WO2006016614A1 - 銅合金改質用マスターアロイおよびそれを用いる鋳造方法 - Google Patents
銅合金改質用マスターアロイおよびそれを用いる鋳造方法 Download PDFInfo
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- WO2006016614A1 WO2006016614A1 PCT/JP2005/014678 JP2005014678W WO2006016614A1 WO 2006016614 A1 WO2006016614 A1 WO 2006016614A1 JP 2005014678 W JP2005014678 W JP 2005014678W WO 2006016614 A1 WO2006016614 A1 WO 2006016614A1
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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
- C22C9/04—Alloys based on copper with zinc as the next major constituent
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- A—HUMAN NECESSITIES
- A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
- A61P—SPECIFIC THERAPEUTIC ACTIVITY OF CHEMICAL COMPOUNDS OR MEDICINAL PREPARATIONS
- A61P11/00—Drugs for disorders of the respiratory system
- A61P11/06—Antiasthmatics
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
- B22D21/022—Casting heavy metals, with exceedingly high melting points, i.e. more than 1600 degrees C, e.g. W 3380 degrees C, Ta 3000 degrees C, Mo 2620 degrees C, Zr 1860 degrees C, Cr 1765 degrees C, V 1715 degrees C
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
- B22D21/025—Casting heavy metals with high melting point, i.e. 1000 - 1600 degrees C, e.g. Co 1490 degrees C, Ni 1450 degrees C, Mn 1240 degrees C, Cu 1083 degrees C
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
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- 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
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- 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
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/06—Alloys containing less than 50% by weight of each constituent containing zinc
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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
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- 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
Definitions
- the present invention is used in a forging method such as a continuous forging method, a semi-molten forging method, a sand mold forging method, a mold forging method, a low pressure forging method, a die casting, a lost wax, an upcast, a squeeze, and a centrifugal forging method.
- the present invention relates to a master alloy for producing a copper alloy for grain refinement and a method for producing a modified copper alloy using the same.
- the refinement of copper alloy crystal grains improves 0.2% resistance to strength (the strength when permanent strain becomes 0.2%, and may be simply referred to as “proof strength” in the following). This is extremely effective in this regard and is highly desired.
- the resistance to corrosion is determined by the Hall-P etch relational expression (EO Hall, Proc. Phys. Soc. London. 64 (1951) 747. and NJ Petch, J. Iron Steel Inst. 174 (1953 ) From the relational expression of 25)), the crystal grain size D increases in proportion to the power of 1Z2 (D_1 / 2 ).
- the basic form of crystal grain refinement of copper alloys is that (A) the crystal grains become finer when the copper alloy is melted and solidified, and (B) the melted and solidified copper alloy (ingot, slab, etc. , Forged products including die casts, molten forged products, etc.), and the storage energy such as strain energy generated by processing or heat treatment is used as a driving force to refine crystal grains.
- Patent Document 1 JP 2004-100041 A
- Patent Document 2 JP 2002-356728 A
- the constituent elements of a copper alloy are selected and determined so as to have characteristics according to the intended use of the copper alloy.
- modified copper alloys the copper alloy “t, u” is crystallized compared to the copper alloy to be modified.
- each of the methods (b) and (c) has a problem when it takes a large force or time, and has a large shape and a large amount of a shape that is determined by continuous operation. When forging an ingot obviously, it is naturally unsuitable for small, complex shaped bag articles. In addition, there are few industrial advantages that do not realize effective miniaturization to such an extent that it surpasses the problem of the fabrication process.
- the method (d) has the following problems.
- the rapid solidification method such as die-casting has a significant limitation on the solidification shape and production form to which this can be applied, and the rapid solidification method using a cooling metal is local, and there are restrictions on the installation location, etc. Also, the degree of miniaturization is small.
- the method (e) (f) is intended to reduce the grain size during solidification, and is a technology that is fundamentally different from the methods (a) to (d).
- the crystal grain refinement is achieved only when there is equipment (for example, a rolling mill, a wire drawing machine, or a forging machine) to add new energy and add it.
- the energy required for realization and running costs are enormous.
- An object of the present invention is to provide a method for producing a modified copper alloy capable of refining crystal grains at the time of melting and solidification without causing problems in such a conventional method.
- Zr is an active and high melting point metal, it is difficult to control it within a predetermined narrow addition amount range. Even if Zr is added to a copper alloy in a predetermined amount, When Zr is consumed in an acid or sulfur form, it no longer contributes to grain refinement. On the other hand, a large amount of added Zr has a crystal grain refinement effect. In addition to saturation, the function of refining is lost, the crystal grains become larger, and characteristics such as electrical and thermal conductivity are impaired. In addition to these, copper alloy members containing a large amount of Zr depend on the atmosphere during melting and the raw materials used when they are re-dissolved when they are recycled (various manufacturing processes (material-product), waste products, etc.). In Zr, a large amount of oxides and sulfides are generated by Zr, and a good structure cannot be made.
- the present invention is an alloy form consisting of Cu: 40 to 80%, Zr: 0.5 to 35%, and the balance Zn, or Cu added to it with P: 40 to 80%, Zr: 0.5 It is in the master alloy for copper alloy fabrication which is an alloy form consisting of ⁇ 35%, P: 0.01 ⁇ 3%, and the balance Zn.
- the master alloy of the present invention further has a Mg: 0.0 1 to 1%, Al: 0.01 to 5%, Sn: 0.1 to 5%, B: 0.01 to 0.5% in order to facilitate the residual Zr in the molten metal.
- Mn: 0.01 to 5% and Si: 0.01 to 1% are preferably included.
- the master alloy of the present invention By using the master alloy of the present invention, even if a small amount of Zr is added, it is not affected by acid or sulfur, and metal Zr can be present together with P when the molten metal is solidified. Thus, it is easy to crystallize primary grains and crystal grains. Further, according to the present invention, when producing a copper alloy by forging a molten copper alloy containing Zr and P, at least Zr is in the form of Cu-Zn-Zr or Cu-Zn-Zr-P. It can be added by master alloy to produce a modified copper alloy. In the above forging method, the metal Zr concentration in the molten metal required for crystal refinement is 5 ppm or more, preferably 2 Oppm or more. Since it is easy to control to 500 ppm or less, it is possible to efficiently crystallize primary crystal alpha and refine crystal grains.
- FIG. 2 A microstructure of a 76Cu-3Si-21Zn forged product prepared using the master alloy of sample No. 1 shown in Table 1 and observed with a metallographic microscope.
- FIG. 3 Macro structure of 7 6Cu-3Si-21Zn forged using master alloy (50Cu-50Zr) of sample No. 13 shown in Table 1 is there.
- FIG. 4 is a microstructure diagram of a 76Cu-3Si-21 Zn forged product fabricated using the master alloy of Sample No. 13 shown in Table 1 and observed with a metallographic microscope.
- Cu 40 to 80%
- Zr 0.5 to 35%
- the balance is the form of an alloy that also has a force with Zn
- Zr 0.5 Ability to provide a master alloy composed of ⁇ 35%
- the balance Zn the balance Zn.
- Cu Since it is a master alloy of copper alloy, it is a main element. However, just adding Zr to pure Cu (melting point: 1083 degrees) does not reduce the melting point much (it takes time for the master alloy to melt: As a result, Zr is lost, and it is lost in the alloy. Zr oxide formation is increased, resulting in invalid Zr). Further, Cu alone cannot prevent Zr loss during melting of the master alloy and formation of Zr oxide in the alloy. Zr acid loss, sulfide loss, and additional elements to prevent Zr oxide formation in the alloy are required. However, even if other alloying elements (Zn) are added, if Cu exceeds 80%, the above three points (melting point, Zr loss, existence of effective Zr) are insufficient. However, If the alloy system does not contain Zn, it will inevitably be high Cu-low Zn.
- the lower limit is set to 40% because the melting point (liquidus temperature) is hardly lowered unless the Cu amount is less than 0%, and rather a high melting point Zr compound is formed. It is also the power to do. Also, if the Cu content is reduced, that is, if the remaining Zn content is too high, the vaporization of Zn becomes too high during the production of the master alloy, and the melting temperature cannot be raised, making it difficult to produce the master alloy.
- Zr important as a refining element during solidification. Alloying will lower the melting point (liquidus temperature). In other words, the melting point of Zr is 1850 degrees, the Cu-Zr intermediate alloy is 1000 to 1120 degrees, and the copper alloy has a liquidus temperature of 870 to 1050 degrees, a melting temperature of 950 to 1200 degrees, and a filling temperature Is between 890 and 1150 degrees. The master alloy must be below the liquidus of the copper alloy. In addition, when Zr is dissolved in an acidic atmosphere, loss of Zr starts at the same time as dissolution. If dissolution takes time, the amount of Zr does not reach the specified level. Therefore, the lower the melting point, the better.
