JPH09157794A - High damping alloy and its production - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a material having high toughness and high strength by constituting a high damping alloy so that it has a composition containing specific weight percentages of C, Si, Mn, P, S, Cr, Al, and N and having the balance Fe. SOLUTION: The high damping alloy has a composition consisting of, by weight, <=0.02% C, 0.01-0.5% Si, <0.2% Mn, <=0.01% P, <=0.005% S, <0.5% Cr, 0.06-3.5% Al, <=0.006% N, and the balance Fe with inevitable impurities. Further, one or more elements among Cu, Ni, Mo, Nb, V, Ti, B, Ca, and REM can be added. The alloy is heated to 1000-1150 deg.C, hot-rolled under the conditions of 30-70% draft at <=930 deg.C and 830 deg.C rolling finishing temp., and then heat- treated, by which crystalline grain size and (200) diffraction intensity ratio are regulated to <=120μm and >=3.0, respectively. By this method, the steel excellent in damping property can be provided.

Description

Detailed Description of the Invention

[0001]

TECHNICAL FIELD The present invention relates to a damping alloy having a high damping property and a damping alloy having a high toughness as a structural material for ships, bridges, industrial machines and constructions.

[0002]

2. Description of the Related Art Recently, ships, bridges, industrial machines, and buildings tend to be required to have high damping properties at the same time in addition to toughness which is a basic characteristic of structural materials. That is, for example, the problem of suppressing noise and vibration during high-speed railway running on a bridge, large-scale civil engineering, and construction work by the damping effect of the structural material itself, and having sufficient toughness as a structural member is attempted. To do.

Conventional iron-based materials used as members for the purpose of damping property instead of resin sandwich type damping steel plate are high in hysteresis due to irreversible motion of domain wall movement under the action of alternating stress due to vibration. In order to obtain a damping property, a ferrite former is added to make the structure into a ferrite single phase, and it is divided into two types: a material to which Al and Si are added and a material to which Cr is positively added.

As an example of the former, Japanese Patent Laid-Open No. 4-99148
As described in Japanese Patent Publication, the Al content is up to 7.05% and S
There is a ferromagnetic damping alloy with i added up to 4.5%. An example of the latter is a ferromagnetic damping alloy with 8 to 30% of Cr as described in JP-A-52-73118. There are vibration alloys.

Further, in JP-A-6-220583 and JP-A-5-302148, there is disclosed a ferromagnetic damping alloy in which Mn is 0.1 or 0.2% or less and 1 to 5% of Cr is added. is there. In addition, the inventors of the present invention filed Japanese Patent Application No. 6-2589.
No. 82 proposed a ferromagnetic damping alloy in which Mn is added in an amount of 0.2 to 2.5% and Cr is added in an amount of 1 to 5%.

Ryohei Tanaka, Damping Material <Functions and Applications> Published by Kousendo March 1992, p192 to 197, as a ferromagnetic alloy, external stress causes movement of the magnetic domain wall, which causes hysteresis energy to cause vibration energy. Described to be absorbed.

[0007]

However, among these alloys, the alloy described in Japanese Patent Application Laid-Open No. 4-99148 has an inappropriate upper limit regulation of Al and Si addition amounts. This leads to the formation of a product, which acts as the point of origin of fracture, resulting in a decrease in toughness. Also,
Since the alloy described in JP-A-52-73118 has excessive Cr addition, the toughness of Cr-based inclusions is reduced as in the above case.

Further, in JP-A-6-220583 and JP-A-5-302148, the toughness is low because no aggressive measures for improving the toughness are taken. In addition, Japanese Patent Application Hei 6
No. 258982 has insufficient toughness because it has priority on securing toughness.

In the literature of damping materials, the mechanism of damping alloys is written, and there is no description on the improvement method, specific component system, manufacturing method, or method for simultaneously satisfying toughness in addition to damping property. . An object of the present invention is to provide a damping alloy having excellent damping properties and damping properties and high toughness.

[0010]

[Means for Solving the Problems]

(1)% by weight, C: 0.02% or less, Si: 0.01
% Or more and 0.5% or less, Mn: less than 0.2%, P: 0.
010% or less, S: 0.005% or less, Cr: 0.5%
Less than, Al: 0.060% or more, 3.5% or less, N:
A damping alloy containing 0.006% or less, the balance Fe and unavoidable impurities, and having a (200) diffraction intensity ratio of 3.0 or more.

