated phase is promoted, precipitated phase is more tiny, uniform, disperse, and alloy has good combination property；Reinforcement process of the present invention, simplify processing step, save cost, while alloy is obtained good combination property.
Description
Technical field
The present invention relates to a kind of high reinforcement process for leading high-strength copper alloy, particularly a kind of reinforcing work of Cu-Ni-Be alloys
Skill.
Background technology
High-strength high-conductive copper alloy both has high intensity and good plasticity, but also with excellent conduction, heat conduction
Property, corrosion resistance, without ferromagnetism, color and luster is beautiful, there is extensive purposes in modern industry.Common height leads high-strength copper alloy
Mainly leaded framework copper alloy, electrical contact are with copper alloy, electric railway copper alloy for contact line etc. for type, schedule of reinforcement
Typically there are alloying and composite method.
Conventional Cu-Ni-Be alloy products, production technology are ingot casting forging+solid solution+water cooling+cold deformation+timeliness, technique
Process is grown, and the metallograph after alloy solid solution Ageing Treatment is as shown in Figure 1；And because technological process is complicated in production process,
Add the production cost of product.
The content of the invention
Goal of the invention：In view of the above-mentioned problems, it is an object of the invention to provide a kind of reinforcing work for Cu-Ni-Be alloys
Skill, optimization design product processes process, form the manufacturing technique method new to Cu-Ni-Be alloy products.
Technical scheme：A kind of Cu-Ni-Be alloys thermo-mechanical processi reinforcement process, comprises the following steps：
Step 100：Cu-Ni-Be alloy cast ingots are heated to 960~980 DEG C, are incubated 60~180min；
Step 200：Ingot casting progress 30~60% after step 100 is handled is hot-pressed, and hot extrusion speed 0.05~
1m/s, then water cooling, billet enters coolant-temperature gage not less than 950 DEG C after hot extrusion, and circulating water water temperature is no more than 30 DEG C；
Step 300：Billet after step 200 is handled carries out 470 DEG C × 3h Ageing Treatments, then air cooling, you can.
Further, in step 100, before the heating of Cu-Ni-Be alloy cast ingots, ingot casting is first formed into forging stock after hot forging.
When forming forging stock, in step 200, it is hot-pressed or hot that the forging stock after step 100 is handled carries out 30~60%
Pressing formation, hot extrusion speed or hot pressing 0.05~1m/s of speed, then water cooling, billet enters coolant-temperature gage not after hot extrusion or hot pressing
Less than 950 DEG C, circulating water water temperature is no more than 30 DEG C.
When forming forging stock, optimal, forging stock is round billet or square billet.
Further, in step 100, the rate of heat addition is 10 DEG C/min.
Further, the Cu-Ni-Be alloys, Ni are added with pure Ni, and Be is added with Cu-Be intermediate alloys, and alloy exists
Melting in non-vacuum induction furnace, antivacuum casting form.
Further, the composition of the Cu-Ni-Be alloys is Ni 1.9wt%, Be 0.38wt%, impurity is no more than
0.1wt%, surplus Cu.
Further, hot extrusion deformation equipment is JH23-63 types in step 200.
The present invention principle be：To Cu-Ni-Be alloys using heating, hot extrusion or hot pressing, the integration of water cooling, timeliness
Handling process, there is significant ageing strengthening characteristic after alloy aging：Supersaturated solid solution → G-P areas (or γ ＂) → γ ' (mistakes
Cross phase) → γ (stable phase).The implementation of reinforcement process, deflection and deformation velocity are controlled, ensure that alloy enters coolant-temperature gage and cold
But, abundant refining alloy crystal grain, the precipitation of ageing strengthening phase is effectively controlled, alloy is obtained good combination property.
Beneficial effect：Compared with prior art, it is an advantage of the invention that：According to the reinforcing base of Cu-Ni-Be alloy products
Present principles, design heating, hot extrusion or hot pressing, water cooling, the integrated processing technique of timeliness, promote alloy aging precipitated phase
Further precipitation, precipitated phase is more tiny, uniform, disperse, and alloy has good combination property；Reinforcement process of the present invention,
Simplify processing step, save cost, while alloy is obtained good combination property.
