AU2004319350A1 - Free-cutting, lead-containing Cu-Ni-Sn alloy and production method thereof - Google Patents
Free-cutting, lead-containing Cu-Ni-Sn alloy and production method thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims description 79
- 239000000956 alloy Substances 0.000 title claims description 79
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 229910018100 Ni-Sn Inorganic materials 0.000 title description 9
- 229910018532 Ni—Sn Inorganic materials 0.000 title description 9
- 238000001816 cooling Methods 0.000 claims description 71
- 238000000034 method Methods 0.000 claims description 44
- 238000010438 heat treatment Methods 0.000 claims description 28
- 238000011282 treatment Methods 0.000 claims description 21
- 239000000203 mixture Substances 0.000 claims description 20
- 230000015572 biosynthetic process Effects 0.000 claims description 15
- 239000000126 substance Substances 0.000 claims description 15
- 238000005266 casting Methods 0.000 claims description 14
- 238000009749 continuous casting Methods 0.000 claims description 10
- 238000001125 extrusion Methods 0.000 claims description 9
- 238000001953 recrystallisation Methods 0.000 claims description 7
- 238000009718 spray deposition Methods 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 238000005096 rolling process Methods 0.000 claims description 5
- 230000003068 static effect Effects 0.000 claims description 5
- 238000005491 wire drawing Methods 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052749 magnesium Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 239000000047 product Substances 0.000 description 33
- 239000000463 material Substances 0.000 description 20
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 19
- 239000011133 lead Substances 0.000 description 18
- 239000010949 copper Substances 0.000 description 12
- 238000005496 tempering Methods 0.000 description 12
- 239000011135 tin Substances 0.000 description 12
- 229910052718 tin Inorganic materials 0.000 description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 9
- 229910052802 copper Inorganic materials 0.000 description 8
- 229910052759 nickel Inorganic materials 0.000 description 8
- 238000005204 segregation Methods 0.000 description 8
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 7
- 241000237858 Gastropoda Species 0.000 description 6
- 238000001330 spinodal decomposition reaction Methods 0.000 description 6
- 239000007921 spray Substances 0.000 description 5
- 230000002349 favourable effect Effects 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 229910001369 Brass Inorganic materials 0.000 description 3
- 229910017532 Cu-Be Inorganic materials 0.000 description 3
- 239000010951 brass Substances 0.000 description 3
- 239000012530 fluid Substances 0.000 description 3
- 238000000265 homogenisation Methods 0.000 description 3
- 238000012345 traction test Methods 0.000 description 3
- 238000007514 turning Methods 0.000 description 3
- 229910020816 Sn Pb Inorganic materials 0.000 description 2
- 229910020922 Sn-Pb Inorganic materials 0.000 description 2
- 229910008783 Sn—Pb Inorganic materials 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 229910052790 beryllium Inorganic materials 0.000 description 2
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium atom Chemical compound [Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 229910052745 lead Inorganic materials 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910018663 Mn O Inorganic materials 0.000 description 1
- 108091034117 Oligonucleotide Proteins 0.000 description 1
- 241000566150 Pandion haliaetus Species 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 229910000796 S alloy Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 229910001128 Sn alloy Inorganic materials 0.000 description 1
- VRUVRQYVUDCDMT-UHFFFAOYSA-N [Sn].[Ni].[Cu] Chemical compound [Sn].[Ni].[Cu] VRUVRQYVUDCDMT-UHFFFAOYSA-N 0.000 description 1
- 230000001154 acute effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
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- 238000000151 deposition Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000003467 diminishing effect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000013467 fragmentation Methods 0.000 description 1
- 238000006062 fragmentation reaction Methods 0.000 description 1
- 230000008642 heat stress Effects 0.000 description 1
- 231100000086 high toxicity Toxicity 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000002035 prolonged effect Effects 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
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/02—Alloys based on copper with tin as the next major constituent
Description
International Patent Application English translation Applicant SWISSMETAL - UMS Usines Metallurgiques Suisses SA 2732 Reconvilier, Switzerland inventor(s) Emmanuel Vincent Attorney Giovanni Gervasio Patents & Technology Surveys Ltd Terreaux 7, P 0 Box 2848 CH-2001 Neuchatel, Switzerland Title "Machinable copper-based alloy and production method" (Original title: "Alliage decolletable base de cuivre ct m6thode de production") Filing date Filing number Attorney's reference 0S.04.2004 2004WO-EP050449 (WOOS108631) SMETAL-2-PCT Versions Numi] Date VersIoages ason Submitted Filed 1.E Englisi transIatin 20 National phase I, Anne Kristine Kjelsen, domiciled at Lnclistrasse 20, CI--347Bremgarten bei Berne (Switzerland), translator, do hereby solemnly and sincerely declare: 1. that I am acquainted with the French language; 2. that I am acquainted with the English language; 3. that I am the translator of the above referenced document; 4. and that to the best of my knowledge and belief the following is a true and correct English translation thereof. Berne 14.09.2006 (Place & Date) (Anne Krist fie Kjelsen) .. . .... .. .... . .