(2)% by weight, C: 0.02% or less, S
i: 0.01% or more and 0.5% or less, Mn: 0.2% or more and 2.5% or less, P: 0.010% or less, S: 0.0
05% or less, Cr: less than 0.5%, Al: 0.060%
As a result, it contains 3.5% or less and N: 0.006% or less,
A vibration-damping alloy comprising the balance Fe and unavoidable impurities and having a (200) diffraction intensity ratio of 2.5 or more.

(3) Cu: 0.05 to 2.5 by weight%
%, Ni: 0.05-2.5%, Mo: 0.05-4.
5%, Nb: 0.005 to 0.2%, V: 0.005 to
0.2%, Ti: 0.005 to 0.1%, B: 0.00
The vibration damping alloy according to any one of (1) and (2), characterized in that it contains one or two or more of 03 to 0.005%.

(4)%: Ca: 0.001 to 0.
05%, REM: 0.001 to 0.1% 1 or 2
The damping alloy according to any one of (1) to (3), which contains a seed. (5) The damping alloy according to any one of (1) to (4), characterized in that high toughness is ensured by setting the crystal grain size to 120 μm or less.

(6) The heating temperature is 1000 to 1150 ° C.,
After the hot rolling at a rolling reduction temperature of 930 ° C. or less at 30 to 70% and a rolling finishing temperature of 830 ° C. or less, the temperature is cooled to room temperature.
The method for producing a vibration damping alloy according to any one of (1) to (5), characterized by performing a tempering or annealing heat treatment at 980 ° C.

(7) Rolling finishing temperature range is 630 to 83
The method for producing a vibration damping alloy according to (6), characterized in that hot rolling is performed at 0 ° C. (8) Roll finishing temperature range is Ar ₁ -20 ° C to Ar ₁ +
The method for producing a vibration damping alloy according to (6) or (7), characterized in that hot rolling at 50 ° C. is performed.

[0016]

The present invention has been made in view of the above circumstances, and in order to obtain a high damping property due to the hysteresis due to the irreversible motion of the domain wall movement under the action of alternating stress due to vibration, It is based on pure iron-based components in which the elements that cause harmful harmful elements, inclusions, and precipitates, interfere with domain wall movement, and greatly impair vibration damping are minimized.

Further, in the past, since the crystal grain boundary hindered the domain wall movement, the vibration damping property was improved only by coarsening the grain. However, as a result of various studies by the inventors, the vibration damping by the coarsening has been performed. As an alternative to the method for improving the vibration resistance, it has been found that the vibration damping property is significantly improved by increasing the (200) diffraction intensity. By increasing the (200) diffraction intensity, the <100> orientation parallel to the steel sheet surface is strengthened.

That is, the easy magnetization direction is strengthened in the direction parallel to the steel plate surface. It is a new discovery that the damping property is improved by strengthening the easy magnetization direction. This (200)
It was found that the vibration damping property is improved by setting the diffraction intensity ratio to 2.5 or more. When the (200) diffraction intensity ratio is 2.5 or more, the loss coefficient, which is an index of the vibration damping property, may be 0.02 or more. From the viewpoint of the vibration damping performance, (2)
The higher the (00) diffraction intensity ratio, the better, but in view of the balance with other steel material properties such as toughness, the (200) diffraction intensity ratio is preferably in the range of 2.5 to 12.0, resulting in 0.02 to 0. It is preferable to ensure a loss factor of 0.055.

Here, the (200) diffraction intensity ratio is (200) at a quarter thickness position in the plate thickness direction by X-ray diffraction.
The diffraction intensity was measured and the ratio to the (200) diffraction intensity of the random sample material in which the specific orientation was not strengthened or controlled was determined. As a result of this study, the maximum value of the (200) diffraction intensity ratio was about 15.

In order to increase the (200) diffraction intensity ratio, it is necessary to carry out low temperature rolling, and as a result of examination, 93
This can be achieved by setting the rolling reduction at 0 ° C. or less to 30% or more. Regarding the upper limit of the low temperature rolling temperature, alloy components, especially M
It is necessary to limit by n, and 930 ° C. may be used when Mn is less than 0.2%, but 88 when Mn is 0.2% or more.
Must be 0 ° C.

Therefore, the rolling finishing temperature is 830 ° C. (0.
For high Mn steel of 2% or more, it becomes 780 ° C. or less. Furthermore, as a result of a detailed study for improving the vibration damping property, by setting the rolling finishing temperature to Ar ₁ −20 ° C. to Ar ₁ + 50 ° C. (2
It has been found that the 00) diffraction intensity ratio is further improved and the vibration damping property is further improved.

