JPS6238418B2 - - Google Patents

Description

[Detailed description of the invention]

The present invention provides vibration damping that is optimal for preventing pollution caused by vibrations and noises of various transportation systems and large machines, performance deterioration caused by vibrations of various precision machines and electronic devices, and harmful effects of various vibrations and noises that exist in the living environment. This study concerns Al-Sn-based vibration-absorbing alloys with high performance. 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 the damping ability 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 high damping ability, but their specific gravity is around 8 g/ ^cm3 , making them unsuitable when reducing the weight of equipment.Al-Cu-Ni The disadvantage of these alloys is that they have 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 is based on Al, which has a very low specific gravity of 2.7 g/cm ³ , and adds tin in a weight ratio of 0.1 to 90%.
Up to 50% lead, antimony, up to 40% germanium, cerium, up to 20% silicon, nickel,
Cobalt, up to 15% iron, niobium, zirconium, tantalum, up to 10% titanium, calcium,
Total amount of one or more types of boron up to 3%
A multi-component alloy consisting of 0.1 to 50% aluminum and the balance is cold-worked to a rate of 5% or more to increase the dislocation, and if necessary, annealed at 150℃ or less to create a large damping capacity and high strength due to the hysteresis phenomenon. The object of the present invention is to provide a vibration-absorbing alloy that has the following properties. 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) Homogeneous solution treatment at as high a temperature as possible, for example at a temperature of 150°C or higher below the melting point of the alloy.
After heating for at least 5 minutes and as long as possible (preferably at least 5 minutes and up to 100 hours), it is rapidly cooled or slowly cooled at a rate of 1° C. or less per second. (B) Next, 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) After processing with a cold working rate of 5% or more in (B)
At a temperature of 150℃ or less for 1 minute or more (preferably 1 minute)
(for more than 500 hours) and then rapidly cooled, or slowly cooled at a rate of 1°C per second or less. When dissolving, a flux of MgCl ₂ , borax, CaF ₂ , KCl, etc. in a total amount of 5% or less may be added as a blocking agent, and magnesium, beryllium, etc. in a total amount of 0.5% or less may be added as a deoxidizing agent. In the homogeneous solution treatment step (A), if the heating temperature is high, the heating time must 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, it is necessary to raise the heating temperature and lengthen the heating time, but if the weight of the molded object is small, it may be heated at a relatively low temperature for a short time. The reason for this is that unless homogeneous solution treatment is sufficiently performed, product performance such as damping capacity cannot be made uniform. Cold working in step (B) following the homogeneous solution treatment step (A) increases the dislocation density by processing,
This is an essential step in order to obtain a great ability to reduce pain through the hysteresis phenomenon, and is also necessary to increase the tensile strength of the molded article. In order to increase the damping capacity, cold working of 5% or more is enough to achieve the purpose, but the strength of the working condition,
That is, when the cold working rate is as high as 70 to 95%, or depending on the composition of the alloy, the elongation is extremely small, making it difficult to form by bending, deep drawing, punching, etc. Therefore, after cold working in step (B), step (C)
When heated to a temperature of 150°C or less, the elongation increases, making it easier to form by bending, deep drawing, punching, etc. at room temperature. The reason for setting the temperature below 150℃ in step (C) is that when heated above 150℃, the elongation suddenly increases and workability improves, but the damping capacity Q ^-1 decreases to below 4 x 10 ^-3 and the desired purpose cannot be achieved. This is so that you will not be affected. 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 using a high-frequency induction electric furnace while passing Ar 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 200℃ for 10 hours, slowly cooled, and then cold swaged and drawn into a 1.1mm wire.
A mm line was cut and used as a sample. The damping capacity Q ^-1 was measured by the inverted torsion pendulum method at a frequency of approximately 1 Hz and a maximum strain amplitude γm = 10 x 10 ^-6 . Adding one or two of various other elements to Al-Sn alloy
Cold working rate of 95% for multi-component alloys with more than one species added
The values of the attenuation capacity Q ^-1 when applying are as shown in Tables 1 and 2.

