JP2007321243A - HIGH-STRENGTH HIGH-DAMPING Fe-Mn-Cr-Ni ALLOY, MANUFACTURING METHOD THEREFOR, AND FORMED BODY THEREOF - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide alloy which has low manufacturing costs, assurable quality, high strength and high damping property, a manufacturing method therefor and a formed body thereof. <P>SOLUTION: The alloy which has composition consisting of, by weight, ≤0.05% carbon, 15 to <18% manganese, 9 to <15% chromium, 0.01 to <4% nickel, 0.01 to <0.05% aluminum, ≤0.01% nitrogen and the balance iron with inevitable impurities, is melted and cast. The resultant cast alloy is heated uniformly, hot worked, and further cold worked if necessary to be formed into a stock. Subsequently, solution heat treatment is applied at 800 to <1,000°C and further working is applied at 10 to 60% draft at ordinary temperature or at 50 to 200°C to allow an epsilon martensite phase of ≥10% to occur. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a high-strength, high-damping capacity Fe—Mn—Cr—Ni alloy, a method for producing the same, and a molded body thereof.

  Conventionally, in the fields of automobiles, precision equipment, electronic equipment, and medical equipment, provision of materials having a function of reducing vibration and noise has been demanded. In response to this, materials having vibration damping ability include lead, cast iron, Mn—Cu alloy, Mg—Zr alloy, Mg—Ni alloy, Al—Zn alloy, Fe—Cr—Al alloy, Ni—Ti alloy, Cu -Al-Ni alloys and the like are known. Such a material has excellent vibration damping capability, but its mechanical properties are poor and cannot be used for anything other than special applications, and it contains a lot of expensive elements, which increases the price of alloy materials. Application was extremely limited.

  In order to solve such problems, a high-strength and high-damping capacity Fe—Cr—Mn alloy and a method for producing the same have been disclosed as materials having high mechanical strength and vibration damping capacity. In this patent, a material composed of Cr: 9 to 15% by weight, Mn: 18 to 26% by weight, Fe: balance iron is subjected to solution heat treatment at a temperature of 1000 to 1150 ° C. and then cooled to 15 to 80%. A high-strength, high-damping capacity Fe—Cr—Mn alloy and a method for producing the same have been disclosed, characterized in that an ε-martensite phase of 40% or more is developed by performing inter-working. The Fe—Cr—Mn alloy is compositionally based on stainless steel, and therefore its mechanical properties are almost the same as stainless steel, and its vibration damping capacity is comparable to lead or cast iron. This is an epoch-making invention that solves the above problems (see, for example, Patent Document 1).

  Further, it contains 10 to 24% by weight of manganese, carbon as an impurity of 0.2% by weight or less, silicon of 0.4% by weight or less, sulfur of 0.05% by weight or less and phosphorus of 0.05% by weight or less, with the remainder being Fe. An ingot is produced by casting the molten metal composition, which is homogenized at 1000-1300 ° C. for 12-40 hours and hot-rolled, further heated at 900-1100 ° C. for 30-60 minutes, and air-cooled at room temperature. Alternatively, a method for producing an Fe—Mn vibration damping alloy is disclosed, which is water-cooled and cold-worked at a rolling rate of 30% or less near room temperature (25 ± 50 ° C.) (for example, a patent) Reference 2).

Japanese Patent No. 3378565 Japanese Patent No. 2637371

  However, according to the technique disclosed in Patent Document 1, the mechanism for expressing the vibration damping ability is due to the interaction between the γ / ε phase with the epsilon-martensite phase generated in the γ phase. Since the method for regulating impurity elements, particularly carbon and nitrogen, which have a large effect on this action is not shown in the above-mentioned patent, the loss coefficient (η) representing the vibration damping ability varies depending on the production or part. The above and quality assurance problems occur, and this solution is required for practical use.