Brief description of the drawings
Fig. 1 is metallograph of the Cu-Ni-Be alloys after fixation rates in the prior art；
Fig. 2 (a) is images of transmissive electron microscope-low power high score that the reinforcement process of example 1 handles Cu-Ni-Be alloy samples by contrast
Distinguish image (HRTEM)；
Fig. 2 (b) by contrast the reinforcement process of example 1 processing Cu-Ni-Be alloy samples images of transmissive electron microscope-corresponding constituency
Electron diffraction pattern (SADP), incident axle is parallel to [001]α；
Fig. 2 (c) is images of transmissive electron microscope-precipitated phase that the reinforcement process of example 1 handles Cu-Ni-Be alloy samples by contrast
One of amplification full resolution pricture of grain, it is labelled with the dimensional structure of precipitated phase；
Fig. 2 (d) is images of transmissive electron microscope-precipitated phase that the reinforcement process of example 1 handles Cu-Ni-Be alloy samples by contrast
The two of the amplification full resolution pricture of grain, it is labelled with the dimensional structure of precipitated phase；
Fig. 2 (e) is images of transmissive electron microscope-precipitated phase that the reinforcement process of example 1 handles Cu-Ni-Be alloy samples by contrast
The distributional pattern schematic diagram of grain in space；
Fig. 3 (a) is images of transmissive electron microscope-low power high score of the Cu-Ni-Be alloy samples handled through reinforcement process of the present invention
Distinguish image (HRTEM)；
Fig. 3 (b) is images of transmissive electron microscope-corresponding choosing of the Cu-Ni-Be alloy samples handled through reinforcement process of the present invention
Area's electron diffraction pattern (SADP), incident axle is parallel to [110]α；
Fig. 3 (c) is images of transmissive electron microscope-single amplification of the Cu-Ni-Be alloy samples handled through reinforcement process of the present invention
γ " phase morphologies；
Fig. 3 (d) is fast Fourier (FFT) image corresponding to Fig. 3 (c), and incident axle is parallel to [110]α；
Fig. 3 (e) is images of transmissive electron microscope-different zones of the Cu-Ni-Be alloy samples handled through reinforcement process of the present invention
One of individual layer plate-like G-P areas pattern separated out along { 111 } slide surface；
Fig. 3 (f) is images of transmissive electron microscope-different zones of the Cu-Ni-Be alloy samples handled through reinforcement process of the present invention
One of individual layer plate-like G-P areas pattern separated out along { 111 } slide surface；
Fig. 4 is the metallograph of the Cu-Ni-Be alloys handled through reinforcement process of the present invention.
Embodiment
Below in conjunction with the accompanying drawings and specific embodiment, the present invention is furture elucidated.
Embodiment 1
A kind of Cu-Ni-Be alloys thermo-mechanical processi reinforcement process, specifically includes following steps：
Step 100：Cu-Ni-Be alloy cast ingots are heated to 960~980 DEG C, the rate of heat addition is 10 DEG C/min, Ran Houbao
60~180min of temperature；
Step 200：Ingot casting progress 30~60% after step 100 is handled is hot-pressed, and hot extrusion speed 0.05~
1m/s, then water cooling, billet enters coolant-temperature gage not less than 950 DEG C after hot extrusion, and circulating water water temperature is no more than 30 DEG C；
Step 300：Billet after step 200 is handled carries out 470 DEG C × 3h Ageing Treatments, then air cooling, you can.
Embodiment 2
A kind of Cu-Ni-Be alloys thermo-mechanical processi reinforcement process, specifically includes following steps：
Step 100：Cu-Ni-Be alloy cast ingots are first subjected to hot forging, form circular or square forging stock, then forging stock will
960~980 DEG C are heated to, the rate of heat addition is 10 DEG C/min, is then incubated 60~180min；
Step 200：Forging stock after step 100 is handled carries out 30~60% hot-pressed or hot formings, hot extrusion
Speed or hot pressing 0.05~1m/s of speed, then water cooling, billet enters coolant-temperature gage not less than 950 DEG C after hot extrusion or hot pressing, circulation
Water cooling water temperature is no more than 30 DEG C；
Step 300：Billet after step 200 is handled carries out 470 DEG C × 3h Ageing Treatments, then air cooling, you can.
In embodiment 1,2, raw material Cu-Ni-Be alloy cast ingots, composition is Ni 1.9wt%, Be 0.38wt%, impurity
Added no more than 0.1wt%, surplus Cu, Ni with pure Ni, Be is added with Cu-Be intermediate alloys, and alloy is in non-vacuum induction furnace
Melting, antivacuum casting form.Hot extrusion deformation equipment is JH23-63 types.
Influence of the thermal deformation to alloy is studied in terms of two below.