- the lower limit of Zr is set to 0.5%, 100 times the required amount of 0.005%, taking into consideration economic problems and labor of charging.
- the upper limit of Zr is better with higher Zr, but the melting point does not decrease. Taking into account that the liquidus temperature should be kept below 35%.
- the preferred range is 1-20%, the more preferred range is 1-10% and the optimum range is 2-6%.
- Zn a low-melting intermetallic compound of Zr, Zn, and Cu can be formed, and the melting point becomes lower than that of the matrix portion.
- oxygen exists in the molten metal, and before the oxygen forms Zr oxides, it forms a small amount of Zn oxide to reduce the amount of oxygen in the molten metal. It prevents the acid. Therefore, the force depending on the oxygen concentration of the molten metal Zr and Zn are preferable. More preferably 2Zr Zn, and most preferably 3Zr Zn. However, the amount of Zr and Zn must be in an appropriate relationship depending on the amount of Zn allowed as the impurity concentration.
- the best mode composition is Cu 50 to 65%, Zrl to 10% (2 to 6%), and the balance Zn.
- the melting point is the lowest and Zr in the master alloy melts, more Zn than Zr dissolves at the same time, preventing Zr acid loss and Zr acid formation. It is also power.
- P force that is an essential element Cu—Zr—P—Zn It is also possible to add Cu—P in the form of an alloy element without being made into an alloy element.
- the amount of additive is Cu-7-20% P, preferably Cu-10-15% P is used, and Cu-Zr-0.01-3% P-Zn is used in the case of Cu-Zr-P-Zn.
- the master alloy of the present invention further comprises Mg: 0.01 to 1%, Al: 0.01 to 5%, Sn: 0.1 to 5%, B: 0.01 to 0.5%, Mn: 0.01 to 5%, Si : It is preferable to include at least one selected from the group consisting of 0.01 to 1% strength.
- Mg contains 0.005 mass% or more of Mg before Zr charging
- the S component in the melt is removed or fixed in the form of MgS.
- Mg contains 0.005 mass% or more of Mg before Zr charging
- Mg is added excessively, it will acidify like Zr and cause defects such as entrainment of acid.
- Mn also has the effect of removing S components, although not as much as Mg.
- Sn alone has little effect on the miniaturization effect, but it exhibits a remarkable miniaturization function in the presence of Zr and P.
- Sn improves mechanical properties (strength, etc.), corrosion resistance, and wear resistance, and also has the function of breaking up the dendrite arm and making the crystal grains finer and finer. It is particularly prominent in the presence.
- the gamma phase produced by Sn-added powder suppresses the growth of crystal grains after melting and solidification, and contributes to the refinement of crystal grains.
- Sn exceeds 5%
- a high melting point Zr—Sn—Cu intermetallic compound having a melting point exceeding 1000 ° C. may be formed. Therefore, Sn and Zn are preferably satisfied.
- A1 improves the molten metal flow and prevents Zr oxidation and sulfur loss.
- Zr and P By co-adding Zr and P, A1 has a positive effect on the remarkable grain refinement effect in the forging stage. give.
- A1 like Sn, has a function of dividing the dendrite arm and granulating crystal grains, and further improves strength, wear resistance, and the like.
- the master alloy can be manufactured by the following method.
- the Zn concentration at that time should be 3-25% due to the relationship between the molten metal temperature and the Zn vapor pressure.
- the temperature of the molten metal is raised to 1100 to 1200 degrees, a predetermined amount of commercially available Cu—10 to 60% Zr is charged, and finally low melting point Zn is charged.
- B and Mg active metals
- These intermediate alloys can be cast into shapes such as boats, grains, etc., or made into rods or lines by continuous forging.
- a large bowl is made and formed into a wire, bar, plate, or thin plate shape by hot extrusion or hot rolling.
- a powerful master alloy ensures that a predetermined concentration of Zr is present in the molten copper alloy in the presence of predetermined P by once or continuously charging it into a melting furnace, holding furnace, tundish, etc. Can do.
- components other than Zr are included in the composition range of a given alloy.
- additional elements for desulfurization and deoxidation Mg, Sn, Al, Mn, and Si are added as appropriate within the alloy's effective component range (or less than the impurity concentration), and desulfurization and deoxidation Do it just in case.
- melting furnaces, dredging, tundish, and distributors are covered with charcoal in order to isolate them from the atmosphere.
- the refined element P it is better to put the deficiency as Cu-P (generally 10-15% P) into the melting furnace.
- a Zr master alloy containing Zr concentration and subcomponents is selected depending on the type of alloy (melting point, additive element, etc.).
- the master alloy is charged into the melting furnace so that Zr becomes a predetermined amount. Then, forge. However, it takes time to complete the forging (semi-continuous forging), and Zr is oxidized in a melting furnace. In order to make up for this, the shortage of Zr in the tundish and distributor immediately before filling is continuously applied to a granular master alloy with a size of several millimeters to 20 mm, or a linear or rod-shaped master alloy. Or add it at regular intervals. At this time The master alloy is naturally selected to be lower than the penetration temperature of the alloy. If the master alloy is completely dissolved in the tundish or distributor without stirring within 1 minute, add Zr with high accuracy if the dissolution loss during fabrication is measured in advance. it can.
- Another method is to pour the molten metal after deoxidation, desulfurization and P addition to the tundish or distributor, and first add the master alloy so that the Zr concentration becomes a predetermined amount. Added. While producing continuously, granular, linear, or rod-shaped master alloy with a size of several millimeters to 20mm is continuously charged into the tundish or distributor. If the amount of Zr required is 50 ppm, the master alloy of 5% Zr is calculated to be only 1/1000 addition, so there is no problem! / ⁇ . Zr should be added in an amount commensurate with the loss, for example 1 to 40%, even in a master alloy alloy in a tundish or distributor.
- the first condition is to melt quickly (the second is not to oxidize), so it contains l-10% Zr and the Cu concentration is 50-65%.
- Preferred is a secondary alloy master alloy that lowers the melting point of the alloy as appropriate.
- Zr is important to melt quickly. The loss of Zr is small. It is important that Zr is not in the form of oxide and / or sulfate.
- This type of forging method has a melting furnace with a relatively good sealing degree, and there are many types of melting furnaces in which raw materials are sequentially added to match the manufactured product while making the manufactured product.
- the melting furnace temperature will decrease and this will lead to a reduction in the forging temperature. Therefore, batch raw material charging should not be performed except for joints in the morning, noon, night, etc. It is common. In other words, it is usual to charge a small amount of raw material so that the temperature change is small. There are two main methods for this continuous operation.
- the master alloy is obtained by cutting a granular material, bar, wire, boat shape, etc. into a predetermined length.
- wastewater such as runners, where there is little oxidation and sulfur slag, process waste that occurs sequentially, defective products are also actively used in continuous operation.
- the master alloy is added in consideration of the amount of Zr contained. When waste products are used as raw materials, they are used at the joint of work. In this case, Zr master alloy is added after sufficiently deoxidizing and desulfurizing the molten metal with Mg or A1.
- the forging method of the present invention is a copper alloy in which, when a small amount of Zr is added in the presence of P, a primary alpha phase is crystallized, and a peritectic reaction or a eutectic reaction occurs during solidification to refine crystal grains.
- Cu-Zn, Cu-Zn-Si, Cu-Zn-Sn, Cu-Zn-Al, Cu-Zn-Pb, Cu-Zn-Bi, Cu-Zn-Si- Mn, Cu—Zn—Si—Pb, Cu—Zn—Si—Sn, Cu—Zn—Si—Al, Cu—Zn—Sn—Pb, Cu—Zn—Sn—Bi, Cu—Zn—Sn—Al, Cu—Sn, Cu—Sn—Pb, Cu—Sn—Bi, Cu—Al, Cu—Al—Si, Cu—Si, Cu—Cr, Cu—Pb, Cu—P, and Cu—Te are exemplified.
- the master alloy shown in Table 4 below is adjusted and used within the range of the above-described composition ratio.
- a small amount of Zr in the presence of P preferably 0.01 to 0.35 mass%, that is, 5 ppm or more, preferably 20 ppm or more and 500 ppm or less.
- Zr alone can only slightly refine copper alloy crystal grains, but it is extremely effective in coexistence with P. It is a thing that demonstrates. Such a function is demonstrated when the Zr content is 5 ppm or more. The power refinement function is remarkably exhibited when Zr is added at 1 Oppm or more, and more significantly when Zr is added at 20 ppm or more. Will be. Therefore, the Zr content needs to be 5 ppm or more. In particular, the Zr content is preferably 10 ppm or more, more preferably 20 ppm or more. However, the minimum value of the amount of Zr at which the crystal grain refining function by Zr is exhibited in the presence of P greatly depends on the composition of the matrix.
- the amount of Zr added which does not form oxides and sulfates, be 500 ppm or less, more preferably 300 ppm or less. It is optimal to keep it below 200 ppm.