  Further, according to the technique disclosed in Patent Document 1, the manganese composition is claimed to be 18 to 26% by weight. However, when this material is melted, the manganese component is easily evaporated, so the yield of the manganese alloy to be added. However, manganese has the drawback of significantly increasing the melting loss of the refractory used at the time of smelting, which increases the cost of smelting, so that the industrial uses are extremely limited. In addition, the materials for electronic equipment, precision equipment, and medical equipment, which are the main applications of the high-strength, high-damping capacity Fe-Mn-Cr-Ni alloy of the present invention, have the same rust resistance and non-resistance as conventional stainless steel. Although magnetism is required, the Fe—Cr—Mn alloy according to the invention of Patent Document 1 is insufficient in this respect.

  The Fe—Mn vibration damping alloy disclosed in Patent Document 2 is theoretically equivalent to that of Patent Document 1, but cannot be used for any of the above applications because of its extremely poor rust resistance.

  In addition, conventional bolts and nuts, cutting tool supports, ball screws, vibration isolation tables, hard disk drive suspensions, honeycomb structures, springs, steel balls, automobile oil tanks, engine gaskets, exhaust gas purification device components, and other controls Since molded bodies such as vibration parts are made by processing normal steel or stainless steel, the vibration damping capacity of the material itself is extremely small, so from the viewpoint of functions related to vibration, noise and vibration control. Is insufficient.

  The high-strength and high-damping capacity Fe-Mn-Cr-Ni alloy provided by the present invention is carbon 0.05 wt% or less, manganese 13 wt% or more, less than 18 wt%, chromium 9 wt% or more, less than 15 wt%, It consists of nickel 0.01 wt% or more, less than 6 wt%, aluminum 0.01 wt% or more, less than 0.05 wt%, nitrogen 0.01 wt% or less, the balance iron and inevitable impurities, and the epsilon martensite phase is It is characterized by being 10% or more (hereinafter referred to as the first invention).

  Furthermore, the high-strength and high-damping capacity Fe—Mn—Cr—Ni alloy provided by the present invention has a tensile strength of 700 MPa or more and 1200 MPa or less, and a loss coefficient (η) (hereinafter referred to as “measured by the test method defined in JIS G0602”). The loss coefficient (η) is 0.005 or more and 0.10 or less (hereinafter referred to as the second invention).

  Further, the method for producing a high-strength and high-damping capacity Fe—Mn—Cr—Ni alloy provided by the present invention includes carbon 0.05 wt% or less, manganese 13 wt% or more, less than 18 wt%, chromium 9 wt% or more, Less than 15 wt%, nickel 0.01 wt% or more, less than 6 wt%, aluminum 0.01 wt% or more, less than 0.05 wt%, nitrogen 0.01 wt% or less, balance iron and inevitable impurities The melted and cast material is subjected to homogenization heat treatment, then subjected to hot working, further subjected to cold working as necessary, heated at 800 ° C. or more and less than 1000 ° C., and then cooled with water or air. The heat treatment is performed, and if necessary, further cold working is performed (hereinafter referred to as the third invention).

  Furthermore, the method for producing a high-strength, high-damping capacity Fe—Mn—Cr—Ni alloy provided by the present invention is a method in which the Fe—Mn—Cr—Ni material after the solution heat treatment is treated at room temperature or a temperature of 50 ° C. or more and 200 ° C. or less. The processing is performed at a processing rate of 10% or more and 60% or less (hereinafter referred to as a fourth invention).

  And the compact | molding | casting of the high intensity | strength high damping ability Fe-Mn-Cr-Ni alloy which this invention provides is made from the high strength, high damping ability Fe-Mn-Cr-Ni alloy of 1st or 2nd invention. Bolts and nuts, cutting tool supports, ball screws, vibration isolation tables, hard disk drive suspensions that are processed to be used under vibration stresses of 10% or more and 50% or less of 0.2% proof stress in tensile tests , Honeycomb structures, springs, steel balls, automobile oil tanks, engine gaskets, exhaust gas purification device members, vibration-damping parts, and the like (hereinafter referred to as fifth invention).