Machinable copper-based alloy and production method Technical field The present invention concerns an alloy based on copper, nickel, tin, lead and its prodUction method. In particular, thoLIgh not exclusively, 5 the present invention concerns an alloy based on copper, nickel, tin, lead easily machined by turning, slicing or milling. State of the art Alloys based on copper, nickel and tin are known and widely used. They offer excellent mechanical properties and exhibit a strong 10 hardening during strain-hardening. Their mechanical properties are further improved by the known heat-aging treatment such as spinodal decomposition. For an alloy containing, by weight, 15% of nickel and 8% of tin (standard alloy ASTM C72900), the mechanical resistance can reach 1500 MPa. 15 Another favorable property of the Cu-Ni-S alloys is that they offer good tribological properties, comparable to those of bronzes, while exhibiting superior mechanical properties. Another advantage of these materials is their excellent formability, combined with favorable elastic properties. Moreover, these 20 alloys offer a good resistance against corrosion and an excellent resistance to the constraints' heat relaxation. For this reason, the Cu-Ni-Sn springs do not lose their compression force with age, even under vibrations and strong heat stresses. These favorable properties, combined with good heat and 25 electricity conductivity, mean that these materials are widely used for making highly reliable connectors for telecommunications and the car industry. 'These alloys are also used in several switches and electrical or 2 electromechanical devices or as supports of electronic components or for making bearing friction surfaces subjected to high charges. The Cu-Be alloys can be machined fairly well and can contend with and even outperform the mechanical properties of Cu-Ni-Sn alloys. 5 The machinability index of the Cu-Be alloys can reach 50-60% relatively to standard ASTM C36000 brass. Their cost is however high and their production, use and recycling are particularly constraining because of the beryllium's high toxicity. The resistance to the constraints' heat relaxation of these materials is lower than that of the Cu-Ni-Sn for temperatures 10 above 150-175*C. One inconvenience of the Cu-Ni-Sn alloys is however that they are poorly suited to processes such as milling, turning or slicing or to any other known process. A further inconvenience of these alloys is their strong segregation during casting. 15 It is thus an aim of the present invention to propose an alloy associating the favorable mechanical characteristics of alloys based on copper, nickel and tin with a good workability. It is another aim of the present invention to propose a method for producing a machinable product on the basis of Cu-Ni-Sn free from the 20 inconveniences of the prior art, It is another aim of the present invention to propose a machinable alloy combining high elasticity and mechanical resistance characteristics but free from beryllium or toxic elements. A further aim of the present invention is to propose a method for 25 producing a machinable product on the basis of Cu-Ni-Sn allowing the problems relative to segregation to be solved. These aims are achieved by the product and the method that are the object of the independent claims of corresponding category and rM~ITAI -')4(T 3 notably by a machinable product composed of an alloy comprising between 1 % and 20% by weight of Ni, between 1 % and 20% by weight of Sn, between 0.1 % and 4% of Pb, the remainder being constituted essentially of Cu, having undergone a heat homogenizing treatment comprising a step 5 of heating said alloy followed by a step of cooling at a speed sufficiently slow to prevent fissuring. Detailed description of the invention The present invention concerns alloys on the basis of copper, nickel, tin and lead obtained by a continuous or semi-continuous casting 10 method, a static billet casting or casting by sprayforming. The copper nickel-tin alloys have a long solidification interval leading to a considerable segregation during casting. Of the four aforementioned processes, casting by sprayforming, also known by the name "Osprey" method, and described for example in patent EP0225732 makes it a possible to obtain an almost 15 homogenous microstructure presenting a minimal degree of segregation. In this process, a metal billet is obtained by continuous depositing of atomized droplets. The segregation can take place only on the scale of the atomized droplets. The diffusion distances required for diminishing the segregation are thus shortened. In the case of continuous or semi 20 continuous casting, the segregation is stronger than with the sprayforming process, but it remains sufficiently reduced to avoid an excessive fragility of the alloy. The static billet casting leads to a strong segregation that can be eliminated only by a prolonged heat processing. Lead being essentially insoluble in the other metals of the alloy, 25 the product obtained will comprise lead particles dispersed in a Cu-Ni-Sn matrix. During the machining operations, the lead has a lubricating effect and facilitates the fragmentation of the slivers. The quantity of lead introduced in the alloy depends on 'the degree of machinability that one strives to achieve. Generally, a quantity of 30 lead up to several percents by weight can be introduced without the alloy's mechanical properties at normal temperature being modified. However, 4 above the lead melting point (327 'C), the liquid lead strongly weakens the alloy. Alloys containing lead are thus difficult to make, on the one hand because -they have a very strongly pronounced tendency towards fissuring and, on the other hand, because they can exhibit a two-phased 5 crystallographic structure containing an undesirable weakening phase. The method of the present invention makes it possible to produce a machinable Cu-Ni-Sn-Pb product containing up to several percents by weight of lead, without It fissuring during