JPS5930783B2 - vibration absorbing alloy - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a vibration absorbing alloy having a large vibration damping ability.

In recent years, elements made of vibration-absorbing alloys having high damping ability have been used in machinery such as aircraft, ships, and vehicles that generate noise and vibration that cause pollution problems, as well as precision instruments that generate vibration.

As vibration-absorbing alloys, Mn--Cu, Ni--Ti, and Zn--Al alloys having a damping capacity Q-1 of 0.005 or more are commonly used.

Q-1 can be expressed by the following formula (δ in the formula represents a logarithmic attenuation rate).

In other words, the larger the value of Q-', the greater the amount of energy reduction, the smaller the amplitude of vibration in a shorter time, and the greater the damping effect.

However, among vibration-absorbing alloys, Mn-Cu alloys and Ni-T
Although i-based alloys have excellent damping properties near room temperature,
It decreases dramatically as the temperature rises, and at around 100°C, it hardly loses its properties, becoming the same as those of general metal materials.

Therefore, these alloys cannot be expected to be effective as vibration-absorbing alloy elements at high temperatures exceeding 100°C.

Further, the Zn-Al alloy has very low damping ability near room temperature, but increases as the temperature rises, and exhibits relatively high damping ability in a high temperature range of 100° C. or higher.

Both alloys also have the disadvantage of poor cold workability and poor corrosion resistance.

The present invention improves the performance of conventional vibration-absorbing alloys, and provides a vibration-absorbing alloy element that has excellent damping ability in a wide temperature range from low to high temperatures, has excellent cold workability, and has good corrosion resistance. It is in.

The alloy of the present invention is a binary alloy consisting of Cu0.01 to 5% and the balance Fe or C as a subcomponent in weight ratio.
r40% or less, Al, Nb2Mo.

W t T 1 , V , Ta 10% or less, Si
5% or less, and one or more of Co and Y in a total amount of 0.01 to 400; b is added.

Next, a method for producing the alloy of the present invention will be explained.

First, in the above composition range, appropriate amounts of iron and copper, or these as the main components, are further added as subcomponents, and after melting in an ordinary melting furnace in air, inert gas, or vacuum, manganese, silicon, titanium, aluminum, etc. Add a small amount (1% or less) such as calcium to remove harmful impurities, stir thoroughly to create a compositionally uniform molten alloy, and then forge, roll, or swage at room temperature or a temperature below 1300°C. to form a material with a shape that suits the purpose.

In the present invention, this molded body is subjected to the following heat treatment.

The material is heated for 1 minute to 100 hours at a high temperature of 800° C. or higher below the melting point to undergo homogeneous solution treatment and then quenched, or annealed by slow cooling at a rate of 1° C. per second or less.

(B) Cold working is performed after the above quenching or annealing.

(C) After quenching in CA) or cold working in (B), heat at 100°C to below the quenching temperature (800°C) for 1 minute to 100 hours, and then slowly cool at a rate of 1°C or less per second.

The vibration absorption mechanism of the vibration absorption alloy of the present invention will be described as follows.

Generally, when vibrations are applied to an object, the vibrations attenuate until they become zero.

In this phenomenon, vibrational energy is converted into thermal energy etc. in the object, and the applied energy becomes zero and disappears.

This is called internal friction in the sense of absorption of energy within the object.

The higher the internal friction value of the high damping capacity alloy, the better the characteristics.

Conventionally known vibration absorbing alloys are classified as follows.

The vibration-absorbing alloy of the present invention is a Cu-Fe-based vibration-absorbing alloy, and has at least the above-mentioned ferromagnetic type vibration absorption mechanism, but it has complex causes such as dislocation-type and composite-type dislocations or internal friction within the crystal. It is thought that the structure has a mechanism that absorbs vibrations.

The vibration damping mechanism in an alloy involves movement of magnetic domain walls due to energy such as impact or vibration received from the outside world.

The direction of spontaneous magnetization changes due to the movement of the magnetic domain walls, and energy is dissipated.

High attenuation ability can be obtained from materials whose magnetic domain walls are easily movable.

This tendency for magnetic domain walls to move easily is not a property unique to alloys.

Therefore, even if the composition is the same, some have no vibration absorbing ability and others do not.

As mentioned above, the vibration-absorbing properties of vibration-absorbing alloys depend on ■composition, ■heat treatment,
■It has something to do with machining, and unless the composition is at least compatible, vibration absorption properties will not be obtained no matter how you heat treat it.

For example, steel with directional properties will never be able to absorb vibrations.

This is because the magnetic domains are aligned in a fixed direction due to the directional processing, and the ease of movement of the magnetic domain walls is completely lost.

On the other hand, if the direction of magnetization of the magnetic domains is random, the domain walls will move until the directions of magnetization are aligned in the same direction, and this will cause internal friction and the vibration energy will be attenuated by thermal energy etc. be.