  The high-strength, high-damping capacity Fe—Mn—Cr—Ni alloy according to the first or second invention provided by the present invention is 0.05% by weight or less of carbon, 13% by weight or more of manganese and less than 18% by weight, chromium 9 % By weight or more, less than 15% by weight, nickel 0.01% by weight or more, less than 6% by weight, aluminum 0.01% by weight or more, less than 0.05% by weight, nitrogen 0.01% by weight or less, remaining iron and inevitable impurities A high-strength, high-damping capacity Fe-Mn-Cr-Ni alloy characterized by having an epsilon-martensite phase of 10% or more, and a tensile strength of 700 MPa or more and 1200 MPa or less, a loss factor (η ) Is 0.005 or more and 0.10 or less, the manufacturing cost is low, the technical and quality assurance problems are solved, and the nickel addition has good rust resistance and It is magnetized.

  Moreover, in the manufacturing method of the Fe-Mn-Cr-Ni alloy according to the third or fourth invention provided by the present invention, since manganese is kept low, there is little refractory refractory loss during melting. Since the manufacturing cost is low and measures against carbon and nitrogen are taken, the variation in loss factor (η) from manufacturing to manufacturing is small, so that technical and quality assurance problems are solved.

  Also, a bolt / nut and cutting tool support machined to be used under a vibration stress of 10% to 50% of the 0.2% proof stress in the tensile test of the alloy according to the fifth invention provided by the present invention Bodies, ball screws, vibration isolation tables, hard disk drive suspensions, honeycomb structures, springs, steel balls, automobile oil tanks, engine gaskets, exhaust gas purification devices, and other vibration-damping parts Since it has high strength and high vibration damping capability, it is highly functional from the viewpoint of vibration resistance, noise resistance, and vibration control.

Here, in the first invention of the present invention, the carbon content is set to 0.05% by weight or less because the impurity element that adversely affects the interaction between the γ / ε phases expressing the vibration damping ability, particularly carbon In order to improve and stabilize the vibration damping capacity by setting the upper limit of the value, if the carbon content exceeds 0.05% by weight, the loss coefficient (η) indicating the vibration damping capacity is lowered and becomes unstable. It is. For nitrogen, which has the same effect as carbon, the amount of nitrogen in steel is 0.01% by weight or less, and the aluminum content is 0.01% by weight or more and 0.05% by weight or less. This is to eliminate the harm of reducing the vibration damping ability due to solid solution nitrogen inevitably mixed in the atmosphere during melting production by making the nitrogen in the steel into the form of inclusions with a large AlN. That is, if the aluminum content is less than 0.01% by weight, the aluminum content necessary for bonding with nitrogen in the steel may be insufficient. If the aluminum content exceeds 0.05% by weight, the surface of the alloy is caused by excess aluminum. This is because Al ₂ O ₃ -based defects are likely to occur inside. Further, if the nitrogen content in the steel exceeds 0.01% by weight, a large amount of aluminum combined with this is required, so that Al ₂ O ₃ -based defects due to aluminum increase.

  Furthermore, in the first invention of the present invention, the manganese content is set to 13 wt% or more and less than 18 wt% by setting the nickel content to 0.01 wt% or more and 6 wt% or less. Thus, it is intended to reduce the manufacturing cost by facilitating the melting of the alloy while maintaining the interaction effect between the γ / ε phases that express the vibration damping capability. That is, the present inventors have studied the interrelationship between the nickel component and the manganese component that stabilize the austenite of the steel and have the effect of exhibiting damping properties. As a result, A value = Mn (%) + Ni (%) Using this A value, an attempt was made to substitute a nickel component for a part of the manganese component that raises the melting cost due to the refractory melt. It has been found that the manganese content can be made 13 wt% or more and less than 18 wt% by setting the nickel content to 0.01 wt% or more and 6.00 wt% or less. Here, when the nickel content is less than 0.01% by weight, the above-mentioned effect of the vibration damping performance is insufficient, and when it exceeds 6.0% by weight, the production cost is unnecessarily increased. Absent. Accordingly, the manganese content can be limited to 13% by weight or more and less than 18% by weight.