【table】

[Table] As is clear from these tables, the cold working rate is 95%.
Cold-worked aluminum has a damping capacity Q ^-1 of 4 x 10 ^-3 , making it unsuitable as a vibration absorbing material for the purpose of the present invention. When one or more of these are added in a total amount of 0.1% or more, Q ^-1 , which is the objective of the present invention,
It can be seen that a large value of =6×10 ^-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 Q ^-1 =1×10 ^-3 of ordinary metals. Example 2 A total of 100g of Al-10.0%Sn-5.0%Sb 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°C for 5 hours and slowly cooled, and then cold swaged and drawn into a 1.1 mm wire at a cold working rate of 71%, and then subjected to a cold working rate of 71%. . This cold-worked material was annealed at 150°C for 30 minutes and 180 minutes, respectively, and then slowly cooled. A wire of 150 mm in length was cut from it and used as a sample. 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 γm =
I went with 10×10 ^-6 . The results are shown in Table 3.

[Table] As described above, in the present invention, the damping increases as the cold working rate increases from 5% to 95%, but elongation decreases, making it brittle and reducing workability.
It is necessary to anneal at a temperature below ℃. When annealing at a temperature of 150°C or lower, the elongation increases by at least three times, making it easier to process, but the damping ability 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. Note that when the annealing temperature is increased to 250℃, the elongation increases rapidly to more than 35%, but the damping capacity decreases.
Q ^-1 becomes less than 4×10 ^-3 and the object of the present invention cannot be obtained. From the results of the above tests, the ingot of the alloy of the present invention (A)
After cold working with a cold working rate of 5% or more, heating at a temperature of 150°C or less for 1 minute or more and 500 hours or less will increase the elongation El and cause bending.
Forming such as deep drawing and punching becomes easier. The relationship between cold working, heating temperature, heating time, elongation El, and damping capacity Q ^-1 for the Al-10.0%Sn-5.0%Sb alloy in Example 2 is as shown in Table 3. The lower the temperature, the longer the heating time needs to be. Furthermore, the upper limit of heating temperature was set to 150℃.
If the temperature is higher than 0.degree. C., the elongation El becomes very large by 25% or more, but the damping capacity Q ^-1 suddenly decreases to 4.times.10.sup. ^-3 or less, which is insufficient for the purpose of the present 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 σt is considerably smaller than 9 g/cm ³ , and the tensile strength σt is considerably larger than 10 Kg/mm ² of cold-worked aluminum. For example, in sample No. 3 of the example, σt=
19Kg/mm ² , ρ=3.7g/cm ³ , σt=18Kg/ for No.7
mm ² , ρ=3.61g/cm ³ . Finally, the reason for limiting the composition of the alloy of the present invention will be described. First, in multi-component alloys, tin and other additive elements such as lead, antimony, germanium, cerium, silicon, nickel, cobalt, iron, niobium,
Zirconium, tantalum, titanium, calcium,
All boron not only contributes to improving the damping capacity Q ^-1 but also strengthens the alloy except for lead. 0.1 to 90% by weight of tin, 50% or less of lead and antimony, 40% or less of germanium, cerium, 20% or less of silicon, nickel, cobalt, 15% or less of iron, niobium, zirconium, tantalum, titanium, The reason for limiting the total amount of one or more of calcium to 10% or less and boron to 3% or more to 0.1 to 50% is that when the lower limit of the composition is not met, sufficient attenuation ability for the purpose of the present invention is not achieved. If the upper limit of the composition is exceeded, sufficient strength cannot be obtained with lead, and cold working is impossible with other elements. Table 4 shows the general trends of the damping ability, mechanical strength, and workability of each component element in the vibration absorbing alloy of the present invention.