In addition to casting and sintered part, almost all of metal material must add during finished product is made through overheat
Work, and either intermediate step or final process, metal is after hot-working, and it is organized and performance will necessarily be to final
Properties of product are brought greater impact.Cu-Ni-Be alloys belong to low stacking fault energy metal, due to their extended dislocation width
It is very wide, it is difficult to by climbing to carry out dynamic recovery for commutative Banach aglebra and edge dislocation, therefore the tendency of dynamic recrystallization to occur
Greatly.By carrying out Experimental comparison in identical heat distortion temperature difference heat distortion amount and identical heat distortion amount difference heat distortion temperature.
1st, influence of the heat distortion amount to alloy property and tissue
Heat distortion amount is 0%, 15%, 30%, 45%, 60% and 75% and then+470 DEG C of water cooling × 3h timeliness, then surveys
Its hardness and conductance.Its performance such as table 1：
Influence of the 1 different heat distortion amounts of table to Cu-Ni-Be alloy properties
| Specimen coding | A# | B# | C# | D# | E# | F# |
| Temperature | 980℃ | 980℃ | 980℃ | 980℃ | 980℃ | 980℃ |
| Deflection | 0% | 15% | 30% | 45% | 60% | 75% |
| Hardness (HB) | 262 | 272 | 276 | 271 | 267 | 263 |
| Conductance (Ms/m) | 28.1 | 28.2 | 28.2 | 27.2 | 27.8 | 28.1 |
2nd, influence of the heat distortion temperature to alloy property and tissue
Heat distortion temperature is set as 900 DEG C, 920 DEG C, 940 DEG C, 960 DEG C, 980 DEG C and 1000 DEG C, to temperature after be incubated, pass through
Water quenching after 30% thermal deformation, air cooling after 470 DEG C × 3h timeliness is carried out, then survey conductance and hardness.Its performance such as table 2：
Influence of the different heat distortion temperature of table 2 to the performance of Cu-Ni-Be alloys
| Specimen coding | 1# | 2# | 3# | 4# | 5# | 6# |
| Technique (DEG C) | 900 | 920 | 940 | 960 | 980 | 1000 |
| Hardness (HB) | 171 | 206 | 237 | 259 | 276 | 186 |
| Conductance (Ms/m) | 31.8 | 31.2 | 30.4 | 29.6 | 28.2 | 26.6 |
To sum up, Cu-Ni-Be alloys carry out+470 DEG C of water cooling × 3h timeliness again after thermal deformation through 980 DEG C of insulations, alloy properties
Can after than 980 DEG C direct solid solution agings alloy performance it is superior, in 30% deflection, the hardness of alloy is 276HB, conductive
Rate is 28.2Ms/m.
Comparative example
A kind of traditional reinforcement process of Cu-Ni-Be alloys：Cu-Ni-Be alloys are first carried out to 980 DEG C × 1h Ageing Treatments,
Then water cooling, then carry out 470 DEG C × 3h Ageing Treatments, last air cooling.
The Precipitation process of Cu-Be bianry alloys, which is generally believed that, is divided into 4 stages：Guinier-Preston(G-P)
Area → γ " → γ ' → stabilization γ.G.P. area is by parallel to { 100 }αThe individual layer plate-like Be atoms composition of Cu matrixes.Metastable
γ ", γ ' and γ precipitated phases have CuBe structure, and are alternatively formed by Be, Cu atom.It is certain when being added into the alloy system
During the Ni of amount, Age-prrcipitation Phase becomes the sheet hardening constituent that Be, Ni atom are alternatively formed, the desolvation process class with Cu-Be alloys
Seemingly, four-stage is also classified into, under the handling process of routine, the individual layer Be atom enrichment regions that preferentially form, i.e. G-P areas are parallel
In { 100 } of supersaturated Cu matrixesαFamily of crystal planes, with the extension of soaking time, metastable γ " Xiang G-P areas forming core is grown up,
Multilayer chip tissue is developed into, there is body-centered structure of the quartet (bct), Ni atoms occupy the position of body-centered.
For embodiment 1,2 and comparative example, the hard of beta alloy is distinguished with hardometer, vortex conductivity test instrument respectively
Degree and conductance, with the tissue of metallography microscope sem observation alloy, by transmission electron microscope diffraction, analyze its microstructure and precipitation
Phase.