  Furthermore, in the second invention of the present invention, the tensile strength of the high-strength, high-damping ability Fe—Mn—Cr—Ni alloy is 700 MPa to 1200 MPa and the loss factor (η) is 0.005 to 010. When the tensile strength is less than 700 MPa and the loss factor (η) is less than 0.005, a high-performance molded product cannot be produced from the viewpoint of vibration resistance, noise resistance and vibration suppression, and the tensile strength is 1200 MPa. The reason why the loss factor (η) is 0.10 or less is that the mechanical properties deteriorate when the loss coefficient (η) is 0.10 or less.

  Further, in the third invention of the present invention, the solution heat treatment temperature is set to 800 ° C. or more and less than 1000 ° C., when the solution heat treatment exceeding 1000 ° C. is performed, the crystal grains become abnormally large, and the subsequent cold working Therefore, it is essential to set the heat treatment temperature to 1000 ° C. or lower. Moreover, it is because it will not be in a solid solution state, but solution heat treatment will become inadequate when it is less than 800 degreeC.

  Furthermore, in the fourth invention of the present invention, the Fe—Mn—Cr—Ni material after the solution heat treatment is processed at a processing rate of 10% or more and 60% or less at room temperature or a temperature of 50 ° C. or more and 200 ° C. or less. This is because the required loss factor (η) cannot be obtained if the processing rate is less than 10%, and the mechanical properties deteriorate if it exceeds 60%.

  Furthermore, in the fifth invention of the present invention, the high-strength, high-damping capacity Fe—Mn—Cr—Ni alloy is used as a bolt / nut, cutting tool support, ball screw, vibration isolation table, hard disk drive suspension, honeycomb. 10% of 0.2% proof stress in tensile test of the alloy when applied to molded bodies such as structures, springs, steel balls, automobile oil tanks, engine gaskets, exhaust gas purifying devices and other damping parts As mentioned above, the reason for using it under a vibration stress of 50% or less is to efficiently absorb vibration energy with respect to the vibration stress imparted with the ε / γ phase interface of the metal crystal structure of the alloy. is there. That is, if it is 10% or less, vibration absorption is insufficient, and if it exceeds 50%, there is a risk of permanent set, that is, so-called “sagging” due to vibration.

  Hereinafter, the present invention will be described by way of examples.

Example 1 is an example of the first invention.
Composition is within the scope of the present invention 0.02% carbon, 17% manganese, 12% chromium, 3% nickel, 0.03% aluminum, 0.005% nitrogen, balance iron and inevitable The composition comprising impurities was melted and cast in a high frequency melting furnace to obtain a 5 kg ingot. After surface cutting of the obtained ingot, heat treatment at 1100 ° C. for 1 hour, forming a plate with a thickness of 5.0 mm by hot rolling, removing the oxide layer on the surface by pickling, and then cold rolling After obtaining a 1.0 mm plate, a solution heat treatment was performed at 900 ° C., and then a treatment for imparting 30% cold work vibration damping capability was performed, and this was treated as Example 1- (1) of the present invention. ).

  Further, the composition is within the scope of the present invention, 0.02% carbon, 13.5% manganese, 12% chromium, 5.5% nickel, 0.03% aluminum, 0.005% nitrogen. %, The remaining iron and the composition consisting of the remaining iron and inevitable impurities were melted and cast in a high-frequency melting furnace to obtain a 5 kg ingot. After surface cutting of the obtained ingot, heat treatment at 1100 ° C. for 1 hour, forming a plate with a thickness of 5.0 mm by hot rolling, removing the oxide layer on the surface by pickling, and then cold rolling After obtaining a 1.0 mm plate, solution heat treatment was performed at 900 ° C., and then a treatment for imparting 30% cold work vibration damping capability was performed, and this was performed as Example 1- (2) of the present invention. ).