Further, Mn was found as an element capable of significantly increasing the strength without impairing the vibration damping property and the toughness. By adding Mn in an amount of 0.2% or more, it is possible to achieve both the vibration damping property and the strength, or to improve all of the vibration damping property, the strength and the toughness.

Next, in order to improve the toughness, the crystal grain size is set to 12
It is necessary to make it 0 μm or less. When the rolling finishing temperature is lower than 630 ° C. in the manufacturing method for setting the (200) diffraction intensity ratio to 2.5 or higher, the crystal grain size may exceed 120 μ, so the rolling finishing temperature is set to 630 ° C. or higher. However, if Mn is less than 0.2%, the grain size may exceed 120μ unless the rolling finishing temperature is set to 680 ° C or higher.

After hot rolling, tempering or annealing heat treatment is necessary in order to increase the (200) diffraction intensity ratio and reduce the strain introduced into the steel sheet by rolling. Since the diffraction intensity ratio becomes low, the upper limit temperature is 980 ° C. However, Mn is 0.2%
In the above cases, the (200) diffraction intensity ratio may be low, so 930 ° C. must be the upper limit.

As described above, the vibration damping property is improved by introducing the texture even in the fine grain structure, and further improvement of the vibration damping property was examined. As a result, it was found that by adding Si, which is a ferrite former, some coarse grains are achieved in the process of strain relief heat treatment after hot rolling, and the vibration damping property is further improved. The strength is also increased by the addition of Si.

Next, the reasons for limitation of the present invention will be described. Since C acts as an obstacle to the movement of the domain wall even if it is in a solid solution state or is precipitated as a carbide and reduces the vibration damping property, the lower the C is, the more preferable the upper limit is 0.02%.

Since Si is important as a deoxidizing material,
It is necessary to add more than 01%, but if added over 0.5%, it acts as an obstacle to domain wall movement in a solid solution state to lower the vibration damping property, so the upper limit is made 0.50%.

Mn is a solid solution strengthening element, has no effect on improving vibration damping property and toughness, and the addition of Mn increases the cost. Therefore, Mn is 0.2% except when high strength of 360 MPa or more is required. It is better to limit it to less than. Especially 36
When high strength of 0 MPa or more is required, Mn is the only element that enhances the strength without deteriorating the vibration damping property and the toughness, so 0.2% or more of Mn is added. Mn fixes S and suppresses grain boundary embrittlement, and at the same time, improves strength by a solid solution strengthening element. However, if the addition amount exceeds 2.5%, the vibration damping property deteriorates, so the upper limit of the addition amount of Mn is 2.
5%.

P and S form a non-metallic inclusion in the steel and segregate to impede the movement of the magnetic domain wall to lower the vibration damping property. Therefore, P is set to 0.010% or less and S is set to 0.005% or less.

In addition to being important as a deoxidizing material, Al is an important ferrite former and is indispensable for improving the vibration damping property, and it is necessary to add more than 0.060%. on the other hand,
If it is added in excess of 3.5%, inclusions such as Al ₂ O ₃ are generated, which acts as a point of occurrence of fracture, resulting in a significant decrease in toughness. Therefore, the addition range of Al is 0.060
% And 3.5% or less.

Cr is a ferrite former, which is an element that coarsens the crystal grains by adding it and slightly improves the vibration damping property, but at the same time causes toughness deterioration and is an expensive element, so it is added as much as possible. Since it is preferable to reduce the amount, the upper limit is limited to less than 0.5%.

N, which acts as an obstacle to the movement of the domain wall even if it is in a solid solution state or precipitates as a nitride, lowers the vibration damping property, so that it is preferably as low as possible, and the upper limit is made 0.006%. Furthermore, Cu, Ni, Mo, Nb, which is added as necessary,
V, Ti, and B are elements effective in increasing strength, and the above amount was set as the lower limit as a range in which the effect is not insufficient, and the above amount was set as the upper limit as the range in which the vibration damping property and toughness were not deteriorated. Further, Ca and REM added as necessary are elements effective for improving the toughness, and the above amount is set as the lower limit as a range in which the effect is not insufficient, and a range in which the toughness is rather lowered and the vibration damping property is not lowered. The upper limit was the above amount.