Under comparative example reinforcement process, Fig. 2 (a)-(e) is given under the technique, the microstructure of Age-prrcipitation Phase.By attached
Fig. 2 (a) is visible, and even dispersion is dispersed with a large amount of strip particles on matrix；From accompanying drawing 2 (b), precipitated phase particle and Cu
The orientation relationship of matrix is：(110)p//(200)α；[001]p//[001]α, i.e., (110)p//(100)α；[001]p//[001]α,
Used analysis face is { 100 }αFamily of crystal planes；By accompanying drawing 2 (c), the high power HRTEM images of the metastable precipitate of accompanying drawing 2 (d), incident electron
[001] of the beam parallel to matrixαDirection, the i.e. plane parallel to paper are Cu matrixes (002) faces, it can be seen that are substantially deposited
In the precipitated phase particle of two orthogonal growths, precipitated phase length is between 8~14nm, and precipitated phase is mainly by 4 layers of Be originals
Son composition, thickness is about 1nm.Precipitated phase particle actually exists in 3 directions in matrix space, i.e. (001) face of precipitated phase point
It is not coplanar parallel to three etc. of (200) of matrix, (020) and (002), shown in the schematic diagram such as accompanying drawing 2 (e) of spatial distribution,
It is defined as γ "1、γ″2With γ "3, the form in accompanying drawing 2 (d) corresponds to γ "1, the orientation relationship with Cu matrixes is：
(001)p//(020)α,(110)p//(200)α；That is (001)p//(010)α,(110)p//(100)α；
[110]p//[001]α.Distribution of the precipitated phase of three kinds of forms in space is all of equal value, i.e., used analysis face is { 100 }α.It is dissolved water
In cold process, it can retain room is formed under high temperature to room temperature, it is less that vacancy defect can preferentially be distributed in elastic strain energy
On crystal face, for the Cu alloy materials of face-centred cubic structure, vacancy defect can precedence partition in its { 100 } family of crystal planes direction, because
And in later stage timeliness desolvation process, solute atoms can form G-P areas preferentially in the high position enrichment of vacancy concentration, and gradually grow
Big γ ", the γ ' and γ phases for forming sheet, with growing up for precipitated phase, the edge of precipitated phase and the coherence degree of matrix drop
Low, the invigoration effect of coherency stress field decreases, and shows as the reduction of alloy rigidity.
Reinforcement process of the present invention is carried out after solid solution holding stage terminates with large-scale pressing equipment to hot alloy sample
Once instantaneous thermal deformation, water cooling immediately after deformation terminates, then carries out timeliness isothermal holding again.For the Cu of face-centred cubic structure
Alloy, { 111 } family of crystal planes are its slip directions, alloy substrate slide surface preferential motion in thermal deformation process, and along with big
The formation of vacancy defect is measured, subsequent quick cooling, these vacancy defects can be retained to room temperature texture.Fig. 3 (a)-(f) gives
Go out under reinforcement process of the present invention, the microscopic pattern of precipitated phase, the electron beam incident direction of each figure is each parallel to [110]α.
In Fig. 3 (a) can simultaneously observe parallel to (002) γ " mutually and parallel toG-P district's groups knit, the former length exists
Between 7~18nm, the length of the latter is about 9nm；Fig. 3 (b) is corresponding SEAD style, does not observe precipitated phase
Diffraction spot, but obvious satellite spots can be observed near matrix spot, represent to exist in oversaturated Cu matrixes obvious
Segregation solute atom area, make matrix lattice index occur skew.Fig. 3 (c) gives a double-layer structure γ " phase constitution,
Length is about 15nm, and thickness is about 0.4nm, and complete coherence state, fast Fourier (FFT) figure in the region are kept with matrix
Orientation relationship of the picture, it may be determined that γ " mutually with Cu matrixes be：I.e.Fig. 3 (e), (f) give different zones along { 111 } slide surface
There are two kinds of forms in the individual layer plate-like G-P areas pattern of precipitation, G-P areas, one kind is that short tufted is organized in flakes, and another kind is single
Strip tissue, complete coherence form is kept with matrix, the coherency stress field of formation is very big, and the macroscopic view for showing as alloy is hard
Degree reaches a peak value.Compared with direct aging sample, under identical aging technique, precipitated phase is grown up smaller, heat
Deformation process makes Cu alloys have very high vacancy concentration on { 111 } slide surface, ageing impact toughness, and a large amount of solute atoms are preferential
Quickly being separated out on each face of { 111 }, the degree of supersaturation of Cu matrixes declines, and the driving force that precipitated phase is grown up reduces, meanwhile,
The solute atoms preferentially separated out is largely distributed on { 111 } family of crystal planes, and the γ " formed is mutually still distributed in { 100 } of Cu matrixes
On used analysis face, the energy increase of atoms permeating, so as to delay the growth process of γ " phases.And this { 111 } face G.P. areas and
{ 100 } the mutually simultaneous microstructures of face γ ", very high coherency stress field is formed, Cu matrixes is obtained highest and strengthen effect
Fruit.