Comparative Example 1

  As Comparative Example 1, it is composed of carbon 0.06% by weight, manganese 17% by weight, chromium 12% by weight, nickel 3% by weight, aluminum 0.03% by weight, nitrogen 0.005% by weight, the remaining iron, iron and inevitable impurities. The alloy was melted and cast in a high-frequency melting furnace to obtain a 5 kg ingot. The obtained ingot was subjected to surface cutting and then heat-treated at 1100 ° C. for 1 hour to obtain a plate thickness of 5.0 mm by hot rolling, and then the surface oxide layer was removed by pickling, followed by cold rolling and 1.0 mm. After obtaining the plate, solution heat treatment was performed at 900 ° C., and then a treatment for imparting 30% cold work vibration damping capability was performed.

Comparative Example 2

  As Comparative Example 2, 0.02 wt% carbon, 17 wt% manganese, 12 wt% chromium, 3 wt% nickel, 0.005 wt% aluminum, 0.010 wt% nitrogen, the remaining iron balance iron, and inevitable impurities. The alloy was melted and manufactured in a high-frequency melting furnace to obtain a 5 kg ingot. The obtained ingot was subjected to surface cutting and then heat-treated at 1100 ° C. for 1 hour to obtain a plate thickness of 5.0 mm by hot rolling, and then the surface oxide layer was removed by pickling, followed by cold rolling and 1.0 mm. After obtaining the plate, solution heat treatment was performed at 900 ° C., and then a treatment for imparting 30% cold work vibration damping capability was performed.

Comparative Example 3

  As Comparative Example 3, 0.06% by weight of carbon, 22% by weight of manganese, 12% by weight of chromium, 0.01% by weight of nickel, 0.005% by weight of aluminum, 0.010% by weight of nitrogen, the remaining iron, iron and inevitable impurities An alloy consisting of the above was melted and produced in a high frequency melting furnace to obtain a 5 kg ingot. The obtained ingot was subjected to surface cutting and then heat-treated at 1100 ° C. for 1 hour to obtain a plate thickness of 5.0 mm by hot rolling, and then the surface oxide layer was removed by pickling, followed by cold rolling and 1.0 mm. Thereafter, a solution heat treatment was performed at 1050 ° C., and then a treatment for imparting 30% cold work vibration damping capability was performed.

Comparative Example 4

  As Comparative Example 4, carbon 0.02 wt%, manganese 17 wt%, chromium 0.01 wt%, nickel 0.01 wt%, aluminum 0.001 wt%, nitrogen 0.010 wt%, balance iron balance iron and An alloy composed of inevitable impurities was melted and manufactured in a high-frequency melting furnace to obtain a 5 kg ingot. The obtained ingot was subjected to surface cutting and then heat-treated at 1100 ° C. for 1 hour to obtain a plate thickness of 5.0 mm by hot rolling, and then the surface oxide layer was removed by pickling, followed by cold rolling and 1.0 mm. Thereafter, a solution heat treatment was performed at 1050 ° C., and then a treatment for imparting a vibration damping capacity of 15% cold work was performed.

Comparative Example 5

As Comparative Example 5, a commercially available SUS304 plate having the same thickness as that of the example was used.

Table 1. Shows the composition of each specimen.
Furthermore, the result of having measured the loss coefficient ((eta)) which shows a vibration damping ability, extract | collecting a test piece from this invention example 1- (1) and 1- (2), comparative materials 1, 2, 3, 4 and 5 Is shown in Table 2. The material of the present invention exhibits a good loss factor (η). On the other hand, the comparative materials 1, 2, 3 and 4 have the same rolling and cold working processes, but the loss factor (η) is significantly low and varies depending on the part. Since the comparative material 5 is a commercial product SUS304 as a matter of course, the vibration damping capability is extremely low. This is because, in the case of the comparative material 1, the carbon content is excessively 0.06%. Moreover, in the case of the comparative material 2, since the solid solution N (0.010 wt%) inevitably mixed and dissolved in the steel refining process is not fixed by aluminum, the vibration damping effect between the γ / ε phases is hindered. It is thought that. On the other hand, since all the nitrogen (0.010% by weight) of the material of the present invention is a large inclusion of AlN due to aluminum, the damage of solute nitrogen is eliminated. Further, in the case of the comparative material 3, similarly to the comparative material 2, it is considered that solute nitrogen inhibits the vibration damping ability between the γ / ε phases. The above examples show that the present invention is effective in stabilizing the vibration damping capability.