fabrication, and having excellent mechanical properties. The ratio of lead can vary between 10 0.1% and 4% by weight, preferably between 0.2% and 3% by weight, even more preferably between 0.5% and 1.5% by weight. After smelting in the foundry, the production methods can be decomposed in successive slugs: for the first slug, two cases must be considered according to whether 'the product is manufactured by 15 continuous casting at small diameter or by static billet casting, sprayforming, semi-continuous or continuous casting at large diameter. The products of the invention are characterized by their excellent machinability, which is greater than that of Cu-Be alloys. The machinability index of the inventive alloys exceeds 80% relatively to standard ASTM 20 C36000 brass and can even reach 90%. First slug: Alloys obtained by continuous small-diameter thread casting, e.g. of 25mm or less, undergo a heat homogenizing treatment or a step of cold deformation by hammering followed by a homogenizing and 25 recrystallization treatment. The temperature of the heat treatment must be within the range where the alloy is one-phased. Cooling after the heat treatment must occur at a speed sufficiently slow to prevent fissuring of the alloy due to internal constraints generated by the temperature differences during cooling, and sufficiently fast to limit the formation of a two-phased 30 structure. If the speed is too slow, a considerable quantity of second phase 5 can appear. This second phase is very fragile and greatly reduces the alloy's deformability. The critical cooling speed required to avoid the formation of too large a quantity of second phase will depend on the alloy's chemistry and is greater for a higher quantity of nickel and tin. 5 Moreover, during cooling, transitory internal constraints are generated within the alloy. They are linked to temperature differences between the surface and the center of the product. If these constraints exceed the alloy's resistance, the latter will fissure and is no longer usable. Internal constraints due to cooling are all the higher the more the product's 10 diameter is large. The critical cooling speeds to avoid fissuring thus depend on the product's diameter. This problem is even more acute with Cu-Ni-Sn Pb alloys since above its melting temperature of 327*C, lead strongly weakens the alloy. In the method of the present invention, cooling after heat 15 treatment occurs at a predetermined speed taking into account the alloy's chemistry and the transversal dimension, or diameter, of the product. The cooling speed must be at the same time sufficiently slow to prevent fissuring and sufficiently great to prevent too large a quantity of fragilizing phase to form. 20 During rmianufacture of a large-diameter product, the internal constraints due to the temperature differences are greater than in a small dimension product, and the cooling speed must consequently be limited. At the same time, strong proportions of Ni and Sn promote the formation of a fragilizing phase and require a faster cooling. 25 Alloys obtained by sprayforming, static billet casting or semi continuous casting undergo a hot extrusion treatment. This is also the case for continuous casting if the product is of large diameter. Cooling during extrusion must be sufficiently slow to prevent fissuring and sufficiently fast to limit the formation of a fragilizing second phase. Alternatively, if cooling 30 during extrusion is too slow, heat homogenizing and recrystallization 6 treatments as explained here above for the case of small-diameter continuous-casting products must follow extrusion. Once the first slug has been made, the final machinable product must be either obtained directly by one or several cold deformation 5 operations, e.g. by rolling, wire-drawing, stretch-forming or any other cold deformation process, or obtained by one or several successive slugs, Successive slugs. From the first slug, the following slugs are obtained by one or several cold deformation operations followed by a heat recrystallization 10 treatment. The temperature of the recrystallization treatment must be within the range where the alloy is one-phased. Cooling after the heat treatment must have a speed sufficiently slow to prevent fissuring but always sufficiently fast to limit the formation of a two-phased structure. Through successive slugs, the size of the product is reduced. From the last 15 slug, the final product is obtained by one or several cold deformation operations. The mechanical properties of the alloy obtained can be subsequently increased by a spinodal decomposition heat treatment. This treatment can take place before the final machining or after the latter. 20 Hereafter, examples of methods and of machinable products according to the present invention will be presented. In the following examples, the cooling temperatures refer to the center of the product. Exm pLe.1 The chemical composition of the alloy in this example is given by 25 table 1: (PAf-.TAI ') DCT 7 Table 1 Component Pro portion pn y weight)_ Cu remainder Ni 7.5% Sn 5% Pb 1% Mn 0.1%-1% other <0.5% .... . Manganese is introduced in the composition as deoxidizer. It is however possible to use instead other elements or devices preventing the alloy from oxidizing. 