JPS6242019B2 - - Google Patents

Description

[Detailed description of the invention]

The present invention provides vibration damping that is ideal for preventing pollution caused by vibration and noise from various transportation systems and large machinery, performance deterioration caused by vibration from various precision machines and electronic equipment, and the harmful effects of various vibrations and noises that exist in the living environment. This is related to the magnitude of the performance of Al-Ni based vibration absorbing alloys. Attenuation capacity generally used to compare attenuation capacity
Q ^-1 has a relationship with the vibrational energy ΔE lost during one cycle of vibration and the total vibrational energy E as shown in the following equation. Q ^-1 = 1/2π·ΔE/E In other words, the larger the value of Q ^-1 , the smaller the amplitude becomes in a shorter time and the greater the damping effect. Conventionally known vibration-absorbing alloys include Fe-based alloys such as dientalloy, Mn-Cu alloys, and Al-Cu alloys.
- Includes Ni-based alloys and Ni-Ti-based alloys. Fe-based vibration-absorbing alloys such as Dientalloy and Mn-Cu-based alloys have a large damping capacity, but their specific gravity is around 8 g/ ^cm3 , making them unsuitable when reducing the weight of equipment. Ni-based alloys and Ni-Ti-based alloys have the disadvantage of poor cold workability and are completely impossible to cold work. In order to obtain a vibration-absorbing alloy that is lighter than conventional vibration-absorbing alloys, the present invention uses aluminum as its base, which has a very small specific gravity of 2.7 g/ ^cm3 , and has a weight ratio of 0.1 to 20.
% nickel, 50% or less of one or both of lead and antimony, 40% or less of one or both of germanium and cerium, 20% or less of tantalum, and one or more of niobium, cobalt, iron, and zirconium. A multi-component alloy containing 0.1 to 50% of one or more of two or more, 15% or less of titanium or calcium, 10% or less of one or both of titanium and calcium, and 3% or less of boron at a temperature below the melting point of 250℃ After homogeneous solution heat treatment at a temperature above, cold working is performed at a rate of 5% or more to increase dislocations, and if necessary,
The object of the present invention is to provide a vibration-absorbing alloy which is heat-treated at a temperature of 0.degree. Next, a method for manufacturing the alloy of the present invention will be explained. First, an alloy with the above composition range is melted in an ordinary melting furnace in air, an inert gas, or a vacuum, and then sufficiently stirred to form a uniform molten metal.Then, the alloy is poured into a sand mold or metal mold, and an ingot is poured into an ingot. Build. Next, this ingot is subjected to the following heat treatment. (A) For homogeneous solution treatment, heat at a temperature as high as possible, for example, at a temperature of 250°C or higher below the melting point of the alloy, for 5 minutes to 100 hours (preferably 30 minutes or more), and then rapidly cool or heat at 1°C per second.
Cool slowly at the following speed. (B) Subsequently, cold working is performed at room temperature by forging, rolling, extrusion, swaging, or drawing at a cold working rate of 5% or more in order to obtain the large damping capacity that is the objective of the present invention. (C) A product that has been processed with a cold working rate of 5% or more in (B) is heated at a temperature of 250°C or less for 1 minute or more (preferably 30 minutes or more and 500 hours or less) and then rapidly cooled or 1°C per second. Cool slowly at the following speed. In addition, when dissolving, a flux of MgCl ₂ , borax, CaF ₂ , KCl, etc. in a total amount of 5% or less is added as a blocking agent, and a total amount of 0.5% or less of Mg, Be, etc. is added as a deoxidizing agent.
% or less may be added. The reason why homogeneous solution treatment is performed in step (A) is because the inhomogeneity of components may occur in the ingot due to the temperature difference between each part of the ingot and the difference in specific gravity between the solid and liquid phases during the solidification of the molten metal. This is to make the ingredients homogeneous. If the heating temperature is high, the heating time can be shortened, and if the heating temperature is low, the heating time must be lengthened. On the other hand, if the weight of the molded object is large,
Although it is necessary to raise the heating temperature and lengthen the heating time, if the weight of the molded product is small, it may be heated at a relatively low temperature for a short time. The reason for this is that unless the solution treatment is sufficiently performed, the performance of the product, such as the damping capacity, cannot be made uniform. The cold working step (B) following the solution treatment step (A) is an essential step in order to increase the dislocation density due to processing strain and obtain a large damping capacity due to the hysteresis phenomenon. , is also necessary to increase the tensile strength of the molded article. In addition, in order to increase the damping capacity, cold working of 5% or more is enough to achieve the purpose, but if the cold working rate is 70% to 95%,
% or the composition of the alloy contains many subcomponents, it may be difficult to form by bending, deep drawing, punching, etc. For this reason, if the cold-worked product in step (B) is heated to a temperature of 250°C or less in step (C), the damping capacity and strength will not deteriorate significantly and forming processes such as bending, deep drawing, and punching will be possible at room temperature. It becomes even easier. In this case, set the heating temperature to 250
If the temperature is higher than 0.degree. C., the elongation will rapidly increase to 24% or more, but the damping capacity Q ^-1 will drop to 4 x 10 ^-3 or less, which is not preferable. Next, examples of the present invention will be described. Example 1 Total amount of metal with the composition shown in Tables 1 and 2: 100g
was melted in an alumina crucible in a high-frequency induction electric furnace while passing argon gas through the surface, and cast into an iron mold to obtain an ingot with a diameter of 10 mm. Next, this was heated at 500° C. for 5 hours and slowly cooled, then cold swaged and drawn into a 1.1 mm wire, and a 150 mm long wire was cut from this to serve as a sample. Attenuation ability
Q ^-1 was measured using the inverted torsional pendulum method with a frequency of approximately 1.
Hz, maximum strain amplitude γ _n =10×10 ^-6 . Tables 1 and 2 show the values of Q ^-1 when a 95% cold working rate is applied to a multi-component alloy in which one or more of various other elements are added to an Al--Ni alloy. .