Regarding the manufacturing conditions, the heating temperature is 1150 ° C. or lower in order to make the heated austenite grains fine and the (200) diffraction intensity ratio high, and further 1000 ° C. or higher in order to eliminate the temperature deviation in the steel sheet during heating. And

Regarding the rolling conditions, in order to raise the (200) diffraction intensity ratio, low temperature rolling is necessary, and the upper limit of the temperature is 930 ° C. when Mn is less than 0.2%. When Mn is 0.2% or more, the temperature is lower than 880.
Perform at or below ° C. Rolling with a rolling reduction of 30% or more is required in a range of these temperatures or less, but if the rolling reduction exceeds 70%, the load on the rolling mill becomes large, and the rolling time becomes long, which causes a cost increase. , The upper limit is 7
0%.

The rolling finishing temperature is 830 ° C. or less (780 ° C. when Mn is 0.2% or more) because the rolling is performed at a rolling reduction of 30% or more in the low temperature rolling under the above conditions, but 68
If the temperature is lower than 0 ° C. (630 ° C. when Mn is 0.2% or more), the ferrite region may be rolled and the crystal grain size may exceed 120 μ, which may lower the toughness, so the lower limit is 680 ° C. (Mn
Is 0.2% or more, the temperature is 630 ° C.). Therefore, the rolling finishing temperature range is 630 to 830 ° C. further,
Improved finish rolling temperature (200) by the _{Ar 1 -20 ℃ ~Ar 1 + 50} ℃ diffraction intensity ratio further damping characteristics are further improved.

After hot rolling and cooling to room temperature, (20
0) In order to further improve the diffraction intensity ratio and reduce the strain introduced into the steel sheet by rolling, tempering or annealing heat treatment is required, and heat treatment at 680 ° C. or higher is performed, but the (200) diffraction intensity ratio is The upper limit temperature is set to 980 ° C., because heat treatment weakens at high temperatures. The relationship between the temperature range of the heat treatment and the (200) diffraction intensity ratio also depends on the Mn content of the alloy, and when Mn is less than 0.2%, 680 ° C or higher and 980 ° C or higher.
A temperature range of ℃ or less is good, and when Mn is 0.2% or more, heat treatment in a temperature range of 630 to 930 ° C is good.

[0037]

[Examples] Matching alloys having the ranges of components shown in Table 1 were prepared, and a plate-shaped test piece having an original thickness of 40 mm and a width of 400 mm was processed, and the vibration damping property was measured by the mechanical impedance method. .

[Table 1]

[0038]

[Table 2]

[0039]

[Table 3]

[0040]

[Table 4]

Among the alloys shown in Table 1, steels A1 to A5 and B
1 to B5 are alloys in the composition range of the present invention, and steels F1 to F5
8 and G1 to G10 are alloys outside the compositional range of the present invention. A1-A5 and F1-F8 are low Mn and less than 0.2%, B1-B5 and G1-G10 are high Mn and 0.2.
~ 2.5%. The various properties of these steels produced under the production conditions shown in Table 2 are also shown in the table. Each steel sheet having a thickness of 6 mm or more was hot-rolled, cooled to room temperature, and then heat-treated. Those having a plate thickness less than that were hot-rolled, wound, and then heat-treated.

Examples 1 to 12 are examples of the present invention, and Examples 13 to 3 are
8 is a comparative example. Examples 1 to 3 and 13 to 19 are 30 m thick
m, 7-9, 25-32 is 25 mm thick, Example 4 is 2 m thick
m, Example 10 is 1.8 mm thick, Examples 5 and 6 are 55 mm thick, Examples 11 and 12 are 35 mm thick, Examples 20-24 are 20 mm thick,
Examples 33 to 38 have a plate thickness of 18 mm.

Looking at the low Mn materials of Examples 1 to 6,
The inventive example of Example 1 has a (200) diffraction intensity ratio of 3.0 or more and high vibration damping performance (η ≧ 0.025). Example 2
No. 6 has a rolling finishing temperature of 680 ° C. or higher, and (200)
The diffraction intensity ratio is 3.0 or more, the crystal grain size is 120 μ or less, and high vibration damping performance (η ≧ 0.025) and high toughness (≧ 8
0J). Since Examples 3 and 4 contain the selective element effective for increasing the strength, the strength is higher, and Examples 5 and 6 contain the selective element effective for increasing the toughness, and therefore the higher toughness (≧
100J).