- the amount of Zr is set in such a range, even when the modified copper alloy is dissolved in the air as a reusable material, the generation of Zr oxides and sulfides is reduced, and a healthy state is obtained again.
- a modified copper alloy can be obtained and can be easily converted to a modified copper alloy.
- Zr is added in the form of a granular material, a thin plate-shaped material, or an intermediate alloy material having these shapes, just before the ingot, so that the acid product and the sulfated product are produced during the fabrication. It is preferable that Zr which does not form the above is added. That is, Zr is easy to oxidize as described above. Therefore, it is better to add Zr just before pouring when making it.
- the melting point of Zr is 800 to 1000 degrees higher than the melting point of the copper alloy
- the granular material particle size: about 2 to 50 mm
- thin plate thickness: about 1 to about LOmm
- a master alloy in the form of a low-melting-point alloy which is an intermediate alloy material made of these granular materials and thin-plate-like materials, which is close to the melting point of the copper alloy and contains many necessary components.
- P like Zr, can only slightly refine the forged structure by itself, but exhibits a remarkable miniaturization function in the presence of Zr, Zr, or Si.
- Such a miniaturization function is exerted by keeping the P content at 100 ppm (0.01 mass%) or more and Si is not co-added. In this case, it will be noticeable if the P content is 200 ppm or more, and more prominent if it is 300 ppm or more.
- the P content is 0.35 mass% or more, the above-mentioned function saturates.
- the P content is preferably set to 0.25 mass% or less, more preferably 0.2 mass% or less, and most preferably 0.15 mass% or less.
- an intermetallic compound of Zr and P is considered to be present in the crystal refinement, and the amount between them is 0.5 PZZr 150, preferably 1 PZZr 50, more preferably 1.2. It is preferable that the relationship PZ Zr 25 holds.
- primary alpha can be crystallized during solidification, and beta phase can be crystallized by peritectic reaction or eutectic reaction, thereby achieving crystal refinement.
- the present invention realizes refinement of crystal grains at the forging stage, the hot workability of the copper alloy itself is improved. After forging, rolling, forging, extrusion, wire drawing, etc. Even when this process is performed, the processing can be performed satisfactorily.
- forging sand mold forging, mold forging, low pressure forging, continuous forging, die casting, squeeze, lost wax, etc., precision forging, semi-solid (semi-solidification method) or molten metal forging.
- the strength of the copper alloy structure is improved by the method of the obtained product, lumps, ingots, slabs, etc.
- a hot extruded material of the copper alloy to be modified is equivalent to a drawn grain size. Because of its strength, it can be used as a substitute for these extruded materials and drawn materials (or forging materials that use these as raw materials), making it possible to omit processing steps such as extrusion, and greatly producing them. Costs can be reduced and energy can be saved.
- the primary crystal at the time of melt-solidification is an alpha phase in order to effectively refine the crystal grains at the time of melt-solidification.
- the phase structure has a beta phase with an area ratio of 95% or less and the phase structure at room temperature after melting and solidification has a beta phase with an area ratio of 50% or less.
- the beta phase is 20% or less, and the beta phase is preferably transformed into alpha, kappa, gamma, delta, and mu phases.
- the phase structure in the high-temperature state immediately after melt solidification includes the beta phase, the kappa phase, the gamma phase, and the delta phase. It is preferable to include 5 to 95% in area ratio (total).
- the phase structure in the normal temperature state after melt-solidification includes one to four phases selected from among the alpha phase, the beta phase, the kappa phase, the gamma phase, the delta phase, and the neutral phase.
- the kappa phase, the gamma phase, the delta phase, and the mu phase which are observed in the normal temperature state after melting and solidification, do not adversely affect the refinement of crystal grains.
- the presence of these phases has a good effect on the refining effect, and the refining effect is particularly remarkable when there are many kappa phases and Z or gamma phases.
- the corrosion resistance of the fabricated product (such as mold ware) Problems with ductility may occur, but the most difficult problem is to apply an appropriate heat treatment to the fabricated product (eg 400 to 600 degrees, 10 minutes to 4 hours) It can be solved by applying heat treatment under the conditions of That is, the beta phase is not lost by heat treatment and can be divided. The disappearance and division of the solid phase by such heat treatment is more effectively performed as the crystal grains become finer.
- the two-dimensional form of the solid phase at the time of melt solidification or the normal temperature state after the melt solidification is obtained.
- the two-dimensional morphology of the crystal grains or alpha phase in the dendrite arm is preferably divided into a circular shape or a non-circular shape close to this. That is, it is preferable that these two-dimensional form force dendrite arms have a divided shape, a circular shape, an elliptical shape, a cross shape, a needle shape, or a polygonal shape.
- forged products in which the above two-dimensional form is close to a circle and it is strongly desired to form a forged structure (forged products, including ingots, ingots, slabs, die casts, etc., molten forged products) Etc.) is in a dendrite arm network state, the fluidity of the molten metal deteriorates and large defects such as nests, sinkholes, blowholes, and forged cracks occur in the forged material.
- the two-dimensional shape is circular or approximate to this, and the solid phase is granulated, the microscopic fluidity is greatly improved, and a good quality forged product can be obtained.
- This improvement in fluidity is beneficial and practical when using a semi-molten forging method or semi-molten forging method that is molded in a semi-molten state (solid phase + liquid phase). It will be.
- a refinement process as a pretreatment for example, refinement of crystal grains by steering, electromagnetic induction stirring or hot working (hot extrusion, drawing, etc.)
- This is especially suitable for thixocasting.
- the crystal grains have a fine shape close to a circle, it has a great resistance to cracks caused by thermal strain immediately after melting and solidification, and also when used as an ingot. As a result, the hot deformability is improved, and the hard-to-heat processed material can be easily obtained without causing cracks.
- the size of the crystal grains was refined by extrusion and drawing and rolling. It is almost the same as copper alloy, and mechanical strength is almost the same or rather higher. In this way, it is important to note that a forged product that has only been melted and hardened in a predetermined composition has a mechanical strength equivalent to that of a forged product in which a large amount of energy such as rolling is stored. It should be worthy.
- the resistance of the forged product (0.2% resistance to the agglomerates in the state after melting and solidification) is higher than that of the to-be-modified copper alloy forged under the same forging conditions due to the refinement of crystal grains. 10% or more (preferably 20% or more, more preferably 30% or more, optimally 40% or more).
- the master alloys shown in Table 1 to Table 3 below are manufactured by the above master alloy manufacturing method.
- alloy l 76Cu-3Si-21Zn alloy was calculated with 75ppmZr + 0.06% P, and the optimum amount of Zr (which does not form an acid / sulfuric acid form) 25 to 75 ppm.
- Cu-35Zr and Cu-50Zr alloys were added with a predetermined amount.
- Each master alloy was cut so that one side became a cube of about 5 mm, and further cut again to a predetermined amount.
- the filling temperature is generally a liquidus temperature plus 30 to 150 degrees, and if it is too high, forging defects such as cracks are likely to occur.
- the melting temperature is generally about 50 ° C. added to the penetration temperature taking into account the temperature drop due to soot and the like. Increasing the temperature unnecessarily leads to wasted energy.
- the resulting porcelain was excised 40 mm from the bottom and the spout (up and down), and after polishing the surface, macrostructures appeared with nitric acid, using a full size and a 7.5x magnifier Then, the size of the crystal grains was measured by a JIS comparison method.
- Fig. 1 shows a 76Cu-3Si-21Zn forged product prepared using the master alloy (62Cu-3Zr-35Zn) of sample No. 1 shown in Table 1, with the surface treated with nitric acid. 7. Macro structure observed with a 5X magnifier.
- Fig. 2 shows a 76Cu-3Si-21Zn forged product prepared by using the master alloy of sample No. 1 shown in Table 1.
- FIG. 3 is a microstructural view of the surface treated with hydrogen peroxide and ammonia and observed with a metallographic microscope. This forged alloy had a crystal grain size of 50 m or less, and it was found that the forged alloy was refined.
- FIG. 3 shows a 76Cu-3Si-21Zn forged product prepared using the master alloy (50Cu-50Zr) of Sample No. 13 shown in Table 1 with its surface treated with nitric acid.
- Fig. 4 shows the macro structure observed with a magnifier of 5 times.
- Fig. 4 shows a 76Cu-3Si-21Zn forged product prepared using the master alloy of Sample No. 13, and the surface thereof is made of hydrogen peroxide and ammonia. It is a microstructure observed with a metallographic microscope after processing with This master alloy has a grain size of 150 / zm!
- An alloy having a specific composition for each alloy system shown in Table 4 is 60 ⁇ Cu-3.5Si-l.
- the refined copper alloy can be refined in a cast, squeeze, centrifugal forging, welding, lining, overlay or overlay.