【table】

[Table] As is clear from these tables, the cold working rate is 95%.
Aluminum treated with aluminum has a damping capacity Q ^-1 of 4 × 10 ^-3 and is not suitable as a vibration absorbing material for the purpose of the present invention. 0.1% in total amount
If the above amount is added, Q ^-1 = 6×
It can be seen that a large value of 10 ^-3 or more can be obtained. In short, the value of the damping capacity Q ^-1 of the alloy of the present invention is several tens of times larger than the value of the damping capacity Q ^-1 =1×10 ^-3 of general metals. Example 2 A total of 100g of Al-1.0%Ni-1.0%Co ternary alloy was melted in an alumina crucible using a high-frequency induction electric furnace while passing Ar gas to the surface, and cast into an iron mold to reduce the diameter.
A 10 mm ingot was obtained. Next, this was heated at 500℃ for 5 hours and slowly cooled, and then cold swaged and drawn into a 1.1 mm wire at cold working rates of 71% and 95%, and then cold worked at a rate of 71%. and 95% was applied. This cold-worked material was annealed at 150°C, 200°C, and 250°C for 60 minutes, 180 minutes, 30 minutes, and 10 minutes, respectively, and then slowly cooled. A wire of 150 mm in length was cut from the sample. And so. The damping capacity Q ^-1 was measured using the inverted torsional pendulum method at a frequency of approximately 1 Hz and a maximum strain amplitude γ _n = 10.
It was carried out at ×10 ^-6 . The results are shown in Table 3.

[Table] As described above, in the present invention, the damping capacity increases as the cold working rate increases from 5% to 95%, but the elongation decreases and the workability decreases due to brittleness.
It is necessary to anneal at a temperature below ℃. When annealing at a temperature below 250°C, the elongation increases by at least three times, making it easier to process, and the damping capacity decreases slightly, but this is not a problem. This is because the number of dislocations increased by processing is annealed by annealing, resulting in fewer dislocations. Incidentally, when the annealing temperature is raised to 250° C. or higher, the elongation increases rapidly to 25% or higher, but the damping capacity Q ⁻¹ becomes 4×10 ⁻³ or lower, and the object of the present invention cannot be obtained. From the results of the above tests, it was found that when an ingot of the alloy of the present invention is heat treated and subjected to cold working at a cold working rate of 5% or more, it elongates when heated at a temperature of 250°C or less for 1 minute or more and 500 hours or less. El increases, making it easier to form by bending, deep drawing, punching, etc. The relationship between the cold working rate, heating temperature, heating time, elongation El, and damping capacity Q ^-1 for the Al-1.0% Ni-1.0% Co alloy in Example 2 is as shown in Table 3. The lower the heating temperature, the longer the heating time needs to be.
Furthermore, the upper limit of the heating temperature was set at 250℃ because if the heating temperature is higher than 250℃, the elongation El will be very large at about 25%, but the damping capacity Q ^-1 will suddenly decrease and become less than 4 × 10 ^-3 . This is because it is insufficient for the purpose of the invention. Furthermore, the specific gravity ρ of the alloy of the present invention is 7 to 7 of that of general metals.
The tensile strength σ t is considerably smaller than 9 g/cm ³ , and the tensile strength σ _t is considerably higher than 10 Kg/mm ² for cold-worked aluminum. For example, sample No. 7 of the example has σ _t =23
Kg/mm ² , ρ = 2.9g/cm ³ , σ _t = 27Kg/ for sample No. 8
mm ² , ρ = 2.8g/cm ³ , sample No. 20 has σ _t = 25Kg/mm ² ,
ρ=2.9g/cm ³ is shown. Finally, the reason for limiting the composition of the alloy of the present invention will be described. First, in multi-component alloys, Ni and other additive elements Pb, Sb, Ge, Ce, Ta, Nb, Fe, Zr,
Ti, Ca, and B all not only contribute to improving the damping capacity Q ^-1 but also strengthen the alloy except for Pb.
Ni is 0.1 to 20% by weight, either Pb or Sb is 50% or less, Ge or Ce is 40% or less, and Ta is
20% or less, 15% or less of any of Nb, Co, Fe, or Zr, 10% or less of any of Ti or Ca, and 3% or less of B. The total amount of one or more of the following is 0.1 to 50%. The reason for this limitation is that if the lower limit of the composition is not met, sufficient attenuation ability for the purpose of the present invention cannot be obtained, and if the upper limit of the composition is exceeded, the attenuation ability deteriorates altogether, and sufficient strength cannot be obtained with Pb. gone,
This is also because cold working is impossible with other elements. Table 4 shows the general tendency that the component range of each component element in the vibration absorbing alloy of the present invention has on damping ability, mechanical strength, workability, etc.