When the vibration-absorbing alloy of the present invention is placed in a strong magnetic field and magnetized, its vibration-absorbing ability disappears.

Figure 5 shows the state in which when a Fe-1 Cu-5%5i-15%Cr vibration absorbing alloy is placed in a magnetic field and magnetized, its vibration absorption capacity approaches zero, and when it is demagnetized, its vibration absorption capacity is restored. .

This is because the magnetic domains of vibration-absorbing alloys that have magnetic domains aligned in random directions are aligned in a certain direction due to magnetization, and the magnetic domain walls no longer move. Even if vibration or shock is applied from the outside, the vibration will not be damped.

However, when the alloy of the present invention in such a state is demagnetized again, the vibration absorbing ability is restored.

However, even if stainless steel having the same composition as the alloy of the present invention is demagnetized, no vibration absorption ability will be produced.

This is evidence that ordinary stainless steel does not have the same vibration absorption mechanism as the vibration absorption alloy of the present invention.

An alloy having vibration absorbing ability can be obtained by creating a state where magnetic domains are likely to move by high-temperature heat treatment, machining, or a combination of these.

The defect structure or internal strain in the crystal lattice described above is caused by the following reasons.

(a) When an alloy is heat-treated, additive elements precipitate, precipitate, or aggregate in the crystal lattice, resulting in internal strain, that is, lattice defects.

When internal strain occurs in a crystal, when vibrations are applied from the outside, the crystal lattice attempts to restore itself to a stable, undistorted state, resulting in dislocation of atoms within the crystal, which converts into thermal energy. Vibration applied from the outside disappears.

(b) Since the additive elements are precipitated at the magnetic domain boundaries of the crystal, these elements act as lubricants, making it easier for the magnetic domain walls to move.

This is also a defective structure, and vibrational energy is lost due to the movement of magnetic domains.

When an alloy is subjected to mechanical processing such as wire drawing, rolling, forging, bending, etc. for shaping, mechanical strain occurs in the crystal lattice, which improves mechanical strength, but reduces damping capacity.

This is because when mechanical strain occurs in the crystal lattice, the structure becomes rigid and it becomes difficult for magnetic domains to move, resulting in a decrease in attenuation ability.

For this reason, it is necessary to remove mechanical strain by heat treatment.

In the above heat treatment, (5) After homogeneous solution treatment by heating at a high temperature of 800 °C or higher below the melting point (approximately 1300 °C) for 1 minute to 100 hours,
When annealed, the vibration absorption capacity is maximized.

This is due to the homogenization of the material and the removal of strain through high-temperature heat treatment, which increases the movement of the domain walls, changes the direction of spontaneous magnetization, and generates eddy currents, resulting in the highest attenuation ability.

(B) Cold Working Knee However, mechanical strength is insufficient only by annealing, so cold working is subsequently performed.

Cold working improves mechanical strength, but reduces damping capacity.

Therefore, quenching is performed when a damping capacity and mechanical strength intermediate between cold worked and annealed states are required, and the quenching temperature is about 800° C. or slightly higher.

(C) Reheating knee after quenching When cold working is performed for the above purpose, mechanical strain occurs in the crystal, so in order to remove this strain, the temperature is lower than 100°C or below the quenching temperature (800°C). The mixture is heated for 100 hours or more, and then gradually cooled at a rate of 1° C. or less per second.

Next, the present invention will be explained with reference to examples.

After melting about 500 g of Fe and Cu having the composition shown in Table 1 in an alumina crucible in a high-frequency induction electric furnace while passing argon gas, the molten metal was thoroughly stirred and cast into an iron mold to form a square mold of 35 mm x 35 mm. Got a lump.

Next, this is forged into a round bar of approximately 10 mr/L,
After annealing at 1000℃ for 1 hour, cold drawing at room temperature
．． A 5 mm line was obtained.

A wire of a suitable length was cut from this, heated at 100°C for 1 hour, and then cooled at a rate of 100°C/hour to prepare a sample.

The damping capacity of such a sample was determined by the twisted pendulum method, and the results shown in Table 1 were obtained.

The measured values of typical alloys of the present invention are shown in Tables 2 to 4.

As is clear from Tables 1 to 4, the damping capacity of binary and ternary alloys is generally large in any processing state, and is particularly greatest in the annealed state, followed by the water-quenched state and the cold-worked state. It is gradually decreasing.

These values are several tens of times larger than those of ordinary metals.

Figure 1 shows the relationship between the composition of the Fe-Cu alloy and the damping capacity in the annealed state, and Figure 2 shows the relationship between the composition and the damping capacity of the Fe-1% Cu - Cr alloy in the annealed state. is the indication.

Figure 3 also shows 99.0% Fe-
1,0%Cu alloy, 84.0%Fe-1,0%Cu-
15,0% Cr alloy and 88,0% Mn-12,0%
The relationship between the damping ability of the Cu alloy and the heating temperature is shown.