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US10/597,568 US20080253924A1 (en) | 2004-08-10 | 2005-08-10 | Master Alloy for Casting a Modified Copper Alloy and Casting Method Using the Same |
MXPA06011720A MXPA06011720A (es) | 2004-08-10 | 2005-08-10 | Aleacion maestra para uso en la modificacion de aleaciones de cobre y metodo de fundicion que la utiliza. |
DE602005024006T DE602005024006D1 (de) | 2004-08-10 | 2005-08-10 | Verwendung von vorlegierung zur modifizierung von kupferlegierung und giessverfahren damit |
AU2005272455A AU2005272455B2 (en) | 2004-08-10 | 2005-08-10 | Master alloy for use in modifying copper alloy and casting method using the same |
EP05770571A EP1777309B1 (en) | 2004-08-10 | 2005-08-10 | Use of master alloy for modifying copper alloy and casting method using the same |
CN2005800194129A CN1969051B (zh) | 2004-08-10 | 2005-08-10 | 铜合金铸造用中间合金及其铸造方法 |
AT05770571T ATE483826T1 (de) | 2004-08-10 | 2005-08-10 | Verwendung von vorlegierung zur modifizierung von kupferlegierung und giessverfahren damit |
CA2561295A CA2561295C (en) | 2004-08-10 | 2005-08-10 | Master alloy for casting a modified copper alloy and casting method using the same |
JP2006531691A JP4486966B2 (ja) | 2004-08-10 | 2005-08-10 | 銅合金改質用マスターアロイおよびそれを用いる鋳造方法 |
US14/534,807 US20150132179A1 (en) | 2004-08-10 | 2014-11-06 | Master alloy for casting a modified copper alloy and casting method using the same |
US16/802,844 US20200190630A1 (en) | 2004-08-10 | 2020-02-27 | Master alloy for casting a modified copper alloy and casting method using the same |
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US10/597,568 A-371-Of-International US20080253924A1 (en) | 2004-08-10 | 2005-08-10 | Master Alloy for Casting a Modified Copper Alloy and Casting Method Using the Same |
US14/534,807 Division US20150132179A1 (en) | 2004-08-10 | 2014-11-06 | Master alloy for casting a modified copper alloy and casting method using the same |
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PCT/JP2005/008662 WO2006016442A1 (ja) | 2004-08-10 | 2005-05-02 | 結晶粒が微細化された銅基合金鋳物 |
PCT/JP2005/014698 WO2006016630A1 (ja) | 2004-08-10 | 2005-08-10 | 銅合金鋳物及びその鋳造方法 |
PCT/JP2005/014678 WO2006016614A1 (ja) | 2004-08-10 | 2005-08-10 | 銅合金改質用マスターアロイおよびそれを用いる鋳造方法 |
PCT/JP2005/014691 WO2006016624A1 (ja) | 2004-08-10 | 2005-08-10 | 銅合金 |
PCT/JP2005/014687 WO2006016621A1 (ja) | 2004-08-10 | 2005-08-10 | 海水用構造物並びにこれを構成する線状若しくは棒状の銅合金材及びその製造方法 |
PCT/JP2005/014699 WO2006016631A1 (ja) | 2004-08-10 | 2005-08-10 | Sn含有銅合金及びその製造方法 |
PCT/JP2005/014697 WO2006016629A1 (ja) | 2004-08-10 | 2005-08-10 | 被削性、強度、耐摩耗性及び耐蝕性に優れた銅合金鋳物及びその鋳造方法 |
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PCT/JP2005/014698 WO2006016630A1 (ja) | 2004-08-10 | 2005-08-10 | 銅合金鋳物及びその鋳造方法 |
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PCT/JP2005/014699 WO2006016631A1 (ja) | 2004-08-10 | 2005-08-10 | Sn含有銅合金及びその製造方法 |
PCT/JP2005/014697 WO2006016629A1 (ja) | 2004-08-10 | 2005-08-10 | 被削性、強度、耐摩耗性及び耐蝕性に優れた銅合金鋳物及びその鋳造方法 |
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EP (9) | EP1777305B1 (ja) |
JP (8) | JP3964930B2 (ja) |
KR (2) | KR100863374B1 (ja) |
CN (7) | CN100487148C (ja) |
AT (7) | ATE482294T1 (ja) |
AU (3) | AU2005272376B2 (ja) |
BR (1) | BRPI0509025B1 (ja) |
CA (5) | CA2563094C (ja) |
CL (1) | CL2012003194A1 (ja) |
DE (3) | DE602005023737D1 (ja) |
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ES (2) | ES2378874T3 (ja) |
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Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010179356A (ja) * | 2009-02-09 | 2010-08-19 | Dowa Metaltech Kk | 銅合金の鋳造方法 |
Families Citing this family (132)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3964930B2 (ja) * | 2004-08-10 | 2007-08-22 | 三宝伸銅工業株式会社 | 結晶粒が微細化された銅基合金鋳物 |
ATE466965T1 (de) * | 2004-10-11 | 2010-05-15 | Diehl Metall Stiftung & Co Kg | Kupfer-zink-silizium-legierung, deren verwendung und deren herstellung |
JP5306591B2 (ja) * | 2005-12-07 | 2013-10-02 | 古河電気工業株式会社 | 配線用電線導体、配線用電線、及びそれらの製造方法 |
JP5116976B2 (ja) * | 2006-02-10 | 2013-01-09 | 三菱伸銅株式会社 | 半融合金鋳造用原料黄銅合金 |
JP2007211324A (ja) * | 2006-02-13 | 2007-08-23 | Sanbo Copper Alloy Co Ltd | 半融合金鋳造用原料りん青銅合金 |
WO2008041777A1 (fr) * | 2006-10-04 | 2008-04-10 | Sumitomo Light Metal Industries, Ltd. | Alliage de cuivre pour tuyaux sans soudure |
CN101573462B (zh) * | 2006-12-28 | 2012-10-10 | 株式会社开滋 | 耐应力腐蚀开裂性优异的无铅黄铜合金 |
WO2009047919A1 (ja) * | 2007-10-10 | 2009-04-16 | Toto Ltd. | 鋳造性に優れた無鉛快削性黄銅 |
EP2196549B1 (en) | 2007-10-10 | 2019-03-13 | Toto Ltd. | Lead-free, free-machining brass having excellent castability |
TWI452153B (zh) * | 2008-01-09 | 2014-09-11 | Toto Ltd | Excellent lead-free quick-brushed brass |
EP2252143A1 (en) * | 2008-03-19 | 2010-11-24 | NV Bekaert SA | Aquaculture net with polygonal bottom |
JP4725688B2 (ja) * | 2008-04-25 | 2011-07-13 | 三菱マテリアル株式会社 | 太陽電池用インターコネクタ用材料及び太陽電池用インターコネクタ |
US20090286083A1 (en) * | 2008-05-13 | 2009-11-19 | Hitachi Cable, Ltd. | Copper wire for a magnet wire, magnet wire using same, and method for fabricating copper wire for a magnet wire |
CL2008001565A1 (es) * | 2008-05-29 | 2008-08-29 | Ochoa Disselkoen Jose Alberto | Dispositivo flotante sumergible, para la limpieza biologica de redes utilizadas en el cultivo de peces que permite destruir los microorganismos del agua, conformado por medios soportantes, un medio de filtracion de particulas y un medio de desinfecci |
CN101440444B (zh) * | 2008-12-02 | 2010-05-12 | 路达(厦门)工业有限公司 | 无铅易切削高锌硅黄铜合金及其制造方法 |
CN101440445B (zh) | 2008-12-23 | 2010-07-07 | 路达(厦门)工业有限公司 | 无铅易切削铝黄铜合金及其制造方法 |
