CN106435250A - Machinable copper base alloy and production method thereof - Google Patents

Machinable copper base alloy and production method thereof Download PDF

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CN106435250A
CN106435250A CN201610288541.8A CN201610288541A CN106435250A CN 106435250 A CN106435250 A CN 106435250A CN 201610288541 A CN201610288541 A CN 201610288541A CN 106435250 A CN106435250 A CN 106435250A
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alloy
product
briquet
hour
subsequently
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N.德沃布罗托
D.埃姆普尔
L.费尔伯鲍姆
V.拉波特
A.莫尔滕森
A.罗索尔
E.樊尚
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Swiss Metal -Ums Swiss Metal Processing Ltd
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Priority claimed from CN2009801591773A external-priority patent/CN102439182A/en
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    • 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
    • C22C9/02—Alloys based on copper with tin as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • 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
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/08—Alloys based on copper with lead 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
    • C22F1/08—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

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

The invention discloses a machinable copper base alloy. The machinable copper base alloy comprises 1-20 wt% of Ni, 1-20 wt% of Sn and 0.5-3 wt% of Pb in copper; and Cu is at least 50 wt% of the alloy. The alloy is characterized by further comprising 0.01-5 wt% of single or integrated P or B. The invention further relates to a metal product with reinforced mechanical resistance and excellent machinability at a medium temperature (300-700 DEG C). The metal product can be used for manufacturing connectors, electric mechanical workpieces or micro mechanical workpieces.

Description

Machinable acid bronze alloy and its method of production
The application is Application No. 200980159177.3（PCT/EP2009/054250）, filing date April 8 in 2009 The divisional application of the application for a patent for invention of day.
Technical field
The present invention relates to the alloy based on copper, nickel, tin, lead, and its production method.Especially, although be not exclusive Ground, the present invention relates to the alloy based on copper, nickel, tin, lead being processed easily by turning, cutting or milling.
Background technology
Alloy based on copper, nickel and tin is known and widely used.They provide excellent mechanical performances and Strong hardening is demonstrated during strain hardening.Their mechanical performance is processed such as metastable further by known heat ageing State decomposition improves.For the alloy of the tin (standard alloy ASTM C72900) of the nickel containing 15wt% and 8wt%, machinery Resistance can reach 1500 MPa.These alloys also provide for good proof stress slackness and aerial highly corrosion resistant.
The another advantage of these materials is their excellent formability, has concurrently and is brought by their high yield stress Favourable elastic characteristic.Additionally, these alloys provide good corrosion resistance and excellent heat-resisting slackness.For that reason, Cu- Ni-Sn spring will not lose their compression stress with advancing age, even under vibrations and Gao Re or stress.
These favourable performances, also have good thermal conductivity and electrical conductivity concurrently, it is meant that these materials are widely used for manufacturing Highly reliable connector used by communication and auto industry.These alloys are also used for switch and electric or electromechanical equipment or use Make the carrier of electronic unit or for manufacturing the bearing friction surface standing high load capacity.
Good mechanical processability in these alloys is typically by adding what lead obtained, and the latter is to exist as inclusion Fine dispersion in alloy substrate and be distributed.Unfortunately, this interpolation of lead also can increase significantly alloy heat lack Falling into (warm shortness), this can cause problem in processing and use.
The loss of the ductility of Cu base alloy under moderate temperature (300 DEG C-700 DEG C) is long-term known problem and By R. V. Foulger and E. Nicholls at " Metals Technology " 3, the 366-369 page (1976) neutralize by V. Laporte and A. Mortensen is at " International Materials Reviews ", in printing in (2009) It is reviewed.The starting of grain boundary sliding in this temperature range can cause space and cavity on grain boundary Formed and the usual ductile fracture by copper and its alloy is changed into intercrystalline brittleness and destroyed.Observe this for fine copper Plant phenomenon, but this phenomenon will be apparent from much when embrittled alloys element or impurity element are present in this alloy.More At a temperature of Gao, exceeding this critical range, dynamic recrystallization can recover ductility.