5 This alloy can be cast according to the different methods mentioned further above. In this example, this alloy is obtained by continuous billet casting with a diameter of 180mm. Eirst .slug: the billets are extruded for example to a diameter of 18mm. At the exit of the extrusion die, the alloy is cooled by a stream of 10 compressed air allowing a cooling speed of 50*C/min to 300 0 C/min to be achieved, as measured at the center of the alloy. This speed is sufficiently slow to avoid fissuring and sufficiently fast to limit the formation of a fragilizing second phase. Cooling by water spray can also be used, possibly allowing cooling speeds of 300*C/min to 1000*C/min to be achieved without 15 fissuring of the material. Other means for reaching a suitable cooling speed can also be used. If cooling at the exit of the extrusion die is not sufficiently fast, a too great a proportion of second phase can form, the alloy will have to undergo a homogenization treatment with the same characteristics for the cooling speed at a temperature within the range where the alloy is 20 one-phased, i.e. between 690'C and 920*C for the composition of table 1. Second sLg; the material of the first slug at a diameter of 18mm is rolled to a diameter of 13mm then annealed in a through-type furnace or removable cover furnace. For the alloy with the chemical composition of example 1, the annealing temperature must be comprised between 690*C 25 and 920*C. A cooling speed on the order of 10 0 C/min is sufficient to limit the formation of second phase for this composition and this diameter of CftA.I Al *) I/' 8 13mm. Furthermore, water spray cooling at speed of 300*C/min to 3000*C/min allows fissuring to be prevented and the formation of a fragilizing second phase to be limited. Finishing: the material of the second slug is wire-drawn or 5 stretch-formed to a diameter of 8mm to obtain a machinable product. A spinodal decomposition treatment is finally performed on the machinable product or on the machined pieces to obtain optimal mechanical properties. Examp.I 2 10 The chemical composition of the alloy in this example is given by table 2: Table 2 Component Proportion (by weight) Cu remainder In this example, this Ni 9% alloy is obtained by continuous Sn 6% 15 thread casting with a diameter of Pb 1% Mn O.1%.1% 18mm. Impurities <0.5% FirstIUg.: the thread undergoes a homogenization treatment in a through-type furnace at a temperature between 700*C and 920"C, corresponding to the one-phase 20 range of the chemical composition of example 2. A cooling speed between 100*C/min and 1000"C/min allows fissuring to be prevented and the proportion of fragilizing second phase to be limited. Such cooling speeds can for example be achieved by using compressed air, water spray or a gas/water exchanging cooler. 25 SecondsLug: the material of the first slug at a diameter of 18mm is rolled, wire-drawn or stretch-formed to a diameter of 13mm then annealed in a through-type furnace at a temperature comprised between 700*C and 920*C. With a diameter of 13mm and the chemical composition CAr--r , ,,*, 9 of table 2, a cooling speed between 100*C/min to 3000 0 C/min allows the formation of a second phase to be limited while avoiding fissuring. Third s Lug: the material of the second slug at a diameter of 13mm is rolled, wire-drawn or stretch-formed to a diameter of 10mm then 5 annealed in a through-type furnace or tempering furnace at a temperature comprised between 700 0 C and 920*C. With a diameter of 10mm and the chemical composition of table 2, a cooling speed between 100 0 C/min to 15000*C/min allows the formation of a second phase to be limited without any fissuring being created. 10 Fourth sjug: the material of the third slug at a diameter of 10mm is rolled, wire-drawn or stretch-formed to a diameter of 7mm then annealed in a through-type furnace or tempering furnace at a temperature comprised between 700 0 C and 920 0 C. With a diameter of 7mm and the chemical composition of table 2, a cooling speed between 100*C/min to 15 20000*C/min allows the formation of a fragilizing second phase to be limited without any fissuring being created. Fifth slug: the material of the fourth slug at a diameter of 7mm is rolled, wire-drawn or stretch-formed to a diameter of 5mm then annealed in a through-type furnace or tempering furnace at a temperature 20 comprised between 700*C and 920"C. With a diameter of 5mm and the chemical composition of table 2, a cooling speed between 100"C/min to 30000*C/min allows the formation of a fragilizing second phase to be limited without any fissuring being created. A cooling speed on the order of 15000*C/min can be achieved by tempering in appropriate fluids. 25 SixtLsLg: the material of the fifth slug at a diameter of 5mm is rolled, wire-drawn or stretch-formed to a diameter of 3mm, annealed in a through-type furnace or tempering furnace at a temperature comprised between 700*C and 920*C, then cooled at a cooling speed comprised between 100"C/min to 40000 0 C/min. Al'-TA I - ii'T 10 Seventh slug: the material of the sixth slug at a diameter of 3mm is rolled, wire-drawn or stretch-formed to a diameter of 2mm, annealed in a through-type furnace or tempering furnace at a temperature comprised between 700*C and 920*C, then cooled at a cooling speed comprised 5 between 100*C/min to 40000*C/min. Eighth slug: the material of the seventh slug at a diameter of 2mm is rolled, wire-drawn or stretch-formed to a diameter of 1,60mm, annealed in a through-type furnace or tempering furnace at a temperature comprised between 700*C and 920 0 C, and then cooled at a cooling speed 10 comprised between 100*C/min to 50000"C/min. Finishirng: the material of the eighth slug is rolled, wire-drawn or stretch-formed to a diameter of 1mm to obtain a machinable product. A spinodal decomposition treatment is finally performed on the machinable product or on the machined pieces to obtain optimal mechanical 15 properties. The "ASTM test method for machinability" test proposes a method for determining the machinability index relatively to standard CiZn39Pb3, or C36000 brass. The machinability index of the alloy according to this aspect of the invention is better by 80%. 20 Example 3 The chemical composition of the alloy in this example is the same as that of the second example given by table 2. In this example, the alloy is obtained by continuous casting at a diameter of 25mm. First s1Ig: the thread cast at a diameter of 25mm is hammered to 25 a diameter of 16mm. The hammering allows the material to deform with a considerable reduction rate without prior heat homogenizing treatment. With this method, a high remainder ratio of fragilizing second phase can be tolerated at this stage. The second phase can reach a volume ratio on the order of 50%.