US10311991B2 (en) * | 2009-01-09 | 2019-06-04 | Mitsubishi Shindoh Co., Ltd. | High-strength and high-electrical conductivity copper alloy rolled sheet and method of manufacturing the same |
JP5356974B2 (ja) * | 2009-02-03 | 2013-12-04 | 日立電線株式会社 | 鋳造材、その製造方法及びこれを用いたマグネットワイヤ用銅線並びにマグネットワイヤ及びその製造方法 |
CA2753515A1 (en) * | 2009-03-03 | 2010-09-10 | Questek Innovations Llc | Lead-free, high-strength, high-lubricity copper alloys |
US20100226815A1 (en) * | 2009-03-09 | 2010-09-09 | Lazarus Norman M | Lead-Free Brass Alloy |
US20100303667A1 (en) * | 2009-03-09 | 2010-12-02 | Lazarus Norman M | Novel lead-free brass alloy |
JP4871380B2 (ja) * | 2009-03-18 | 2012-02-08 | 株式会社Lixil | 鋳造用銅基合金 |
DE102009002894A1 (de) * | 2009-05-07 | 2010-11-18 | Federal-Mogul Wiesbaden Gmbh | Gleitlagermaterial |
CN101919357A (zh) * | 2009-06-16 | 2010-12-22 | 铜联商务咨询(上海)有限公司 | 一种铜合金材料的应用 |
JP5513230B2 (ja) * | 2009-06-17 | 2014-06-04 | サンエツ金属株式会社 | 鋳造用銅基合金 |
EP2451604B1 (en) * | 2009-07-10 | 2017-08-30 | Luvata Franklin, Inc. | Copper alloy for heat exchanger tube |
US20110123643A1 (en) * | 2009-11-24 | 2011-05-26 | Biersteker Robert A | Copper alloy enclosures |
BR112012012098A2 (pt) * | 2009-11-24 | 2018-03-20 | Luvata Appleton Llc | receptáculos de liga de cobre |
CN101775509B (zh) * | 2010-01-28 | 2011-04-13 | 吉林大学 | 通过添加氧族合金元素提高铜抗腐蚀能力的方法 |
CN102206772A (zh) * | 2010-03-30 | 2011-10-05 | Lclip有限公司 | 黄铜合金 |
CA2807637C (en) * | 2010-08-24 | 2018-09-11 | Tomoyuki Ozasa | Method for preventing elution of bi from copper alloy |
CA2813495C (en) * | 2010-10-25 | 2015-09-01 | Mitsubishi Shindoh Co., Ltd. | Pressure resistant and corrosion resistant copper alloy, brazed structure, and method of manufacturing brazed structure |
KR101260912B1 (ko) * | 2011-02-01 | 2013-05-06 | 주식회사 풍산 | 해수용 동합금재 및 이의 제조 방법 |
CN102230105A (zh) * | 2011-04-08 | 2011-11-02 | 菏泽广源铜带股份有限公司 | 一种高强度锡黄铜 |
WO2012140977A1 (ja) * | 2011-04-13 | 2012-10-18 | サンエツ金属株式会社 | 鍛造性、耐応力腐食割れ性及び耐脱亜鉛腐食性に優れた銅基合金 |
US9050651B2 (en) * | 2011-06-14 | 2015-06-09 | Ingot Metal Company Limited | Method for producing lead-free copper—bismuth alloys and ingots useful for same |
DE102012002450A1 (de) | 2011-08-13 | 2013-02-14 | Wieland-Werke Ag | Verwendung einer Kupferlegierung |
US8465003B2 (en) | 2011-08-26 | 2013-06-18 | Brasscraft Manufacturing Company | Plumbing fixture made of bismuth brass alloy |
US8211250B1 (en) | 2011-08-26 | 2012-07-03 | Brasscraft Manufacturing Company | Method of processing a bismuth brass article |
JP5785836B2 (ja) * | 2011-09-20 | 2015-09-30 | 三菱マテリアル株式会社 | 銅合金及び鋳造品 |
JP5742621B2 (ja) * | 2011-09-20 | 2015-07-01 | 三菱マテリアル株式会社 | 銅合金及び鋳造品 |
KR101340487B1 (ko) * | 2011-09-30 | 2013-12-12 | 주식회사 풍산 | 쾌삭성 무연 구리합금 및 이의 제조방법 |
IN2014MN00785A (ja) * | 2011-11-04 | 2015-05-22 | Mitsubishi Shindo Kk | |
KR20130054022A (ko) * | 2011-11-16 | 2013-05-24 | 주식회사 대창 | 양식 어망용 동합금 |
CN103131887B (zh) * | 2011-11-21 | 2016-07-06 | 宁波三旺洁具有限公司 | 一种耐腐蚀硼铜合金 |
CN102578008B (zh) * | 2012-02-16 | 2014-01-01 | 中国水产科学研究院东海水产研究所 | 刚柔结合装配的锥体网箱箱体构建方法 |
WO2013145964A1 (ja) | 2012-03-30 | 2013-10-03 | 株式会社栗本鐵工所 | 水道部材用黄銅合金 |
CN102703740A (zh) * | 2012-06-20 | 2012-10-03 | 河南平高电气股份有限公司 | 一种Cu-Cr-Zr合金的制备方法 |
DE102012013817A1 (de) | 2012-07-12 | 2014-01-16 | Wieland-Werke Ag | Formteile aus korrosionsbeständigen Kupferlegierungen |
WO2014018564A1 (en) | 2012-07-23 | 2014-01-30 | Zieger Claus Dieter | Multiple proportion delivery systems and methods |
US8991787B2 (en) | 2012-10-02 | 2015-03-31 | Nibco Inc. | Lead-free high temperature/pressure piping components and methods of use |
US10006106B2 (en) * | 2012-10-31 | 2018-06-26 | Kitz Corporation | Brass alloy and processed part and wetted part |
CN103509967B (zh) * | 2013-01-22 | 2016-04-27 | 阮媛清 | 一种重力铸造专用dzr环保黄铜合金锭及其制作工艺 |
US10287653B2 (en) | 2013-03-15 | 2019-05-14 | Garrett Transportation I Inc. | Brass alloys for use in turbocharger bearing applications |
DE112014002690T5 (de) * | 2013-06-05 | 2016-02-25 | San-Etsu Metals Co., Ltd. | Kupferlegierung |
JP5406405B1 (ja) * | 2013-06-12 | 2014-02-05 | 株式会社栗本鐵工所 | 水道部材用銅合金 |
JP2015016501A (ja) * | 2013-07-12 | 2015-01-29 | 株式会社ブリヂストン | 鋳物の鋳造方法、鋳物及びタイヤ成形用金型 |
DE102013012288A1 (de) | 2013-07-24 | 2015-01-29 | Wieland-Werke Ag | Korngefeinte Kupfer-Gusslegierung |
KR101660683B1 (ko) | 2013-09-26 | 2016-09-27 | 미쓰비시 신도 가부시키가이샤 | 구리합금 |
CA2922455C (en) * | 2013-09-26 | 2017-03-14 | Mitsubishi Shindoh Co., Ltd. | Copper alloy and copper alloy sheet |
CN103526067B (zh) * | 2013-10-13 | 2015-07-08 | 蒋荣 | 一种高强度稀土掺杂铜合金的制备方法 |
KR102181051B1 (ko) * | 2013-10-21 | 2020-11-19 | 주식회사 대창 | 내구성이 향상된 죽방렴 구조물 |
CN103555991B (zh) * | 2013-11-20 | 2016-01-20 | 苏州天兼金属新材料有限公司 | 一种无铅环保铜基合金管及其制造方法 |
US20150203940A1 (en) * | 2014-01-22 | 2015-07-23 | Metal Industries Research&Development Centre | Brass alloy and method for manufacturing the same |
US10358696B1 (en) | 2014-02-07 | 2019-07-23 | Chase Brass And Copper Company, Llc | Wrought machinable brass alloy |
US9951400B1 (en) | 2014-02-07 | 2018-04-24 | Chase Brass And Copper Company, Llc | Wrought machinable brass alloy |
CN103849794B (zh) * | 2014-03-07 | 2016-05-25 | 镇江金鑫有色合金有限公司 | 一种环保自润滑耐磨铜合金 |
JP2015175008A (ja) * | 2014-03-13 | 2015-10-05 | 株式会社Lixil | 鉛レス黄銅材料および水道用器具 |
JP5656138B1 (ja) * | 2014-05-08 | 2015-01-21 | 株式会社原田伸銅所 | 抗菌性を有するリン青銅合金及びそれを用いた物品 |
CN103938021B (zh) * | 2014-05-09 | 2016-04-13 | 邵建洪 | 一种海洋围殖渔网专用编织铜合金线材及其制备方法 |
CN104032176B (zh) * | 2014-06-23 | 2015-03-11 | 江西鸥迪铜业有限公司 | 低铅黄铜合金 |
JP6354391B2 (ja) * | 2014-07-03 | 2018-07-11 | 三菱マテリアル株式会社 | Cu−Zn−Sn系合金の連続鋳造方法 |