Melted existence in this Cu-alloy for the Pb inclusion can cause Liquid Metal Embrittlement (LME), especially should high Under variable Rate.Meanwhile, the lead content of as little as 18 ppm it is reported can the grain boundary of brittle Cu-Ni alloy, and 800 The alloy DEG C being exposed to lead gas lost efficacy in a brittle manner, and this shows that lead also can cause solid grains border brittle；With LME is contrary, and this is more serious under low strain rate.Known other elements causing grain boundary embrittlement in Cu-alloy It is sulphur and oxygen.
Content of the invention
Therefore the purpose of the present invention is the metal product proposing to be made up of Cu-Ni-Sn-Pb base alloy, and it overcomes existing skill At least some of art limits.
It is a further object to provide the metal product being made up of Cu-Ni-Sn-Pb base alloy, it has enhancing Tensile property and there is good machining property.
According to the present invention, these purposes are the systems of the feature by including independent claims and method realizes, Preferred embodiment in the dependent claims and indicates in the description.
These purposes also can be by the conjunction of the Pb of Sn, 0.5%-3wt% of Ni, the 1%-20wt% containing 1%-20wt% in Cu Gold realizes, Cu accounts at least 50wt% of alloy；It is characterised by that this alloy contains the independent of 0.01wt%-5wt% further or ties mutually P or B closing.
In one embodiment of the invention, this alloy contains the independent of 0.01wt%-0.5wt% further or combines P or B.
In a preferred embodiment of the invention, this alloy comprises the Pb of Sn, 1wt% of Ni, 6wt% of 9wt%.
The alloy of the present invention be characterized for 800 DEG C be heat-treated about 1 hour, subsequently in water or be quenched it in atmosphere After being substantially higher than 180 MPa and yield strength Rp of 333 MPa respectively measured by 400 DEG C0.2With maximum stress Rm.Should Alloy is also characterized for being substantially higher than after follow-up aging about 12 hours after 800 DEG C of heat treatments about 1 hour and at 320 DEG C The Hv hardness of 190.
These purposes are also by the producer that is metal product and that comprise the following steps being made up of the alloy of the present invention Method realizes：Obtain first block of this alloy with homogeneous texture；At a temperature of between 690-880 DEG C by this alloy annealing with Just homogenizing and improvement alloy cold forming performance；Cooldown rate cooling between 50 DEG C/min and 50000 DEG C/min, this depends on The lateral dimension of described product and the composition of described alloy；And cold forming.
The present invention also includes the metal product that be made up of and by the present invention method produces, this product the alloy of the present invention It is characterized at 700-1500 N/mm2Between mechanical resistance, the Hv hardness between 250 and 400, and more than 70% can Machinability indexes, relative to standard ASTM C36000 brass.
Machinable metal product can manufacture and moderate temperature (300 DEG C-700 in the case of not having crack DEG C) under there is excellent machinery and tensile property.
In the description of the invention, whole % wt% represent, even if not explicitly mentioning in the text.
Brief description
By reading appended claim and utilizing narration that is that example provides and that illustrated by accompanying drawing, Ke Yigeng Understand the present invention well, wherein：
Fig. 1 represents the metallographic profile of the Cu-Ni-Sn-Pb alloy containing B according to the present invention；With
Fig. 2 represents the metallographic profile of the Cu-Ni-Sn-Pb alloy containing P according to the present invention.
Detailed description of the invention
In one embodiment of the invention, Cu base alloy comprises the Ni of 1%-20wt%, the Sn of 1%-20wt%, and ratio Can be the Pb of 0.1%-4wt%, remainder is substantially made up of Cu, and wherein inevitable impurity typical content is 500 Ppm or lower.
Lead is substantially insoluble in other metals of this alloy, and the product being obtained will include being dispersed in Cu-Ni-Sn matrix In lead particle.In machine operations, this lead has lubricant effect and promotes the fragmentation of fragment.