Next, looking at the high Mn materials of Examples 7 to 12, the invention example of Example 7 has a (200) diffraction intensity ratio of 2.5.
With the above, with high strength (≧ 360 MPa), high vibration damping performance (η ≧
0.020). In Examples 8 to 12, the rolling finishing temperature was 630 ° C. or higher, the (200) diffraction intensity ratio was 2.5 or higher, the crystal grain size was 120 μ or less, and the high strength (≧ 36).
It has high vibration damping performance (η ≧ 0.020) and high toughness (≧ 80 J) at 0 MPa. Since Examples 9 and 10 contain the selective element effective for increasing the strength, the strength is further increased (≧ 390 MPa).
In a), Examples 11 and 12 have higher toughness (≧ 100 J) because they contain a selective element effective for increasing toughness.

Looking at Comparative Examples 13 to 24 having low Mn, Comparative Example 13 has a (200) diffraction intensity ratio of 3.0 or more, but has a crystal grain size of more than 120 μm, a high C, and is excellent in vibration damping performance and toughness. Low. In Example 14, the (200) diffraction intensity ratio is 3.0 or more and the crystal grain size is 120 μ or less, but Si is high and the vibration damping performance is low. In Examples 15 and 16, the (200) diffraction intensity ratio is 3.0 or more and the crystal grain size is 120 μ or less.
5 has a high P and Example 16 has a high S, and the vibration damping performance is low.

In Example 17, the (200) diffraction intensity ratio is 3.0 or more and the crystal grain size is 120 μ or less, but Cr is high,
Low toughness. Example 18 has a (200) diffraction intensity ratio of 3.0 or more and a crystal grain size of 120 μ or less, but has a low Al content,
Vibration control performance is low. Example 19 has a (200) diffraction intensity ratio of 3.
Although it is 0 or more and the crystal grain size is 120 μ or less, Al is high, and the vibration damping property and the toughness are low.

In Example 20, the (200) diffraction intensity ratio is 3.0 or more and the crystal grain size is 120 μ or less, but N is high and the vibration damping performance is low. Example 21 has a high heating temperature, and Example 22 has 93
The rolling reduction at 0 ° C. or lower is low, the (200) diffraction intensity ratio is low, the crystal grain size is more than 120 μm, and the vibration damping performance and toughness are low.
In Example 23, the heat treatment temperature is low, the (200) diffraction intensity ratio is low, and the crystal grain size is 120 μ or less, but the vibration damping performance is low. In Example 24, the heat treatment temperature is high, the (200) diffraction intensity ratio is low, and the crystal grain size is 120 μm or less, but the vibration damping performance is low.

On the other hand, looking at the comparative example of high Mn, the comparative example 25 has a (200) diffraction intensity ratio of 2.5 or more, but has a crystal grain size of more than 120 μ, a high C, and low vibration damping performance and toughness. . In Example 26, the (200) diffraction intensity ratio is 2.5 or more and the crystal grain size is 120 μ or less, but Si is high and the vibration damping performance is low. In Example 27, the (200) diffraction intensity ratio is 2.5 or more and the crystal grain size is 120 μ or less, but the Mn is low and the intensity is low.

In Example 28, the (200) diffraction intensity ratio is 2.5 or more and the crystal grain size is 120 μ or less, but the Mn is high and the vibration damping performance is low. In Examples 29 and 30, the (200) diffraction intensity ratio is 2.5 or more and the crystal grain size is 120 μ or less.
9 has a high P, and Example 30 has a high S, and the vibration damping performance is low. In Example 31, the (200) diffraction intensity ratio is 2.5 or more and the crystal grain size is 120 μ or less, but Cr is high and the toughness is low.

Example 32 has a (200) diffraction intensity ratio of 2.5 or more and a crystal grain size of 120 μ or less, but has a low Al content,
Low strength and vibration damping performance. Example 33 has a (200) diffraction intensity ratio of 2.5 or more and a crystal grain size of 120 μ or less.
l is high and toughness is low. In Example 34, the (200) diffraction intensity ratio is 2.5 or more and the crystal grain size is 120 μ or less, but N
Is high and the damping performance is low.

The heating temperature is high in Example 35, and 880 in Example 36.
Low rolling reduction below ℃, low (200) diffraction intensity ratio,
If the crystal grain size exceeds 120μ, vibration damping performance and toughness are low. Example 3
7 has a low heat treatment temperature and a low (200) diffraction intensity ratio,
The crystal grain size is 120 μ or less, but the vibration damping performance is low. In Example 38, the heat treatment temperature is high, the (200) diffraction intensity ratio is low, and the crystal grain size is 120 μm or less, but the vibration damping performance is low.