11 After hammering, the thread at a diameter of 16mm undergoes a homogenizing and recrystallization treatment in a through-type furnace. The temperature of the heat treatment must be comprised between 700*C and 920*C. The following cooling will take place at a speed comprised 5 between 100*C/min and 3000*C/m in. These cooling speeds make it possible to prevent fissuring and to limit the ratio of second phase for a product of this diameter and of this composition. Such speeds can be obtained by using compressed air, water spray or gas/water exchangers. Finishing: the material of the first slug is wire-drawn or stretch 10 formed to a diameter of 10mm to obtain a machinable product. A spinodal decomposition treatment is finally performed on the machinable product or on the machined pieces to obtain optimal mechanical properties. Ex aprwie 4 The chemical composition of the alloy in this example is given by 15 table 3: Table 3 Cornpornent Pro portion (by weight) Cu remainder Ni 15% Sn 8% Pb 1% Mn 0.1%-1% Impurities <0.5% This alloy can be cast according to the different methods mentioned here above. In this example, this alloy is obtained by sprayforming billets whose diameter is 240mm. 20 First sly.g: the billets are extruded for example to a diameter of 20mm. If the billets' dimensional irregularities are too great, a turning step can be necessary before extrusion. At the exit of the extrusion die, the alloy is cooled by water spray allowing a cooling speed of 300 0 C/min to 3000 0 C/min to be achieved, as measured at the center of the alloy. This '~I, NA 12 speed is sufficiently slow to avoid fissuring and sufficiently fast to limit the formation of a fragilizing second phase. If cooling at the exit of the extrusion die is not sufficiently fast, a too great a proportion of second phase can form. The alloy will then have to undergo a homogenization 5 treatment with the same characteristics for the cooling speed at a temperature within the range where the alloy is one-phased, i.e. between 780 0 C and 9204C for the composition of table 3. Second sluq: the material of the first slug at a diameter of 20mm is hammered to a diameter of 11mm then annealed in a through-type 10 furnace. For the alloy with the chemical composition of example 3, the annealing temperature must be comprised between 780*C and 920"C. With a diameter of 11mm and the chemical composition of table 3, a cooling speed comprised between 300*C/min and 15000*C/min allows the presence of second phase to be limited while avoiding fissuring. Use of hammering 15 allows considerable strain-hardening rates to be achieved, even with a fragile material. With this method, the remainder rate of fragilizing second phase can be higher than with rolling, wire-drawing or stretch-forming methods. It can reach values on the order of 50% by volume. Third sug: the material of the second slug at a diameter of 11mm 20 is hammered to a diameter of 6,5mm then annealed in a through-type furnace or tempering furnace at a temperature comprised between 780"C and 920*C. With a diameter of 6,5mm the alloy of table 3 allows cooling speeds between 300*C/min to 20000*C/min without any fissuring. These speeds allow the ratio of fragilizing second phase to be limited. 25 Fjnjisbjng: the material of the third slug is wire-drawn or stretch formed to a diameter of 4mm to obtain a machinable product. A spinodal decomposition treatment is finally performed on the machinable product or on the machined pieces to obtain optimal mechanical properties. C &A t 1'A I 'I 1IC 13 Cooling test Samples of the inventive alloy have been subjected to test of fast cooling to determine the occurrence of fissuring. The chemical composition of the alloy in this test is given by table 2. 5 The samples were subjected to a heat treatment at a temperature of 800 0 C and then cooled quickly by immersion in a tempering fluid (EXXON XD90) and in water. For each cooling, the cooling speed, in *C/min, was measured with a thermocouple at the center of the sample. The presence of fissuring 10 was verified by a traction test. Table 5 diameter/mm speed traction test speed traction test 4 24000 0 63000 X 6 16000 0 48500 x 8 12000 0 33000 X 10.8 8350 0 - X 13 6500 O/X 23500 X (0 = success / x failure) The test permits to observe that the diameters up to about 10mm can tolerate a cooling in a tempering fluid. Water tempering, on the other hand, always leads to a fissuring of the sample, and this up to a minimal 15 diameter of 4mm. For small-dimension products of Cu-Ni-Sn-Pb, cooling speeds greater than 24000*C/min can be used, In this case, water tempering can be efficient if the product's size is sufficiently small to limit the transitory internal constraints and thus prevent fissuring from forming. 20 The machinable products of the examples 1, 2, 3 and 4 can each be made by the methods of the examples 1, 2, 3 and 4 provided that the CACTrAl M,* 14 cooling speeds and the heat treatment temperatures are adapted to the chemical compositions and to the dimensions. In each of the presented examples, the number of slugs can vary according to the size of the finished product. 5 Part of the copper of the alloys of the present invention can be replaced by other elements, for example Fe, Zn or Mn, at a ratio for example up to 10%. Other elements such as Nb, Cr, Mg, Zr and Al can also be present, at a ratio up to several percents. These elements have among others the 10 effect of improving the spinodal hardening. SMETAL-2-PcT
Claims (42)
1. Production method of a metallic product composed of an alloy comprising between 1% and 20% by weight of Ni, between 1 % and 20% by weight of Sn, between 0.1% and 4% of Pb, the remainder being 5 constituted essentially of Cu, the method comprising a heat treatment comprising a step of heating said alloy followed by a cooling step at a speed sufficiently slow to prevent fissuring.