The amount of the lead introducing in the alloy depends on the degree of the machinability striving for realizing.Typically, can introduce The lead amount of at most several percetages by weight, and do not change the mechanical performance of alloy at normal temperatures.But, it is higher than lead fusing point (327 DEG C), this liquid lead weakens this alloy consumingly.Alloy containing lead is accordingly difficult to manufacture, on the one hand because they have very The notable tendency in strong generation crack and, on the other hand, because they can show that containing undesirable weakening phase Two-phase crystal structure.Therefore, in the alloy of the present invention, lead content is preferably between 0.5wt%-3wt% or at 0.5wt%- Between 2wt%, even more preferably between 0.5wt% and 1.5wt%.
This alloy composition can comprise the element such as Mn of 0.1%-1% optionally further, introduces at this composition as deoxidant In.This Cu alloy also can comprise other elements, such as the combination of at least two in Al, Mg, Zr, Fe or these elements, replaces Mn Or together with Mn.The existence of these elements also can improve Spinodal hardening (spinodal hardening) of Cu alloy. In addition, the means preventing Cu alloy oxidation can be used.
In another embodiment, a part for the Cu content of the alloy of the present invention can be by other elements such as Fe or Zn Substitute, according to the ratio of for example at most 10%.
In yet another embodiment of the present invention, Cu base alloy contain at least 0.01wt% be selected from Al, Mn, Zr, P Additional alloy element in (phosphorus) or B (boron).In addition, the Cu base alloy of the present invention contain at least 0.01wt% selected from Al, The mixture of at least two additional elements in Mn, Zr, P or B.
In a preferred embodiment of the invention, this Cu base alloy contains P or B of 0.01wt%-5wt%.
In the more preferred of the present invention, this Cu base alloy contain Sn, 1wt% of Ni, 6wt% of 9wt% Pb, P or B with 0.02%-0.5wt%.
Have studied the impact for Cu-Ni-Sn-Pb alloy mechanical performance at moderate temperatures for the interpolation of P and/or B.For This purpose, at semi-continuous casting equipment (capacity under the covering of argon gas：By pure composition (prealloy Cu3P and CuZr in 30kg)： 99.5wt%, Al：99.9wt%, all other：99.99wt%) prepare the metal product being made up of Cu base alloy, this Cu base alloy Containing about：The Pb of the Sn of the Ni of 9wt%, 6wt%, 1wt%, and P or B of about 0.02-0.5%.
Being analyzed to measure by inductively coupled plasma (ICP) is given in Table 1, wherein studied forming of different-alloy Composition is reported by wt%, and surplus is Cu.The value ICP method of Zr fails to detect
The composition of table 1 alloy.
Metal product is cast into cylindrical bar, 12 mm diameters, with after be swaged into the straight of 7.5 mm through three steps Footpath.Go out to have the tensile sample of the measuring length of 30 mm and the diameter of 4 mm with machining from these.Sample is at air In in 800 DEG C be homogenized 1 hour, then in water be quenched.
Alloy C1 and C2 is increased in this list and to investigate when using the alloying additive of lower content be The no characteristic that also can reach machinability and high intensity.Contrary with the alloy being expressed as B, the sample of alloy C1 and C2 exists 800 DEG C of annealing cool down for 1 hour afterwards in atmosphere.
Fig. 1 and 2 represent according to the present invention contain respectively B (B4) and containing P (B5) alloy metallographic section SEM show Micro-photo.Alloy B4 and B5 demonstrate formed respectively when B or P is added in Cu base alloy rich in Ni, Sn and/or The hard second phase particle 1 of person B or P.Also the hard second rich in Ni, Sn and Zr is formed when Zr adds in Cu base alloy Phase particle 1（Do not show）.Second phase 1 is harder than the remainder of Cu base alloy substrate.Alloy B4 and B5 is also by grain size (this In substantially 35 μm of average diameters) characterize, this grain size is free from nearly two points of the grain size in other alloys of B or P One of.It is respectively provided with relatively low B or alloy C1 and C2 of P content and has displayed that Second Phase Particle 1, but content reduces (micro-photograph Piece does not shows).Second Phase Particle 1 is evenly distributed in microstructure and has the size of a few micrometers.Pb inclusion 2 is at figure Occur with white in 1 and 2.