[Table] Sufficient homogeneous solution treatment by heating at a temperature of 150℃ or higher and below the melting point of the alloy for a long period of time for homogeneous solution treatment is absolutely necessary to obtain the required damping ability, strength, and workability. It is. When tin is added to aluminum and dissolved, the aluminum, tin, and subcomponent elements do not form a solid solution, but become dispersed as fine particles in an aluminum matrix. When a compact of such an alloy is subjected to homogeneous solution treatment by heating it at a high temperature of 150°C or higher below the melting point of the alloy for a long period of time, the state of dispersion of tin 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, tin and subcomponent element particles are finely dispersed, and the dislocation density becomes large. When this dislocation density increases, when vibration is applied from the outside, the applied external force (vibration, impact, torsion, compression, tension, etc.) becomes thermal energy and disappears, causing vibration damping. It is. Therefore, in order to increase the attenuation capacity, it is necessary to
Long-term heating at higher temperatures and cold working of 5% or more are enough to achieve the objective, but if the cold working rate is increased to 70-95% or alloys with a large number of subcomponents are added. Depending on the composition of the material, 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 150°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, it is not preferable to set the reheating treatment temperature to 150° C. or higher because the damping ability will decrease. 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 synthesis of the present invention can be applied to materials for various transportation systems, large machines, moving parts of electronic devices, parts operated by magnetic fields, various household goods, and buildings, and can be used to prevent vibration and noise and reduce weight. very suitable.

Claims (1)

[Scope of Claims] 1. 0.1 to 90% tin, 50% or less of one or both of lead and antimony, 40% or less of one or both of germanium and cerium, silicon , nickel, cobalt, any one or more than 20%, iron, niobium, zirconium, tantalum, any one or more than 15%, titanium, calcium, any one or both 10% below,
Total amount of one or more of boron 3% or less
An Al--Sn based vibration absorbing alloy consisting of 0.1 to 50% aluminum with the remainder being aluminum and characterized by having an increased dislocation density damping capacity Q ^-1 of 6 x 10 ^-3 or more. 2 By weight, 0.1 to 90% tin, 50% or less of one or both of lead and antimony, 40% or less of one or both of germanium and cerium, silicon, nickel, and cobalt. 1 or more than 20% of iron, niobium, zirconium, tantalum, 15% or less of iron, niobium, zirconium, tantalum, 10% or less of titanium or calcium,
Total amount of one or more of boron 3% or less
For alloys consisting of 0.1% to 50% aluminum and the balance: (A) After heating at a temperature of 150°C or higher below the melting point of the alloy for 5 minutes or more and 100 hours or less, and then rapidly cooling or slowly cooling at a rate of 1°C per second or less ( B) A method for producing an Al--Sn-based vibration absorbing alloy, characterized in that the damping capacity Q ^-1 is made 6 x 10 ^-3 or more by performing cold working at a rate of 5% or more. 3 By weight, the main components are 0.1 to 90% tin and the balance aluminum, and the secondary components are 50% or less of one or both of lead and antimony, and 40% of one or both of germanium and cerium. Below, silicon,
One or more of nickel and cobalt20
% or less, any one or more of iron, niobium, zirconium, tantalum, 15% or less, titanium, calcium, any one or both of 10% or less, boron 3%
For alloys containing the following: (A) After heating at a temperature below the melting point of the alloy and above 150°C for 5 minutes to 100 hours, and then rapidly cooling or slowly cooling at a rate of 1°C per second or below (B ) Processed with a cold working rate of 5% or more (C), (B) processed with a cold working rate of 5% or more at 150℃
The damping capacity Q ^-1 is increased by 6x by heating at the following temperature for 1 minute to 500 hours and rapidly cooling, or slowly cooling at a rate of 1°C per second or less.
A method for producing an Al--Sn-based vibration-absorbing alloy, characterized in that it has a vibration absorbing alloy of 10 ^-3 or more.