RU2587110C9 (ru) * | 2014-09-22 | 2016-08-10 | Дмитрий Андреевич Михайлов | МЕДНЫЙ СПЛАВ, ЛЕГИРОВАННЫЙ ТЕЛЛУРОМ ТелО, ДЛЯ КОЛЛЕКТОРОВ ЭЛЕКТРИЧЕСКИХ МАШИН |
RU2587108C9 (ru) * | 2014-09-22 | 2016-08-10 | Дмитрий Андреевич Михайлов | МЕДНЫЙ СПЛАВ, ЛЕГИРОВАННЫЙ ТЕЛЛУРОМ ТелМ, ДЛЯ КОЛЛЕКТОРОВ ЭЛЕКТРИЧЕСКИХ МАШИН |
RU2587112C9 (ru) * | 2014-09-22 | 2016-08-10 | Дмитрий Андреевич Михайлов | МЕДНЫЙ СПЛАВ, ЛЕГИРОВАННЫЙ ТЕЛЛУРОМ ТелТ, ДЛЯ КОЛЛЕКТОРОВ ЭЛЕКТРИЧЕСКИХ МАШИН |
CN104451244B (zh) * | 2014-12-17 | 2016-08-17 | 湖南科技大学 | 一种高性能减摩耐磨锰铝青铜合金 |
CN104388749B (zh) * | 2014-12-17 | 2016-07-06 | 湖南科技大学 | 一种高强减摩耐磨锰铝青铜合金 |
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CN104630549A (zh) * | 2015-01-27 | 2015-05-20 | 苏州金仓合金新材料有限公司 | 一种连铸连轧的环保无铅新型合金材料棒及其制备方法 |
JP6477127B2 (ja) * | 2015-03-26 | 2019-03-06 | 三菱伸銅株式会社 | 銅合金棒および銅合金部材 |
US20180087130A1 (en) * | 2015-03-31 | 2018-03-29 | Kurimoto, Ltd. | Copper alloy for use in a member for water works |
CN104711450A (zh) * | 2015-04-03 | 2015-06-17 | 北京金鹏振兴铜业有限公司 | 高强度高延展性镁黄铜合金 |
CN104858364B (zh) * | 2015-04-27 | 2017-09-15 | 海安铸鑫金属制品有限公司 | 覆砂壳型锡青铜复合铸造阀板的制备方法 |
CN104895903A (zh) * | 2015-05-27 | 2015-09-09 | 含山县恒翔机械制造有限公司 | 一种跑车轮毂的防盗螺丝 |
CN104889687A (zh) * | 2015-05-27 | 2015-09-09 | 含山县恒翔机械制造有限公司 | 一种跑车轮毂防盗螺丝的制备方法 |
CN104911390A (zh) * | 2015-06-13 | 2015-09-16 | 陈新棠 | 一种抗菌耐腐蚀的热交换器铜管 |
DE102015116314A1 (de) * | 2015-09-25 | 2017-03-30 | Berkenhoff Gmbh | Verwendung eines aus einer Kupfer-Zink-Mangan-Legierung ausgebildeten metallischen Elements als elektrisches Heizelement |
SG11201803887SA (en) * | 2015-11-12 | 2018-06-28 | Honeywell Int Inc | Sputter target backing plate assemblies with cooling structures |
CN105506358A (zh) * | 2015-12-03 | 2016-04-20 | 中铝洛阳铜业有限公司 | 一种海洋养殖用环保耐蚀黄铜材料的制备工艺 |
CN105387965A (zh) * | 2015-12-24 | 2016-03-09 | 常熟市易安达电器有限公司 | 巷道用压力传感器 |
CN105671360B (zh) * | 2016-04-05 | 2017-07-18 | 上海理工大学 | 一种含有锆的耐海水腐蚀的铜合金及其制备方法 |
DE202016102696U1 (de) * | 2016-05-20 | 2017-08-29 | Otto Fuchs - Kommanditgesellschaft - | Sondermessinglegierung sowie Sondermessinglegierungsprodukt |
CN108495942B (zh) * | 2016-05-25 | 2019-06-07 | 三菱伸铜株式会社 | 黄铜合金热加工品及黄铜合金热加工品的制造方法 |
CN105908014B (zh) * | 2016-06-08 | 2017-08-25 | 上海理工大学 | 一种耐海水腐蚀的铜合金及其制备方法 |
CN106148755B (zh) * | 2016-08-09 | 2018-04-24 | 苏州天兼新材料科技有限公司 | 一种核动力汽轮机耐磨泵块用铸造材料及其制作方法 |
EP3498871B1 (en) | 2016-08-15 | 2022-05-11 | Mitsubishi Materials Corporation | Free-cutting copper alloy casting, use of the free-cutting copper alloy casting, and method for producing free-cutting copper alloy casting |
CN108085531A (zh) * | 2016-11-21 | 2018-05-29 | 宜兴市帝洲新能源科技有限公司 | 一种地暖设备的弯头材料 |
US10568304B2 (en) * | 2016-11-23 | 2020-02-25 | Graduate School At Shenzhen, Tsinghua University | Steel structure cage for marine crustacean aquaculture and integration thereof into vertical fish-crustacean aquaculture system |
RU2629402C1 (ru) * | 2016-12-06 | 2017-08-29 | Юлия Алексеевна Щепочкина | Спеченный сплав на основе меди |
CN107620769A (zh) * | 2016-12-30 | 2018-01-23 | 合肥美诚机械有限公司 | 一种车用新材料轴承 |
KR101796191B1 (ko) * | 2017-01-17 | 2017-11-09 | 주식회사 풍산 | 항균성, 내변색성 및 성형성이 우수한 동합금재 및 이의 제조방법 |
CN107217172A (zh) * | 2017-06-28 | 2017-09-29 | 安徽华飞机械铸锻有限公司 | 一种铜合金铸造工艺 |
US20190033020A1 (en) * | 2017-07-27 | 2019-01-31 | United Technologies Corporation | Thin-walled heat exchanger with improved thermal transfer features |
DE102017007138B3 (de) | 2017-07-27 | 2018-09-27 | Wieland-Werke Ag | Drahtmaterial, Netz und Zuchtkäfig für Aquakultur |
CN107354507B (zh) * | 2017-07-31 | 2019-07-19 | 江苏裕铭铜业有限公司 | 一种单晶导电铜杆上引连铸法生产工艺 |
US11155909B2 (en) | 2017-08-15 | 2021-10-26 | Mitsubishi Materials Corporation | High-strength free-cutting copper alloy and method for producing high-strength free-cutting copper alloy |
CN107381337A (zh) * | 2017-09-22 | 2017-11-24 | 张家港沙工科技服务有限公司 | 一种起重机用吊钩 |
CN108300891A (zh) * | 2017-12-13 | 2018-07-20 | 浙江灿根智能科技有限公司 | 一种多路连续铜及铜合金板材铸造方法 |
CN108384986B (zh) * | 2018-05-07 | 2020-02-21 | 宁波博威合金材料股份有限公司 | 一种铜合金材料及其应用 |
CN108950272B (zh) * | 2018-08-02 | 2020-02-18 | 济南大学 | 一种锌-铜合金的含锑变质剂及变质处理方法 |
CN112805109A (zh) * | 2018-10-10 | 2021-05-14 | 住友电工硬质合金株式会社 | 切削工具及其制造方法 |
KR101969010B1 (ko) | 2018-12-19 | 2019-04-15 | 주식회사 풍산 | 납과 비스무트가 첨가되지 않은 쾌삭성 무연 구리합금 |
FR3090433B1 (fr) * | 2018-12-21 | 2020-12-11 | Thermocompact Sa | fil électrode à laiton en phase Delta pour usinage par électroérosion, et procédé pour sa fabrication |
CN109865804B (zh) * | 2019-03-13 | 2021-08-03 | 北京首钢吉泰安新材料有限公司 | 一种圆珠笔头用易切削不锈钢的铋碲合金化方法 |
CN110000344B (zh) * | 2019-03-14 | 2021-02-02 | 昆明理工大学 | 一种抑制ZCuSn10P1合金锡元素偏析的连续制备半固态浆料的装置和方法 |
DE202019101597U1 (de) * | 2019-03-20 | 2019-04-23 | Otto Fuchs - Kommanditgesellschaft - | Cu-Zn-Legierung |
CN110117736B (zh) * | 2019-06-17 | 2021-11-19 | 上海理工大学 | 一种塑性好耐腐蚀的铋黄铜合金 |
ES2941313T3 (es) | 2019-06-25 | 2023-05-19 | Mitsubishi Materials Corp | Aleación de cobre de fácil corte y método para producir una aleación de cobre de fácil corte |
CN113906150B (zh) * | 2019-06-25 | 2023-03-28 | 三菱综合材料株式会社 | 易切削铜合金铸件及易切削铜合金铸件的制造方法 |
US11450516B2 (en) * | 2019-08-14 | 2022-09-20 | Honeywell International Inc. | Large-grain tin sputtering target |
CN111014623B (zh) * | 2019-12-09 | 2021-09-10 | 宁波兴业盛泰集团有限公司 | 一种铜镁合金大规格扁锭半连续铸造方法 |
CN110952019B (zh) * | 2019-12-24 | 2021-09-14 | 宁波博威合金材料股份有限公司 | 一种易切削锌白铜及其制备方法和应用 |
CN110951989B (zh) * | 2019-12-25 | 2020-11-06 | 鸣浩高新材料科技(江苏盐城)有限公司 | 一种高强韧铜锌铝形状记忆合金及其制备方法 |
JP7347321B2 (ja) * | 2020-05-08 | 2023-09-20 | 三菱マテリアル株式会社 | Cu-Zn-Si系合金の上方引上連続鋳造線材 |
CN111607714B (zh) * | 2020-07-03 | 2021-08-20 | 贵溪骏达特种铜材有限公司 | 一种铝青铜的熔炼工艺 |