2. Method according to claim 1, wherein the speed of said 10 cooling step is sufficiently high to limit the formation of a two-phased structure.
3. Method according to claim 1 or 2, wherein said cooling step occurs at a predetermined cooling speed depending on the alloy's chemical composition and on the size of said metallic product. 15
4. Method according to claim 1 or 2, wherein said heat treatment is followed by a step of cold deformation by rolling, wire drawing, stretch-forming or hammering.
5. Method according to claim 4, comprising a recrystallization step followed by a cooling step at a speed sufficiently slow 20 to prevent fissuring.
6. Method according to claim 1, wherein said heat treatment is performed in a through-type furnace.
7. Method according to claim 1, comprising an initial step of continuous casting. 25
8. Method according to claim 7, comprising a hammering step after said continuous casting. ChACI 7 I 1 11'1 16
9. Method according to claim 1, comprising an initial step of static billet casting or a step of sprayforming billet casting, or a step of semi-continuous billet casting, followed by an extrusion step.
10. Method according to claim 1, wherein said heat 5 treatment takes places at a temperature comprised between 690 0 C and 920 0 C.
11. Method according to claim 1, wherein the transversal dimension of said metallic product during said heat treatment is comprised between 1mm and 100mm. 10
12. Method according to claim 1, wherein the transversal dimension of said metallic product during said heat treatment is comprised between 5mm and 50mm.
13. Method according to claim 1, wherein the transversal dimension of said metallic product during said heat treatment is comprised 15 between 10mm and 20mm.
14. Method according to claim 1, wherein said cooling step of said heat treatment has a cooling speed comprised between 10*C/min and 24000"C/min.
15. Method according to claim 1, wherein said cooling step of 20 said heat treatment has a cooling speed comprised between 10*C/min and 4000C/rnin.
16. Method according to claim 1, wherein said cooling step of said heat treatment has a cooling speed comprised between 100*C/min and 1500'C/min. 25
17. Method according to claim 1, wherein said cooling step of said heat treatment has a cooling speed comprised between 100*C/nin arid 1000OC/min. Czrl~TAI §..D/T 17
18. Method according to claim 1, comprising a step of wire drawing or stretch-forming or hammering or rolling.
19. Method according to claim 1, comprising a step of spinodal hardening. 5
20. Method according to claim 1, wherein said alloy comprises between 6% and 8% of Ni, between 4 and 6% of Sn and between 0.5 and 2% of Pb.
21. Method according to claim 1, wherein said alloy comprises between 8% and 10% of Ni, between 5 and 7% of Sn and 10 between 0.5 and 2% of Pb.
22. Method according to claim 1, wherein said alloy comprises between 14% and 16% of Ni, between 7 and 9% of Sn and between 0.5 and 2% of Pb.
23. Method according to claim 1, comprising up to 10% of 15 one or more of the following elements: Zr, Nb, Cr, Al, Mg.
24. Product from the method of claim 1.
25. Machinable product, composed of an alloy comprising between 1 % and 20% by weight of Ni, between 1 % and 20% by weight of Sn, between 0.1% and 4% of Pb, the remainder being constituted 20 essentially of Cu, having undergone a heat treatment comprising a step of heating said alloy followed by a cooling step at a speed sufficiently slow to prevent fissuring.
26. Machinable product according to claim 25, wherein said alloy comprises between 6% and 8% of Ni, between 4 and 6% of Sn and 25 between 0.5 and 2% of Pb. MFTArI -.- PCT 18
27. Machinable product according to claim 25, wherein said alloy comprises between 8% and 10% of Ni, between 5 and 7% of Sn and between 0.5 and 2% of Pb.
28. Machinable product according to claim 25, wherein said 5 alloy comprises between 14% and 16% of Ni, between 7 and 9% of Sn and between 0.5 and 2% of Pb.
29. Machinable product according to claim 25, wherein said homogenizing treatment is performed in a through-type furnace.
30. Machiiable product according to claim 25, wherein said 10 heat treatment is followed by a step of cold deformation by rolling, wire drawing, stretch-forming or hammering and a recrystallization step followed by a cooling step at a speed sufficiently slow to prevent fissuring.
31. Machinable product according to claim 25, wherein the speed of said cooling step is sufficiently high to limit the formation of a 15 two-phased structure.
32. Machinable product according to claim 25, wherein said heat treatment takes places at a temperature comprised between 690*C and 920"C,
33. Machinable product according to claim 25, wherein the 20 transversal dimension of said metallic product during said heat treatment is comprised between 1mm and 100mm.