  Example 2 is an example of the second invention.

Next, a test piece was collected from the material prepared in Example 1, and material properties other than the loss factor (η), that is, tensile test value, hardness, rust resistance (salt spray test), and magnetism were measured. The results are shown in Table 3. Shown in Although the comparative material 3 (patent document 1) is high intensity | strength, it is inferior in rust resistance. Moreover, since the comparative material 4 (patent document 2) is extremely inferior in the salt spray test, it cannot be used for any of the above application parts. Compared with these, the material of the present invention has good SUS304-like rust resistance and is nonmagnetic, and is easily accepted in the industrial field.

  Example 3 is an example of the third invention.

  Composition within the scope of the present invention: carbon 0.02 wt%, manganese 17 wt%, chromium 12 wt%, nickel 3 wt%, aluminum 0.03% wt, nitrogen 0.005 wt%, balance iron balance iron And the composition which consists of an unavoidable impurity was melt | dissolved and casted with the high frequency melting furnace, and 5 kg of ingots were obtained. After surface cutting of the obtained ingot, heat treatment at 1100 ° C. for 1 hour, forming a plate with a thickness of 5.0 mm by hot rolling, removing the oxide layer on the surface by pickling, and then cold rolling After obtaining a 1.0 mm plate, solution heat treatment is performed at 700 ° C., 800 ° C., 900 ° C., 1000 ° C., and 1100 ° C., and then a treatment for imparting 30% cold work vibration damping capability is performed. This was designated as Example 3 of the present invention.

Table 4 shows the crystal grain size after treatment and the surface condition after 30% cold working according to the solution heat treatment temperature. When the solution heat treatment temperature is 1000 ° C. or higher, the crystal grain size after the treatment is abnormally large as 10 μm or more, and as a result, the surface is cracked after cold working and cannot be used thereafter. Become.

  Example 4 is an example of the fourth invention.

Furthermore, regarding the Fe—Mn—Cr—Ni alloy according to the present invention, the relationship between the cold work rate, the loss factor (η), the tensile strength, and the elongation value was obtained by experiments. That is, the Fe—Mn—Cr—Ni alloy according to the present invention was subjected to cold working of 5, 10, 20, 30, 50, 60 and 70%, and the loss factor (η), tensile strength and elongation value were measured. did. The results are shown in Table 5. According to this, at a cold work rate of 5%, both the loss factor (η) and the tensile strength are insufficient. At a cold work rate of 10 to 60%, the loss factor (η), tensile strength and elongation value are all good. At a cold working rate of 70%, the elongation value is extremely poor and the ductility as a material is lost. That is, it is clear that the Fe—Mn—Cr—Ni alloy according to the present invention has excellent material properties that both the loss factor (η) and the tensile strength are improved together with the cold work rate. And the optimal cold work rate can be selected according to a use.

  Example 5 is an example of the fifth invention.

The Fe—Mn—Cr—Ni alloy according to the present invention is subjected to vibration stress of 10% or more and 50% or less of 0.2% proof stress in the tensile test of the alloy by taking advantage of the material properties of high strength and high damping capacity. Table 5 shows an example of application that is processed to be used in Table 5. Shown in That is, as a result of application to bolts and nuts, it was confirmed that the bolts and nuts themselves absorb vibrations, so that they are difficult to loosen. In addition, when applied to a bite shank, it has been confirmed that the cutting efficiency is improved because the cutting edge itself absorbs vibration caused by cutting and the blade edge does not sway. Furthermore, by applying it to the part that absorbs the vibration of the ball screw, a high-speed silent ball screw superior to the conventional product has been realized. Furthermore, when applied to a vibration isolator for a precision instrument or a honeycomb surface plate, it was confirmed that the instrument is effective for vibration isolation of a precision instrument that absorbs a wide range of vibration frequencies. Furthermore, when applied to HDD suspensions, the material itself absorbs vibration, making it lighter, improving read / write accuracy, increasing the rotational speed of the HDD, and greatly improving the unit capacity. did. It was found that when applied to a spring, the material itself absorbs vibration, so that the vibration is quickly settled and the function is improved. In addition, when applied to steel balls, the material itself absorbs vibration, and it was found that low-noise steel balls for bearings can be manufactured. It was also found that the vibration noise generated when applied to an automobile oil tank can be greatly reduced. Furthermore, when applied to automobile engine gaskets, the gas sealing performance at high temperatures has been dramatically improved. Further, when the exhaust gas purification device member is used, the vibration of the exhaust gas purification device is remarkably reduced.
As described above, it was confirmed that the Fe—Mn—Cr—Ni alloy according to the present invention was suitably applied to various fields.