Table 2 reports 800 DEG C of heat treatments about 1 hour and subsequently after 320 DEG C of aging about 10 hours and 12 hours, right In Vickers hardness (HV10) test value measured by alloy B1-B5.This test value is carried out with the value being obtained for alloy A2 Relatively.Alloy B4 and B5 discovery hardness for the present invention has the raising of top
Time [h] A2 B1 B2 B3 B4 B5
0 98 105 99 102 114 114
10 177 137 161 179 167 190
12 160 138 160 177 188 208
Table 2-Vickers hardness (HV10), unit Hv.
In table 3, yield strength (R is reported for A1-B5 alloy samplep 0.2) and maximum stress (Rm) value.800 DEG C of heat Process about 1 hour, subsequently in water or after being quenched in atmosphere, obtain these values by carrying out hot tensile test.Stretching examination Test is to use servo-hydraulic testing machine (MFL 100 kN) at 400 DEG C 10-2s-1Strain rate under carry out.Sample is by making Quickly heat with lamp stove (Research Inc., Model 4068-12-10), in less than 2 minutes, reach the test of stabilisation Temperature, therefore farthest reduces the generation of phase in version in heating process.Due to quick heating and high strain rate, The rupture of sample is obtained after 400 DEG C of holdings less than 3 minutes
A1 A2 B1 B2 B3 B4 B5
Rp 0.2[MPa] 229 161 - 166 184 190
Rm[MPa] 422 184 158 134 198 333 334
Table 3-yield strength (Rp 0.2) and maximum stress (Rm), unit is MPa.
Lead adds to and significantly causes alloy embrittlement in CuNi9Sn6 alloy.Contain with for other not adding P and/or B The value that the alloy A2-B3 of Pb is obtained is compared, and alloy B4 and B5 for the present invention obtains improved yield strength (Rp 0.2) With maximum stress (Rm) value.400 DEG C of alloy C1 and C2 institutes for the B (0.03wt.%) and P (0.1wt.%) with decrement The value being respectively the yield strength of 160 MPa and about 300 MPa and maximum stress value and alloy A2-B3 at such a temperature obtaining Compare and also improve.
After rupturing in above hot tensile test, the SEM of the longitudinal cut of the broken sample of alloy C1 and C2 studies (not Display) show, it is that intergranular lost efficacy that Second Phase Particle 1 is frequently located in (seeing Fig. 1 and 2) and inefficacy near Pb inclusion 2, this table Pass judgement and split not forming core at bigger Second Phase Particle 1.
Table 3 reports, with qualitative fashion, the liability that quenching-crackle is formed by alloy A2-B5.In table 3, symbol "+" table Show the existence of crackle, from "+" it is then to be gradually increased quantity and the degree of depth to " +++ ", and " 0 " represents there is not any crackle.Pass through First the alloy A2-B5 sample of casting former state is heat-treated 1 hour at 800 DEG C and then drops to sample in the water-bath of room temperature Or drop to be held in 80 DEG C or or be held in the oil bath of 180 DEG C, carry out quenching experiment to described alloy sample.Alloy Then sample surfaces optically detects crackle.Table 3 shows that alloy B4 and B5 according to the present invention is not susceptible to be quenched-split most Line is formed
Water Oil, 80 DEG C Oil, 180 DEG C
A2 +++ ++ +
B1 +++ + +
B2 ++ + +
B3 +++ + +
B4 + 0 0
B5 + 0 0
Table 3.
Pass through drilling（Consider cutting speed, feeding and chip length）The alloy B4-C2 of the present invention being tested processes Property discovery be similar to the respective performances of other alloys without P or B.Compared with other alloys of A1-C2 group, alloy B5 finds There is best machinable.