Claims (8)
1. a kind of Cu-Ni-Be alloys thermo-mechanical processi reinforcement process, it is characterised in that comprise the following steps：
Step 100：Cu-Ni-Be alloy cast ingots are heated to 960~980 DEG C, are incubated 60~180min；
Step 200：Ingot casting after step 100 is handled carries out 30~60% hot-pressed, hot extrusion 0.05~1m/s of speed,
Then water cooling, billet enters coolant-temperature gage not less than 950 DEG C after hot extrusion, and circulating water water temperature is no more than 30 DEG C；
Step 300：Billet after step 200 is handled carries out 470 DEG C × 3h Ageing Treatments, then air cooling, you can.
2. Cu-Ni-Be alloys thermo-mechanical processi reinforcement process according to claim 1, it is characterised in that：In step 100,
Before the heating of Cu-Ni-Be alloy cast ingots, ingot casting is first formed into forging stock after hot forging.
3. Cu-Ni-Be alloys thermo-mechanical processi reinforcement process according to claim 2, it is characterised in that：In step 200,
Forging stock after step 100 is handled carries out 30~60% hot-pressed or hot formings, hot extrusion speed or or hot pressing speed
0.05~1m/s, then water cooling, billet enters coolant-temperature gage not less than 950 DEG C after hot extrusion or hot pressing, and circulating water water temperature does not surpass
Cross 30 DEG C.
4. Cu-Ni-Be alloys thermo-mechanical processi reinforcement process according to claim 2, it is characterised in that：Forging stock is round billet
Or square billet.
5. Cu-Ni-Be alloys thermo-mechanical processi reinforcement process according to claim 1, it is characterised in that：In step 100,
The rate of heat addition is 10 DEG C/min.
6. Cu-Ni-Be alloys thermo-mechanical processi reinforcement process according to claim 1, it is characterised in that：The Cu-Ni-
Be alloys, Ni are added with pure Ni, and Be is added with Cu-Be intermediate alloys, alloy melting in non-vacuum induction furnace, antivacuum casting
Form.
7. Cu-Ni-Be alloys thermo-mechanical processi reinforcement process according to claim 1, it is characterised in that：The Cu-Ni-
The composition of Be alloys is Ni 1.9wt%, Be 0.33wt%, impurity are no more than 0.1wt%, surplus Cu.
8. the Cu-Ni-Be alloy thermo-mechanical processi reinforcement process according to claim 1 or 3, it is characterised in that：Step 200
Middle hot extrusion deformation equipment is JH23-63 types.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010280984A (en) * | 2009-06-08 | 2010-12-16 | Miyoshi Gokin Kogyo Kk | Method for producing copper alloy used as sliding material for motor |
| CN102383078A (en) * | 2011-11-10 | 2012-03-21 | 中色（宁夏）东方集团有限公司 | Preparation method of high-strength and high-conductivity beryllium copper alloy |
| CN102418003A (en) * | 2011-11-24 | 2012-04-18 | 中铝洛阳铜业有限公司 | Processing method of nickel-chromium-silicon-bronze alloy |
| JP2014080646A (en) * | 2012-10-15 | 2014-05-08 | Yazaki Corp | Alloy material for terminal production, production method of the same, terminal, and production method of the same |
| CN105936983A (en) * | 2016-06-24 | 2016-09-14 | 河南江河机械有限责任公司 | High-strength and high-conductivity copper alloy material |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010280984A (en) * | 2009-06-08 | 2010-12-16 | Miyoshi Gokin Kogyo Kk | Method for producing copper alloy used as sliding material for motor |
| CN102383078A (en) * | 2011-11-10 | 2012-03-21 | 中色（宁夏）东方集团有限公司 | Preparation method of high-strength and high-conductivity beryllium copper alloy |
| CN102418003A (en) * | 2011-11-24 | 2012-04-18 | 中铝洛阳铜业有限公司 | Processing method of nickel-chromium-silicon-bronze alloy |
| JP2014080646A (en) * | 2012-10-15 | 2014-05-08 | Yazaki Corp | Alloy material for terminal production, production method of the same, terminal, and production method of the same |
| CN105936983A (en) * | 2016-06-24 | 2016-09-14 | 河南江河机械有限责任公司 | High-strength and high-conductivity copper alloy material |
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