CN112030033A (zh) * | 2020-09-14 | 2020-12-04 | 江西省科学院应用物理研究所 | 一种高强高导接触线用稀土铜合金 |
CN112404889B (zh) * | 2020-10-10 | 2022-03-01 | 厦门格欧博新材料科技有限公司 | 一种锌包铜工艺 |
DE102020127317A1 (de) | 2020-10-16 | 2022-04-21 | Diehl Metall Stiftung & Co. Kg | Bleifreie Kupferlegierung sowie Verwendung der bleifreien Kupferlegierung |
KR102265115B1 (ko) * | 2021-02-24 | 2021-06-15 | 주식회사 풍산 | 내식성 및 내변색성이 우수한 Cu-Zn계 합금 및 이의 제조 방법 |
CN113223629B (zh) * | 2021-05-13 | 2023-04-28 | 中南大学 | 一种Al-Mg-Si-Mn-Fe合金设计方法 |
CN115261665B (zh) * | 2022-06-22 | 2023-04-28 | 昆明冶金研究院有限公司北京分公司 | 铜铁磷系合金用变质剂、其制备方法及应用 |
CN118086716B (zh) * | 2024-04-22 | 2024-07-16 | 中铝科学技术研究院有限公司 | 海洋养殖用铜合金丝材、其制备方法及应用 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS52134811A (en) * | 1976-05-07 | 1977-11-11 | Osamu Hayashi | Golden copper alloy for dental use |
JPS5690944A (en) | 1979-12-24 | 1981-07-23 | Furukawa Kinzoku Kogyo Kk | Alloy for wire cut electrospark machining electrode |
JPH0499837A (ja) * | 1990-08-14 | 1992-03-31 | Nikko Kyodo Co Ltd | 通電材料 |
Family Cites Families (94)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
NL142818B (nl) * | 1947-11-04 | Matsushita Electronics Corp | Elektrode voor een elektrische ontladingsbuis, alsmede ontladingsbuis voorzien van deze elektrode. | |
US3676083A (en) * | 1969-01-21 | 1972-07-11 | Sylvania Electric Prod | Molybdenum base alloys |
US3912552A (en) * | 1972-05-17 | 1975-10-14 | Int Nickel Co | Oxidation resistant dispersion strengthened alloy |
JPS517617B2 (ja) | 1972-08-25 | 1976-03-09 | ||
JPS5078519A (ja) * | 1973-11-14 | 1975-06-26 | ||
US3928028A (en) * | 1974-04-05 | 1975-12-23 | Olin Corp | Grain refinement of copper alloys by phosphide inoculation |
US4055445A (en) * | 1974-09-20 | 1977-10-25 | Essex International, Inc. | Method for fabrication of brass alloy |
US4047978A (en) * | 1975-04-17 | 1977-09-13 | Olin Corporation | Processing copper base alloys |
JPS52107227A (en) * | 1976-02-27 | 1977-09-08 | Furukawa Electric Co Ltd:The | Heat resisting cu alloy with excellent electro- and heat conductivity |
US4110132A (en) * | 1976-09-29 | 1978-08-29 | Olin Corporation | Improved copper base alloys |
JPS5839900B2 (ja) | 1977-12-29 | 1983-09-02 | 三菱マテリアル株式会社 | 継目無し管製造用Cu合金 |
DE2758822C2 (de) * | 1977-12-30 | 1987-01-15 | Diehl GmbH & Co, 8500 Nürnberg | Verfahren zur Herstellung eines Kupfer-Zink-Werkstoffes |
JPS5570494A (en) | 1978-11-18 | 1980-05-27 | Futoshi Matsumura | Wire rod for copper welding excelling in electric conductivity, thermal conductivity and welding performance |
US4353415A (en) * | 1979-07-30 | 1982-10-12 | United Kingdom Atomic Energy Authority | Heat pipes and thermal siphons |
JPS5837143A (ja) * | 1981-08-27 | 1983-03-04 | Furukawa Electric Co Ltd:The | 高強度耐食銅合金 |
JPS5839900A (ja) | 1981-09-01 | 1983-03-08 | Nippon Kokan Kk <Nkk> | 海底パイプラインの緊急漏洩油量制限装置 |
JPS58197243A (ja) * | 1982-05-12 | 1983-11-16 | Sumitomo Electric Ind Ltd | ワイアカツト放電加工電極線用合金線 |
JPS5920811A (ja) * | 1982-07-28 | 1984-02-02 | Yokogawa Hokushin Electric Corp | 光式変位変換器 |
JPS5920811U (ja) * | 1982-07-30 | 1984-02-08 | 三宝伸銅工業株式会社 | 海水取水口用スクリ−ン |
US4515204A (en) * | 1982-12-15 | 1985-05-07 | Nippon Light Metal Company Limited | Continuous metal casting |
JPS59136439A (ja) * | 1983-01-26 | 1984-08-06 | Sanpo Shindo Kogyo Kk | 銅基合金 |
US4515132A (en) * | 1983-12-22 | 1985-05-07 | Ford Motor Company | Ionization probe interface circuit with high bias voltage source |
JPS61542A (ja) * | 1984-06-12 | 1986-01-06 | Nippon Mining Co Ltd | ラジエ−タ−プレ−ト用銅合金 |
JPS6148547A (ja) | 1984-08-14 | 1986-03-10 | Mitsui Mining & Smelting Co Ltd | 海洋用耐食銅合金 |
JPS61133357A (ja) * | 1984-12-03 | 1986-06-20 | Showa Alum Ind Kk | 加工性および耐焼付性にすぐれた軸受用Cu合金 |
US4826736A (en) * | 1985-06-14 | 1989-05-02 | Sumitomo Special Metals Co., Ltd. | Clad sheets |
GB2179673A (en) * | 1985-08-23 | 1987-03-11 | London Scandinavian Metall | Grain refining copper alloys |
GB2181156A (en) * | 1985-10-04 | 1987-04-15 | London Scandinavian Metall | Grain refining copper-bowed metals |
US4822560A (en) * | 1985-10-10 | 1989-04-18 | The Furukawa Electric Co., Ltd. | Copper alloy and method of manufacturing the same |
JPS62218533A (ja) * | 1986-03-18 | 1987-09-25 | Sumitomo Metal Mining Co Ltd | 高導電性銅合金 |
JP2516622B2 (ja) * | 1986-04-10 | 1996-07-24 | 古河電気工業株式会社 | 電子電気機器用銅合金とその製造法 |
JPS62274036A (ja) * | 1986-05-23 | 1987-11-28 | Nippon Mining Co Ltd | 耐磨耗性及び耐食性に優れた銅合金 |
JPS62297429A (ja) | 1986-06-17 | 1987-12-24 | Nippon Mining Co Ltd | 耐食性に優れた銅合金 |
US4874439A (en) * | 1987-02-24 | 1989-10-17 | Mitsubishi Kinzoku Kabushiki Kaisha | Synchronizer ring in speed variator made of wear-resistant copper alloy having high strength and toughness |
JPH0622332B2 (ja) * | 1987-10-14 | 1994-03-23 | 日本電気株式会社 | 入力回路 |
US4770718A (en) * | 1987-10-23 | 1988-09-13 | Iowa State University Research Foundation, Inc. | Method of preparing copper-dendritic composite alloys for mechanical reduction |
JPH01162737A (ja) * | 1987-12-18 | 1989-06-27 | Nippon Mining Co Ltd | 電子部品用銅合金 |
KR910003882B1 (ko) * | 1988-12-21 | 1991-06-15 | 풍산금속공업주식회사 | 전기 및 전자부품용 동합금과 그 제조방법 |
JPH02170954A (ja) * | 1988-12-22 | 1990-07-02 | Nippon Mining Co Ltd | 曲げ加工性の良好な銅合金の製造方法 |
JPH02179857A (ja) * | 1988-12-28 | 1990-07-12 | Furukawa Electric Co Ltd:The | ワイヤ放電加工用電極線 |
JP2809713B2 (ja) | 1989-06-22 | 1998-10-15 | 株式会社神戸製鋼所 | フレキシブルプリント用銅合金圧延箔 |
JPH03291344A (ja) | 1990-04-09 | 1991-12-20 | Furukawa Electric Co Ltd:The | 熱交換器ヘッダープレート用銅合金 |
JPH04224645A (ja) * | 1990-12-26 | 1992-08-13 | Nikko Kyodo Co Ltd | 電子部品用銅合金 |
US5288458A (en) * | 1991-03-01 | 1994-02-22 | Olin Corporation | Machinable copper alloys having reduced lead content |