Result above shows, hard second phase particle 1 does not represent the preferred coring in intercrystalline space in the alloy Point, but hinder Grain Boundary Sliding, this is that in copper alloy, moderate temperature (300-700 DEG C) is brittle and does not has the main of coring space One of reason.Additionally, in the alloy (B3, B4, B5, C1, C2) containing Zr, B and P of the present invention, Pb inclusion 2 shows substantially inclines Contain near the second phase sediment 1 of B-or P-to being proximally located at solid, and there is quite irregular, complicated shape.This Can result in the low-yield interface at moderate temperatures between fusion of lead inclusion 2 and hard second phase 1 so that Pb " soaks " Second Phase Particle 1.This improves melted Pb inclusion 3 and reaches applied stress necessary to instability, thus is delayed containing B and P The rupture of alloy and make it have higher intensity and more ductility, and improved draftability may be obtained in moderate temperature Energy.In other words, institute addition element such as P, B or the Zr in Cu base alloy results in hard second phase 1, the latter and melted Pb Demonstrate low interface energy during contact, thus stablize this particle to avoid deforming upon under applying stress.With A2 and residue B- The more high tensile property (table 2) that series alloy compares B4 and B5 also can be by the difference of crystallite dimension（Wherein B and P uses Make grain refiner）And the second phase 1 of relatively low ductility is born load explain.
Obviously, alloy B4, B5, C1 and C2 of the present invention largely solves owing to closing to improve CuNi9Sn6 Gold machinable and add the moderate temperature embrittlement issue caused by lead.What the B3-C2 alloy of leading retained them has suction Gravitation freely machine attribute.
In one embodiment of the invention, the machinable metal product being made up of the Cu base alloy of the present invention is Obtained by the method including continuously or semi-continuously casting process.In the method, the first metal compact is for example expressed into It is typically capable of the diameter between 25 mm-1 mm.This alloy is then for example by compressed-air actuated stream or pass through water spray Any other suitable method that or can reach suitable cooldown rate is cooled, and this cooldown rate is preferably high enough to limit The formation of brittle second phase and be simultaneously sufficiently fast to avoid crack to produce, this is discussed below.
Then the material of the first briquet experiences one or several cold forming operations, for example by rolling, wire drawing, be drawn into Shape, hammering or any other cold deformation technique.After cold forming steps, the second briquet presents necessarily be in wherein alloy Anneal under the single-phase annealing temperature in that temperature range, typically in passing-type furnace or bell removable stove. For the Cu alloy of a kind of present invention having in above-mentioned composition, annealing temperature is between 690 DEG C and 880 DEG C.Especially make Process step with annealing steps or heat uniforming, in order to induction ductility, become, by making structure, this structure that uniformly becomes more meticulous, and And improve the cold forming performance of alloy.
In the modification of this embodiment, the second briquet can experience at annealing or heat uniforming before cold forming process Reason step.
In annealing steps, the second briquet will occur at least partly recrystallization, and wherein new strainless grain nucleation is simultaneously And growth is to substitute those deforming due to internal stress.Second briquet is again with following cooling velocity quilt after the anneal step Cooling：The formation that this speed is preferably high enough to limit degradation property the second phase is again sufficiently fast to avoid crack to produce simultaneously Raw.
A step of cold forming process or several sequential step can be carried out, each of which cold forming steps followed by Annealing and cooling step, in order to obtain in succession several briquets with required diameter and shape.
After cold forming in succession, annealing and cooling step, final briquet can wire drawing or stretch forming to final Diameter and/or shape, to obtain machinable product.Subsequently, can finally this machinable product or machinery be added The workpiece of work carries out spinodal decomposition heat treatment or hardening, in order to obtain optimal mechanical performance.A rear heat treatment can be Carry out before or after final machining.
Cooling step after extrusion and/or annealing must be carried out under following speed：This speed is enough slow It preventing by the cracking initiation of the alloy being caused by the internal constraint that temperature contrast produces in cooling procedure, but is simultaneously Enough is fast to limit the formation of two phase structures.If this speed is too slow, then a considerable amount of second phase can occur. This second phase is very fragility and the deformability being greatly reduced alloy.For avoiding the formation institute of too substantial amounts of second phase The critical cooling rate needing will depend upon which the chemistry of this alloy and is bigger for the nickel and tin of higher amount.