From these drawings, it is clear that the damping ability of the alloy of the present invention is higher than that of Mn-Cu.
It can be seen that it is much larger than alloys at both room and high temperatures.

The alloy of the present invention has the characteristic that the elastic modulus and tensile strength are increased by adding subcomponents.

Table 5 shows a comparison of the general effects of adding the main components and subcomponents of the vibration absorbing alloy of the present invention.

As is clear from Table 5 above, when 0.1 to 5% of Cu is added to the iron-based alloy as the main component, the damping capacity, corrosion resistance,
Both mechanical strength and workability are improved.

However, if the copper content exceeds 5, the corrosion resistance will improve, but the damping capacity and workability will deteriorate, which is not preferable.

Further, if the copper content is less than 0.1, the desired damping ability cannot be obtained.

In addition, the Fe-Cu base alloy has sub-components of chromium 40 or less, aluminum, niobium, molybdenum, tungsten,
Any one or more elements selected from the group consisting of titanium, vanadium, and tantalum with a factor of 10 or less, silicon of 5 or less, and any one or two of cobalt and yttrium with a factor of 1 or less. Since the addition of these subcomponents improves all of the damping ability, corrosion resistance, mechanical strength, and processability, the addition of these subcomponents is considered to have the same effect as a substance with the same effect.

However, if these subcomponents are added in an amount exceeding the upper limit, any of the damping ability, corrosion resistance, mechanical strength, or workability will deteriorate, so it is not preferable to add them in an amount exceeding the upper limit.

The total amount of subcomponents added should not exceed 1% to 40%.

If the total amount of subcomponents added exceeds 40 parts, it is not preferable because the damping ability deteriorates and either corrosion resistance, mechanical strength, or workability deteriorates.

Further, when the total amount of the subcomponents is less than 1%, it is not preferable because the addition of the subcomponents has no effect.

The alloy of the present invention is very suitable as a vibration-absorbing alloy element for machinery that generates vibration and noise, such as aircraft, ships, and vehicles, or for precision instruments that generate vibration.

[Brief explanation of the drawing]

Figure 1 is a curve diagram showing the relationship between the composition and damping capacity in the annealed state of the Fe-Cu alloy of the present invention, and Figure 2 is a curve diagram showing the relationship between the composition and damping capacity of the Fe-Cu alloy of the present invention in the annealed state.
A curve diagram showing the relationship between the composition and damping capacity of the 1% Cu-Cr alloy in the annealed state, FIG. 3 shows the Fe-Cu alloy of the present invention.
Figure 4 is a characteristic diagram showing the orientation state of the magnetic domains of the vibration absorbing alloy of the present invention;
The figure is a characteristic diagram showing the state in which the damping ability of the vibration absorbing alloy of the present invention disappears and is restored due to magnetization and demagnetization in a magnetic field.

Claims (1)

[Claims] 1. Cu 0.01 to 5% as main component in weight ratio, 40% or less Cr as subcomponents, AA, Nb, Mo
. Any of W, 'ri, V, Ta below 10,
A total amount of 0.01 to 40 parts of Si of 5 parts or less, one or more of Co and Y of 1 part or less, and the balance Fe
A vibration-absorbing alloy consisting of and having a damping capacity of 3X10' or more. 2 Cu 0.01 to 5% as the main component and 40% or less Cr, Al, Nb, and Mo as subcomponents in terms of weight ratio. Any one or more of W, Ti, V, Ta, 10% or less, Si 5% or less, Si 5% or less, Co. The following treatment is applied to a compact of an alloy consisting of any one or two types of Y with a total amount of 0.01 to 40% of one or more types below 1%, and the balance is Fe.
After heating at a high temperature of ℃ or higher for 1 minute to 100 hours and performing homogeneous solution treatment, quenching is performed (B) After the above quenching, cold working is performed (C)
After the capacity processing of (B), the temperature ranges from 100℃ to quenching temperature (800℃).
℃) or less for 1 minute or more and 100 hours or less, and then slowly cooled at a rate of 1℃ or less per second to achieve a damping capacity of 3X10.
- A method for producing a vibration absorbing alloy, characterized by obtaining an alloy of 3 or more. 3 CuO, 01 to 5 as the main component and 40% or less of Cr, Al, Nb, and Mo as the subcomponents in terms of weight ratio. Total amount of one or more of W, Ti, V, Ta, or more than 10φ, Si of 5 or less, Co, Y, or more of 1 or less, 0.01 to 4
The following treatment is applied to a molded body of an alloy consisting of 0% and the remainder Fe.
After heating for a period of time and homogeneous solution treatment, annealing is performed by slow cooling at a rate of 1°C per second or less (B) Cold working is performed after the above annealing (C) After cold working in (B), 100°C to quenching temperature (
800℃) or less for 1 minute or more and 100 hours or less, and then slowly cooled at a rate of 1℃ or less per second to achieve a damping capacity of 3.
A method for producing a vibration-absorbing alloy characterized by obtaining an alloy of X10" or more.