  As is clear from the above description, the Fe—Mn—Cr—Ni alloy according to the present invention not only has high strength and high vibration damping capability, but also has a stable manufacturing process, so that the quality of the material is guaranteed. In addition, it has good characteristics in terms of material strength, rust resistance, and magnetism. Therefore, specific applications of the Fe-Mn-Cr-Ni alloy according to the present invention include bolts and nuts that are less likely to loosen due to the characteristics of having good vibration damping ability, bites and shanks that do not flicker, and high speed. Silent ball screw, anti-vibration table for precision equipment that absorbs vibrations in a wide frequency range, hard disk drive suspension with good seek accuracy, honeycomb surface plate with good vibration absorption efficiency, springs that can quickly absorb vibrations, and steel balls for low noise bearings and It is suitably used for automobile oil pans, engines / gaskets, exhaust gas purification device members, and other damping parts.

The manufacturing process of the Fe-Mn-Cr-Ni alloy with high strength and high vibration damping ability is shown.

Claims (5)

  Carbon 0.05 wt% or less, manganese 13 wt% or more, less than 18 wt%, chromium 9 wt% or more, less than 15 wt%, nickel 0.01 wt% or more, less than 6 wt%, aluminum 0.01 wt% or more Fe-Mn-Cr with high strength and high damping capacity, comprising less than 0.05% by weight, 0.01% by weight or less of nitrogen, balance iron and inevitable impurities, and having an epsilon-martensite phase of 10% or more -Ni alloy.   The high strength and high damping capacity Fe-Mn-Cr-Ni alloy according to claim 1, wherein the tensile strength is 700 MPa or more and 1200 MPa or less, and the loss coefficient (η) is 0.005 or more and 0.10 or less.   Carbon 0.05 wt% or less, manganese 13 wt% or more, less than 18 wt%, chromium 9 wt% or more, less than 15 wt%, nickel 0.01 wt% or more, less than 6 wt%, aluminum 0.01 wt% or more , Less than 0.05% by weight, nitrogen 0.01% by weight or less, melted to a composition consisting of the balance iron and unavoidable impurities, homogenized heat treatment of the cast material, followed by hot working, and further required Or cold-working according to the above, heated at 800 ° C. or more and less than 1000 ° C., then water-cooled or air-cooled to perform solution heat treatment, and further cold-worked as necessary. 2. A method for producing a high-strength, high-damping capacity Fe—Mn—Cr—Ni alloy according to 2.   4. The high processing according to claim 3, wherein the Fe—Mn—Cr—Ni material after the solution heat treatment is processed at a processing rate of 10% or more and 60% or less at a normal temperature or a temperature of 50 ° C. or more and 200 ° C. or less. A method for producing a high-damping capacity Fe-Mn-Cr-Ni alloy.   The high strength and high damping capacity Fe-Mn-Cr-Ni alloy according to claim 1 or 2 is used under a vibration stress of 10% or more and 50% or less of 0.2% proof stress in a tensile test of the alloy. Processed bolts and nuts, cutting tool supports, ball screws, vibration isolation tables, hard disk drive suspensions, honeycomb structures, springs, steel balls, automobile oil tanks, engine gaskets, exhaust gas purification device components, etc. High strength and high damping capacity Fe-Mn-Cr-Ni alloy compacts such as vibration parts.

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