34. Machinable product according to claim 25, wherein said cooling step of said heat treatment has a cooling speed comprised between 10*C/min and 24000*C/min. 25
35. Machinable product according to claim 25, wherein said cooling step of said heat treatment has a cooling speed comprised between 1 0*C/min and 4000*C/min. CRA:rAl .2..DCT 19
36. Machinable product according to claim 25, wherein said cooling step of said heat treatment has a cooling speed comprised between 100*C/min and 1500*C/min.
37. Machinable product according to claim 25, wherein said 5 cooling step of said heat treatment has a cooling speed comprised between 1004C/min and 1000*C/min.
38. Machinable product according to claim 25, comprising a step of spinodal hardening.
39. Machinable product according to claim 25, comprising up 10 to 10% or more of the following elements: Fe, Zn, Mn and/or up to 5% or more of the following elements: Zr, Nb, Cr, Al, Mg.
40. Machinable product, composed of an alloy comprising between 8% and 10% of Ni, between 5 and 7% of Sn and between 0.5% and 2% of Pb, the remainder being constituted essentially of Cu. 15
41. Machinable prodUct according to claim 40, characterized by a machinability index greater than 80%.
42. Machinable product according to claim 40, containing up to 10% or more of the following elements: Fe, Zn, Mn and/or up to 5% or more of the following elements: Zr, Nb, Cr, Al, Mg. rAA-TAI .'..D"T
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/EP2004/050449 WO2005108631A1 (en) | 2004-04-05 | 2004-04-05 | Free-cutting, lead-containing cu-ni-sn alloy and production method thereof |
Publications (2)
| Publication Number | Publication Date |
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| AU2004319350A1 true AU2004319350A1 (en) | 2005-11-17 |
| AU2004319350B2 AU2004319350B2 (en) | 2010-07-08 |
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| US (1) | US20070089816A1 (en) |
| EP (1) | EP1737991A1 (en) |
| JP (1) | JP2007531824A (en) |
| KR (1) | KR20070015929A (en) |
| CN (1) | CN1961089A (en) |
| AU (1) | AU2004319350B2 (en) |
| BR (1) | BRPI0418718A (en) |
| CA (1) | CA2561903A1 (en) |
| IL (1) | IL178448A (en) |
| MX (1) | MXPA06011498A (en) |
| NO (1) | NO20064876L (en) |
| NZ (1) | NZ550305A (en) |
| WO (1) | WO2005108631A1 (en) |
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| DE102006027844B4 (en) * | 2005-06-22 | 2019-10-31 | Wieland-Werke Ag | Copper alloy based on copper and tin |
| US20070253858A1 (en) * | 2006-04-28 | 2007-11-01 | Maher Ababneh | Copper multicomponent alloy and its use |
| RU2508415C2 (en) * | 2009-04-08 | 2014-02-27 | Свиссметал-Юмс Швайцерише Металлверке Аг | Copper-based alloy treated by cutting, and method for its production |
| CN106435250A (en) * | 2009-04-08 | 2017-02-22 | 瑞士金属-Ums瑞士金属加工有限公司 | Machinable copper base alloy and production method thereof |
| CN101709407B (en) * | 2009-11-06 | 2011-09-28 | 江阴新华宏铜业有限公司 | Preparation method of ferrimanganic copper-nickel tube |
| US20110226219A1 (en) * | 2010-03-17 | 2011-09-22 | Caterpillar Inc. | Fuel lubricated pump and common rail fuel system using same |
| US9181606B2 (en) | 2010-10-29 | 2015-11-10 | Sloan Valve Company | Low lead alloy |
| CN102615491B (en) * | 2011-01-31 | 2015-05-20 | 肖克建 | Processing method for copper material |
| CN102304642B (en) * | 2011-08-26 | 2012-10-24 | 河南科技大学 | Cast wear-resistant tin bronze alloy and preparation method thereof |
| CN102321826B (en) * | 2011-08-26 | 2012-10-03 | 河南科技大学 | Extruded high-tin bronze alloy and preparation method thereof |
| JP2015531829A (en) * | 2012-08-22 | 2015-11-05 | バオシダ スイスメタル アーゲーＢａｏｓｈｉｄａ Ｓｗｉｓｓｍｅｔａｌ Ａｇ | Machinable copper alloy for electrical connectors |
| JP6340408B2 (en) * | 2013-03-14 | 2018-06-06 | マテリオン コーポレイション | Ultra high strength copper-nickel-tin alloy |
| CN107354414B (en) * | 2013-03-15 | 2019-11-29 | 美题隆公司 | Metastable alloy and product with uniform grain size |
| JP6190674B2 (en) * | 2013-09-09 | 2017-08-30 | 古河電気工業株式会社 | Copper alloy sheet and manufacturing method thereof |
| DE112015001296T5 (en) | 2014-03-17 | 2016-12-29 | Materion Corporation | High strength, homogeneous copper-nickel-tin alloy and manufacturing process |