CN1021890C (zh) * | 1991-05-12 | 1993-08-25 | 冯金陵 | 代银焊料及其制造方法 |
JPH0533087A (ja) * | 1991-07-31 | 1993-02-09 | Furukawa Electric Co Ltd:The | 小型導電性部材用銅合金 |
JP2758536B2 (ja) | 1992-08-11 | 1998-05-28 | 三菱伸銅株式会社 | 内面溝付溶接銅合金管 |
JPH06184669A (ja) | 1992-12-18 | 1994-07-05 | Mitsubishi Materials Corp | 給水給湯用耐孔食性銅合金配管 |
DE4395519T1 (de) * | 1992-10-27 | 1995-01-26 | Mitsubishi Materials Corp | Gegen Lochkorrosion beständige Kupferlegierungsrohre für die Zufuhr von Kalt- und Heißwasser |
US5486244A (en) * | 1992-11-04 | 1996-01-23 | Olin Corporation | Process for improving the bend formability of copper alloys |
US5370840A (en) * | 1992-11-04 | 1994-12-06 | Olin Corporation | Copper alloy having high strength and high electrical conductivity |
JPH06184674A (ja) * | 1992-12-23 | 1994-07-05 | Nikko Kinzoku Kk | 高導電性銅合金 |
JP3319482B2 (ja) * | 1993-12-30 | 2002-09-03 | 三宝伸銅工業株式会社 | 耐蝕性銅基合金材 |
JPH07282841A (ja) * | 1994-04-05 | 1995-10-27 | Mitsubishi Chem Corp | リチウムイオン二次電池 |
JPH08127830A (ja) | 1994-11-01 | 1996-05-21 | Fujikura Ltd | 電線導体用銅合金及び電線導体の製造方法 |
DE19548124C2 (de) * | 1995-12-21 | 2002-08-29 | Euroflamm Gmbh | Reibkörper und Verfahren zum Herstellen eines solchen |
JP3956322B2 (ja) * | 1996-05-30 | 2007-08-08 | 中越合金鋳工株式会社 | ワンウェイクラッチ用エンドベアリング及びその他の摺動部品 |
JPH1046270A (ja) * | 1996-08-01 | 1998-02-17 | Sumitomo Light Metal Ind Ltd | 耐中間温度脆性、耐焼鈍脆性および耐食性に優れた銅合金並びに伝熱管 |
JP3280250B2 (ja) | 1996-11-26 | 2002-04-30 | 三宝伸銅工業株式会社 | 魚類用養殖網及び魚類養殖用生簀 |
JP2898627B2 (ja) * | 1997-03-27 | 1999-06-02 | 日鉱金属株式会社 | 銅合金箔 |
US6132528A (en) * | 1997-04-18 | 2000-10-17 | Olin Corporation | Iron modified tin brass |
US5853505A (en) * | 1997-04-18 | 1998-12-29 | Olin Corporation | Iron modified tin brass |
JPH10337132A (ja) | 1997-06-05 | 1998-12-22 | Kuraray Co Ltd | 魚介類養殖網 |
JPH111736A (ja) * | 1997-06-09 | 1999-01-06 | Chuetsu Gokin Chuko Kk | 加熱装置用黄銅合金材料 |
JP3820467B2 (ja) | 1997-07-25 | 2006-09-13 | 独立行政法人土木研究所 | 土工事用流動化処理土の製造方法及び装置 |
DE19734780C1 (de) * | 1997-08-06 | 1998-12-10 | Mannesmann Ag | Verfahren zur Herstellung von geschweißten Rohren aus Cu und Cu-Legierungen |
JP4100583B2 (ja) * | 1997-08-25 | 2008-06-11 | 中越合金鋳工株式会社 | 鉄系材料と高力黄銅合金を接合する方法 |
JPH11140677A (ja) | 1997-11-14 | 1999-05-25 | Nakabohtec Corrosion Protecting Co Ltd | 銅又は銅合金製金網の防汚及び局部腐食防止の方法及び装置 |
JP2000087158A (ja) * | 1998-09-11 | 2000-03-28 | Furukawa Electric Co Ltd:The | 半導体リードフレーム用銅合金 |
US7056396B2 (en) * | 1998-10-09 | 2006-06-06 | Sambo Copper Alloy Co., Ltd. | Copper/zinc alloys having low levels of lead and good machinability |
US6413330B1 (en) | 1998-10-12 | 2002-07-02 | Sambo Copper Alloy Co., Ltd. | Lead-free free-cutting copper alloys |
JP3734372B2 (ja) * | 1998-10-12 | 2006-01-11 | 三宝伸銅工業株式会社 | 無鉛快削性銅合金 |
JP3414294B2 (ja) | 1999-01-07 | 2003-06-09 | 三菱マテリアル株式会社 | 0.2%耐力および疲労強度の優れた熱交換器用電縫溶接銅合金管 |
JP4129807B2 (ja) | 1999-10-01 | 2008-08-06 | Dowaホールディングス株式会社 | コネクタ用銅合金およびその製造法 |
JP4387027B2 (ja) * | 2000-03-07 | 2009-12-16 | 三菱伸銅株式会社 | 耐孔食性銅基合金管材 |
JP4294196B2 (ja) * | 2000-04-14 | 2009-07-08 | Dowaメタルテック株式会社 | コネクタ用銅合金およびその製造法 |
JP2002030364A (ja) * | 2000-07-19 | 2002-01-31 | Sumitomo Light Metal Ind Ltd | 高強度快削黄銅 |
KR100513947B1 (ko) * | 2002-03-29 | 2005-09-09 | 닛코 킨조쿠 가부시키가이샤 | 프레스성이 양호한 구리 합금 소재 및 그 제조방법 |
CN1327016C (zh) * | 2002-05-14 | 2007-07-18 | 同和矿业株式会社 | 具有改善的冲压冲制性能的铜基合金及其制备方法 |
JP4014542B2 (ja) | 2002-07-18 | 2007-11-28 | 本田技研工業株式会社 | 銅合金素材の製造方法 |
JP2004100041A (ja) | 2002-07-18 | 2004-04-02 | Honda Motor Co Ltd | 銅合金 |
JP3961529B2 (ja) * | 2002-09-09 | 2007-08-22 | 三宝伸銅工業株式会社 | 高強度銅合金 |
JP2004113003A (ja) | 2002-09-24 | 2004-04-15 | Baba Shoten:Kk | 生け簀装置及び生け簀養殖方法 |
JP4043342B2 (ja) * | 2002-10-25 | 2008-02-06 | 株式会社神戸製鋼所 | リン青銅 |
JP4371257B2 (ja) | 2002-12-02 | 2009-11-25 | 株式会社リコー | 画像形成装置 |
JP3693994B2 (ja) * | 2002-12-04 | 2005-09-14 | 三宝伸銅工業株式会社 | 鉛低減快削性銅合金 |
JP3999676B2 (ja) * | 2003-01-22 | 2007-10-31 | Dowaホールディングス株式会社 | 銅基合金およびその製造方法 |
US20060065327A1 (en) * | 2003-02-07 | 2006-03-30 | Advance Steel Technology | Fine-grained martensitic stainless steel and method thereof |
DE10308779B8 (de) * | 2003-02-28 | 2012-07-05 | Wieland-Werke Ag | Bleifreie Kupferlegierung und deren Verwendung |
US20050039827A1 (en) * | 2003-08-20 | 2005-02-24 | Yoshinori Yamagishi | Copper alloy having excellent corrosion cracking resistance and dezincing resistance, and method for producing same |
JP3731600B2 (ja) * | 2003-09-19 | 2006-01-05 | 住友金属工業株式会社 | 銅合金およびその製造方法 |
JP3964930B2 (ja) * | 2004-08-10 | 2007-08-22 | 三宝伸銅工業株式会社 | 結晶粒が微細化された銅基合金鋳物 |
US8066938B2 (en) * | 2004-09-03 | 2011-11-29 | Haynes International, Inc. | Ni-Cr-Co alloy for advanced gas turbine engines |
ATE498699T1 (de) * | 2005-09-30 | 2011-03-15 | Mitsubishi Shindo Kk | Aufgeschmolzene und erstarrte kupferlegierung die phosphor und zirkon enthält |
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Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS52134811A (en) * | 1976-05-07 | 1977-11-11 | Osamu Hayashi | Golden copper alloy for dental use |
JPS5690944A (en) | 1979-12-24 | 1981-07-23 | Furukawa Kinzoku Kogyo Kk | Alloy for wire cut electrospark machining electrode |
JPH0499837A (ja) * | 1990-08-14 | 1992-03-31 | Nikko Kyodo Co Ltd | 通電材料 |
Non-Patent Citations (2)
Title |
---|
E. O. HALL, PROC. PHYS. SOC., vol. 64, 1951, pages 747 |
N. J. PETCH, J. IRON STEEL INST., vol. 174, 1953, pages 25 |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010179356A (ja) * | 2009-02-09 | 2010-08-19 | Dowa Metaltech Kk | 銅合金の鋳造方法 |
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