Additionally, in cooling procedure, produce temporary transient internal constraint in alloy.They with on the surface of briquet or product With the temperature difference between center is relevant.If these constraints have exceeded the resistance of alloy, then the latter will produce crack and not Useful again.Product diameter is bigger, all higher owing to cooling down the internal constraint causing.Critical for avoid producing required for crack Cooldown rate is accordingly dependent on the diameter of product.In the method for the invention, extrusion and/or annealing steps after, 50 DEG C/ Cool down under cooldown rate between minute and 50000 DEG C/min.
Copper-nickel-tin alloy has long solidification interval, causes sizable segregation in casting operation.Continuously or half In continuous casting process, molten alloy can be stirred to allow casting metal with regard to its surface state and its internal performance Such as segregation and obtain higher systematicness for shrinking.Additionally, when molten alloy fusing and casting, generation tree dendritic crystal is tied Structure and fine-grained alloy cannot be obtained.
Copper alloy can be stirred with electromagnetic mode, in order to agitation melt.It is enough that this magnetic force can produce to briquet Stirring, thus allow to reduce the quantity at segregation center and acquisition has the axle such as fine that average grain size is substantially less than 5 mm The Cu base alloy of crystal.
Or, the melted Cu alloy in briquet mechanically can be stirred by using ultrasonic energy, in order to Air pocket and acoustic streaming is produced in melted material.Other type of mechanical agitation also can use, such as forced gas mixing, and thing This molten alloy, or plant equipment such as rotor, screw or stirring impulse jet are such as vibrated or rock in reason mixing.Or, electromagnetism Stirring can combine with mechanical agitation use, or ultrasonic agitation can combine with mechanical agitation use.
In another embodiment of the present invention, the first briquet of the Cu base alloy with the diameter of at most 320 mm is Produced by using spray-forming method, as that be known as " Osprey " method and be described in patent EP0225732 Method.Here, by using the atomized particle size in the particle size range of 1-500 micron, it is possible to obtain average grain size is less than The alloy of 200 microns.Spray-forming method makes it possible to obtain the almost uniform microstructure with minimum degree of segregation.Other The briquet of type, such as ingot, disk or the bar with square-section, it is also possible to produce with spray-forming method.Motlten metal or The injection of metal alloy particle is in required atmosphere, preferably carries out in inert atmosphere such as nitrogen or argon gas.
Or, it is obtained in that this metal product by static billet casting method or any other appropriate method.
Cu base alloy product is characterized by following performance：Annealing and cooling step after indoor temperature measurement 700-1500 N/mm2Tensile strength between (700-1500 MPa)；Annealing and cooling step after measurement Vickers hardness (HV10) between 250 and 400；With the machinability index more than 70%, relative to standard ASTM For C36000 brass.Additionally, this Cu base alloy product can because the facility of the fragment producing in turning process removes Easily machining and especially needed turning step or free cutting step, punch steps, bending can be advantageously used in In the machining operations of step, drilling step etc..
Can advantageously use the Cu base alloy product of the present invention, to obtain rod, there is circular or any other profile The product of the bar of the silk of shape, bar such as rolling, block, ingot, piece etc..This Cu base alloy product also can be advantageously used in machine The manufacture all or in part of the workpiece of tool processing, described workpiece such as has for example higher than 700 N/mm2High elastic limit Electric conductivity workpiece, such as connector, electromechanical workpiece, the parts in phone manufactures, spring etc., or at such as micro computer Tool, horology, tribology, aviation etc application in micromachine workpiece, or in various applications any other Workpiece.
The method of the present invention makes it possible to produce the P of Pb and 0.01%-0.5% containing at most several percetages by weight And/or B can the Cu-Ni-Sn base product of machining, it does not produce crack in the fabrication process, and has excellent machine Tool and tensile property.
Reference and symbol
1 Second Phase Particle
2 Pb inclusions
Rp0.2Yield strength
RmMaximum stress.