Next, with respect to the steels P1, P2, Q1, Q2, R1 and R2 of the alloys in the composition range of the present invention shown in Table 3, Table 4 is shown.
Various characteristics of the product manufactured under the manufacturing conditions of the present invention shown in are also shown. P1, Q1 and R1 are low Mn less than 0.2%
Steel, P2, Q2 and R2 are high Mn steels of 0.2% or more and 2.5% or less. Examples 39 to 41 and Examples 45 to 47 are examples in which the rolling finishing temperature is in a more desirable range. Examples 39-4
1 has a thickness of 25 mm, and Examples 45 to 47 have a thickness of 20.
mm. Ar ₁ of steels P1, Q1 and R1 is 70 each
A of steels P2, Q2 and R2 at 5 ℃, 730 ℃ and 700 ℃
r ₁ is 675 ° C., 680 ° C., and 670 ° C., respectively.

[0053]

[Table 5]

[0054]

[Table 6]

[0055]

[Table 7]

In Examples 39 to 41 and Examples 45 to 47, the rolling finishing temperature was in the range of Ar ₁ + 50 ° C. to Ar ₁ -20 ° C., and the (200) diffraction intensity ratio was 4.0 or more, and further excellent control was obtained. Vibration performance (η ≧ 0.03) and rolling finish temperature is A
Examples 42 to 4 not in the range of r ₁ + 50 ° C. to Ar ₁ −20 ° C.
4 and Examples 48 to 51 have better vibration damping performance.

[0057]

Industrial Applicability According to the present invention, it is possible to provide a steel having a (200) diffraction intensity ratio of 2.5 or more (loss coefficient of 0.03 or more) and excellent vibration damping performance. In addition to the vibration control performance, the steel has at least one of high toughness of 0 ° C absorbed energy of V notch Charpy impact test ≧ 80 J or high strength of tensile strength ≧ 360 MPa or more at the same time. Ships, bridges,
It becomes possible to supply industrial machinery and structural materials for construction, and the effect on the industry is extremely large.

Claims (8)

[Claims] 1. By weight%, C: 0.02% or less, Si: 0.01% or more, 0.5% or less, Mn: less than 0.2%, P: 0.010% or less, S: 0 0.005% or less, Cr: less than 0.5%, Al: 0.060% or more, 3.5% or less, N: 0.006% or less, and the balance Fe and unavoidable impurities, (2
00) A damping alloy having a diffraction intensity ratio of 3.0 or more. 2. By weight%, C: 0.02% or less, Si: 0.01% or more, 0.5% or less, Mn: 0.2% or more, 2.5% or less, P: 0.010. % Or less, S: 0.005% or less, Cr: less than 0.5%, Al: 0.060% or more, 3.5% or less, N: 0.006% or less, and the balance Fe and unavoidable impurities Consists of (2
00) A damping alloy having a diffraction intensity ratio of 2.5 or more. 3. By weight%, Cu: 0.05 to 2.5%, Ni: 0.05 to 2.5%, Mo: 0.05 to 4.5%, Nb: 0.005 to 0. 2%, V: 0.005-0.2%, Ti: 0.005-0.1%, B: 0.0003-0.005%, 1 type (s) or 2 or more types are contained, It is characterized by the above-mentioned. The damping alloy according to claim 1. 4. One or two of Ca: 0.001 to 0.05% and REM: 0.001 to 0.1% by weight is contained.
The vibration damping alloy according to any one of 1 to 3. 5. The vibration damping alloy according to claim 1, wherein a high toughness is ensured by controlling the crystal grain size to 120 μm or less. 6. A heating temperature of 1000 to 1150 ° C., 93
The rolling reduction at 0 ° C or lower is 30 to 70%, and the rolling finishing temperature is 83.
After hot rolling at 0 ° C or lower, cooled to room temperature,
The method for producing a vibration-damping alloy according to any one of claims 1 to 5, which comprises performing a tempering or an annealing heat treatment at 0 ° C. 7. The rolling finishing temperature range is 630 to 830 ° C.
The method for producing a vibration-damping alloy according to claim 6, wherein hot rolling is performed. 8. A rolling finishing temperature in a range of Ar ₁ -20 ° C.
The method for producing a vibration damping alloy according to claim 6 or 7, wherein hot rolling is performed at Ar ₁ + 50 ° C.