[Table] For homogeneous solution treatment, heating for a long time of 100 hours or less at a temperature of 250°C or higher and below the melting point is sufficient to achieve the required damping capacity, strength, and workability. absolutely necessary to obtain. Note that performing cold working at a cold working rate of 5% or more is an absolutely necessary condition for increasing the damping capacity by increasing the working strain and dislocation density. The alloy molded body is heated to 250℃ below the melting point of aluminum.
When the homogeneous solid solution treatment is performed by heating at the above high temperature for a long time, the state of dispersion of Ni and subcomponent element particles in the aluminum matrix becomes homogeneous. When this is subjected to cold working at a cold working rate of 5% or more, Ni and subcomponent element particles are finely dispersed, and the dislocation density increases. When this dislocation density number increases, when vibration is applied from the outside,
Attenuation of vibration occurs because the applied external force (vibration, impact, torsion, compression, tension, etc.) disappears as thermal energy and other energy. Therefore, in order to increase the attenuation capacity, it is necessary to
Long-term heating at a high temperature above and cold working of 5% or more are enough to achieve the purpose, but if the cold working rate is increased to 70% to 95% or a large amount of subcomponents is added. Depending on the composition of the alloy, it may be difficult to form it by bending, deep drawing, punching, etc. For this reason, when reheated for a long time at a low temperature of 250°C or lower, the damping capacity and strength do not deteriorate significantly, and forming processes such as bending, deep drawing, and punching become extremely easy. In this case, reheating at 250° C. or higher is not preferable because the attenuation ability decreases. As mentioned above, the alloy of the present invention is characterized by having a large damping capacity, being lightweight, having good cold workability, high strength, and being non-ferromagnetic. Therefore, the alloy of the present invention can be applied to various transportation systems, internal combustion engines for automobiles, large machinery, moving parts of electronic devices, parts operated by magnetic fields, various household goods, and structural materials for buildings, etc., and can be used to prevent vibration and noise, Very suitable for weight reduction.

Claims (1)

[Scope of Claims] 1 In terms of weight ratio, the main components are 0.1 to 20% nickel, the balance is aluminum, and the subcomponents are 50% or less of one or both of lead and antimony, and one or more of germanium and cerium. 40% or less of two types, 20% or less of tantalum, 15% or less of any one or more of iron, niobium, cobalt, and zirconium, 10% or less of any one or both of titanium and calcium,
Total amount of one or more boron 3% or less
0.1 to 50%, and has an increased damping capacity Q ^-1 of 6 x 10 ^-3 or more. 2 By weight, the main component is nickel 0.1-20%, the balance is aluminum, and the subcomponents are lead, antimony, one or both of which are less than 50%, germanium and cerium, which are less than 40%, 20% or less of tantalum, 15% or less of any one or more of iron, niobium, cobalt, and zirconium, 10% or less of any one or both of titanium, calcium,
Total amount of any one or two or more types of boron 3% or less
(A) heating at a temperature of 250°C or higher below the melting point of the alloy for 5 minutes or more and 100 hours or less, followed by rapid cooling or slow cooling at a rate of 1°C per second or less; (B) A method for producing an Al--Ni based vibration absorbing alloy, characterized in that the damping capacity Q ^-1 is made to be 6 x 10 ^-3 or more by performing cold working at a rate of 5% or more. 3 In terms of weight ratio, an alloy consisting of 0.1 to 20% nickel and the balance aluminum, with lead as a subcomponent,
50% or less of one or two types of antimony, 40% or less of one or both of germanium and cerium
% or less, tantalum 20% or less, niobium, cobalt,
One or more of iron and zirconium15
(A) 250°C below the melting point of the alloy. After heating at a temperature above 5 minutes to 100 hours, followed by rapid cooling or slow cooling at a rate of 1°C per second or less, (B) cold working with a cold working rate of 5% or more (C) cold working of (B) Attenuation ability can be improved by heat-treating a material that has been processed at a processing rate of 5% or more at a temperature of 250°C or less for 1 minute or more and 500 hours or less, followed by rapid cooling or slow cooling at a rate of 1°C or less per second. Q ^-1 to 6
A method for producing an Al--Ni-based vibration absorbing alloy, characterized in that the vibration absorption alloy is at least ×10 ^-3 .