Claims (17)

1. alloy, it contains the Pb of Sn, 0.5wt%-3wt% of Ni, 1wt%-20wt% of the 1wt%-20wt% in Cu, described Cu accounts at least 50wt% of described alloy；Be characterised by this alloy contain further 0.01wt%-5wt% P individually or together or B.
2. alloy according to claim 1, wherein this alloy contain further 0.01wt%-0.5wt% P individually or together or B.
3. the alloy according to claim 1 or 2, wherein this alloy comprises the Pb of Sn, 1wt% of Ni, 6wt% of 9wt%.
4. alloy according to claim 3, wherein this alloy has yield strength R being substantially higher than 180 MPap 0.2, described Yield strength 800 DEG C of heat treatments about 1 hour and subsequently in water or in atmosphere quenching after 400 DEG C of measurements.
5. the alloy according to claim 3 or 4, wherein this alloy has the maximum stress R being substantially higher than 333 MPam, described Maximum stress 800 DEG C of heat treatments about 1 hour and subsequently in water or in atmosphere quenching after 400 DEG C of measurements.
6. the alloy according to any one in claim 3 to 5, wherein this alloy has the Hv hardness being substantially higher than 190, institute State Hv hardness 800 DEG C of heat treatments about 1 hour and to measure after aging about 12 hours at 320 DEG C subsequently.
7. the alloy according to any one in claim 1 to 6, wherein 800 DEG C heat treatment about 1 hour and subsequently in water or After being quenched in atmosphere, this alloy includes the second phase (1), and the latter contains Ni, Sn and or B or P.
8. the production method of metal product that the alloy being characterized by any one in claim 1 to 7 is constituted, the method include with Lower step：
a）Obtain the first briquet of the described alloy with homogeneous texture；
b）Temperature between 690 DEG C and 880 DEG C anneals this alloy to be homogenized and improve the cold forming performance of this alloy；
c）It with the cooldown rate cooling between 50 DEG C/min and 50000 DEG C/min, is specifically dependent upon the horizontal of described product Size and the composition of described alloy；With
d）Cold forming.
9. method according to claim 8, wherein the step a) of claim 8 is for extruding the diameter of this alloy 25 The continuous casting process of the first briquet between mm-1 mm.
10. the method for according to Claim 8 or 9, wherein the described alloy in the first briquet is with electromagnetic mode or with machinery side Formula stirs, in order to obtain the described alloy with the fine equiaxed crystal that average grain size is substantially less than 5 mm.
11. methods according to claim 8, wherein the step a) of claim 8 be spray-up method and wherein formed described First briquet has diameter and the average grain size less than 200 microns of at most 320 mm.
12. according to Claim 8 to the method for any one in 11, and wherein said cold forming steps includes rolling, wire drawing, stretching Shaping, hammering technique.
13. metal products being obtained by the method that any one in claim 8 to 12 is characterized, wherein said metal product Having the tensile strength between 700-1500 MPa, this tensile strength is at the annealing of claim 8 and cooling step b) and c） After indoor temperature measurement.
14. products according to claim 13, wherein this product at the annealing of claim 8 and cooling step b) and c) after tool There is the Hv hardness between 250-400.
15. according to the product of claim 13 or 14, and wherein this product has the machinability index more than 70 %, relatively For standard ASTM C36000 brass.
16. according to the product of any one in claim 13 to 15, and wherein this product has rod, line, bar, block, ingot and piece Shape.
17. according to the product of any one in claim 13 to 16, the electric conductivity work that wherein this product is crossed for machining Part or the manufacture all or in part of machinery or micromachine workpiece.
CN201610288541.8A 2009-04-08 2009-04-08 Machinable copper base alloy and production method thereof Pending CN106435250A (en)

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CN112981168A (en) * 2021-02-04 2021-06-18 合肥工业大学 Powder hot-forged copper-based pantograph slide plate material and preparation method thereof
CN113789459A (en) * 2021-09-02 2021-12-14 宁波博威合金材料股份有限公司 Copper-nickel-tin alloy and preparation method and application thereof
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