| CN104388743A (en) * | 2014-11-05 | 2015-03-04 | 无锡阳工机械制造有限公司 | Brine corrosion resistant alloy |
| CN104388742A (en) * | 2014-11-05 | 2015-03-04 | 无锡阳工机械制造有限公司 | Brine corrosion resistant alloy |
| CN104372200A (en) * | 2014-11-14 | 2015-02-25 | 无锡阳工机械制造有限公司 | Brine-corrosion-resistant alloy |
| CN105483430B (en) * | 2016-01-29 | 2017-11-14 | 罗仙花 | A kind of preparation method of high intensity high filtration flux Cu alloy material |
| CN105734471B (en) * | 2016-05-12 | 2017-09-29 | 中国兵器工业第五九研究所 | A kind of Ultra-fine grain copper material homogenizes preparation method |
| EP3273307A1 (en) * | 2016-07-19 | 2018-01-24 | Nivarox-FAR S.A. | Part for clock movement |
| EP3273306A1 (en) * | 2016-07-19 | 2018-01-24 | Nivarox-FAR S.A. | Part for clock movement |
| CN106119581A (en) * | 2016-07-29 | 2016-11-16 | 柳州豪祥特科技有限公司 | A kind of preparation technology of powdered metallurgical material |
| CN106086492B (en) * | 2016-07-29 | 2018-10-02 | 柳州豪祥特科技有限公司 | The preparation process of copper based powder metallurgy material |
| CN106065444B (en) * | 2016-07-29 | 2018-10-02 | 柳州豪祥特科技有限公司 | The method that powder metallurgic method prepares corronil material |
| CN106345811A (en) * | 2016-09-01 | 2017-01-25 | 史汉祥 | Method for manufacturing brass rod wire |
| BE1025772B1 (en) * | 2017-12-14 | 2019-07-08 | Metallo Belgium | Improvement in copper / tin / lead production |
| CN109750184B (en) * | 2019-03-08 | 2020-11-03 | 金华市程凯合金材料有限公司 | Preparation method of high-fine-grain atomized copper alloy powder |
| JP7433262B2 (en) | 2020-03-30 | 2024-02-19 | 日本碍子株式会社 | Method for manufacturing Cu-Ni-Sn alloy and cooler used therein |
| JP7433263B2 (en) | 2021-03-03 | 2024-02-19 | 日本碍子株式会社 | Manufacturing method of Cu-Ni-Sn alloy |
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| US4406712A (en) * | 1980-03-24 | 1983-09-27 | Bell Telephone Laboratories, Incorporated | Cu-Ni-Sn Alloy processing |
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| JPH02129328A (en) * | 1988-11-09 | 1990-05-17 | Nishidai Densen Kogyo Kk | Free-cutting spinodal copper alloy |
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| DE4121994C2 (en) * | 1991-07-03 | 1995-06-08 | Wieland Werke Ag | Process for producing a copper-nickel-tin alloy and its use |
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| JPH08283889A (en) * | 1995-04-14 | 1996-10-29 | Chuetsu Gokin Chuko Kk | High strength and high hardness copper alloy |
| DE69941805D1 (en) * | 1998-02-24 | 2010-01-28 | Taiho Kogyo Co Ltd | BEARING FOR INTERNAL COMBUSTION ENGINE |
-
2004
- 2004-04-05 WO PCT/EP2004/050449 patent/WO2005108631A1/en active Application Filing
- 2004-04-05 CN CNA2004800432423A patent/CN1961089A/en active Pending
- 2004-04-05 BR BRPI0418718-0A patent/BRPI0418718A/en not_active Application Discontinuation
- 2004-04-05 KR KR1020067020938A patent/KR20070015929A/en not_active Application Discontinuation
- 2004-04-05 AU AU2004319350A patent/AU2004319350B2/en not_active Ceased
- 2004-04-05 EP EP04725712A patent/EP1737991A1/en not_active Withdrawn
- 2004-04-05 NZ NZ550305A patent/NZ550305A/en not_active IP Right Cessation
- 2004-04-05 JP JP2007506666A patent/JP2007531824A/en active Pending
- 2004-04-05 MX MXPA06011498A patent/MXPA06011498A/en unknown
- 2004-04-05 CA CA002561903A patent/CA2561903A1/en not_active Abandoned
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2006
- 2006-10-03 US US11/542,508 patent/US20070089816A1/en not_active Abandoned
- 2006-10-04 IL IL178448A patent/IL178448A/en not_active IP Right Cessation
- 2006-10-26 NO NO20064876A patent/NO20064876L/en not_active Application Discontinuation
Also Published As
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|---|---|
| CA2561903A1 (en) | 2005-11-17 |
| KR20070015929A (en) | 2007-02-06 |
| NO20064876L (en) | 2006-12-21 |
| EP1737991A1 (en) | 2007-01-03 |
| NZ550305A (en) | 2010-07-30 |
| IL178448A0 (en) | 2007-02-11 |
| AU2004319350B2 (en) | 2010-07-08 |
| MXPA06011498A (en) | 2007-03-21 |
| JP2007531824A (en) | 2007-11-08 |
| WO2005108631A1 (en) | 2005-11-17 |
| CN1961089A (en) | 2007-05-09 |
| BRPI0418718A (en) | 2007-09-11 |
| US20070089816A1 (en) | 2007-04-26 |
| IL178448A (en) | 2011-06-30 |
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