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Iron-based alloy and process for producing the same

a technology of iron-based alloys and fe-based alloys, which is applied in the direction of magnetic materials, magnetic bodies, electrical equipment, etc., can solve the problems of inferior ductility of ni—mn—ga-based materials, temperature control of shape-memory alloys, and poor response, so as to achieve a large reversible strain, high elastic deformation, and displacably controlled

Inactive Publication Date: 2009-07-16
JAPAN SCI & TECH CORP
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  • Summary
  • Abstract
  • Description
  • Claims
  • Application Information

AI Technical Summary

Benefits of technology

The present invention provides an Fe-based ferromagnetic alloy with good ductility that can be magnetically driven by application and removal of a magnetic field gradient. The alloy contains specific amounts of Al, Si, Cr, Ni, Ti, V, Mn, Co, Ni, Cu, Zr, Nb, Mo, Hf, Ta, W, B, C, P, and S. The alloy can also contain specific amounts of one or more additional elements such as B, C, P, and S. The alloy has a large reversible strain and is formed by solution-treating and working the alloy at specific conditions. The alloy has a metal structure with an existing twin crystal generated by working. The technical effects of the invention are improved magnetically driven deformation and ductility of the Fe-based alloy.

Problems solved by technology

However, the shape-memory alloy requires temperature control and further has a poor response since the shape change of the shape-memory alloy in being cooled is rate-controlled by thermal diffusion.
However, the Ni—Mn—Ga based material has inferior ductility, and it is difficult to apply a complicated and precise shape required for machine parts to the Ni—Mn—Ga based alloy.

Method used

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  • Iron-based alloy and process for producing the same
  • Iron-based alloy and process for producing the same
  • Iron-based alloy and process for producing the same

Examples

Experimental program
Comparison scheme
Effect test

example 1

[0040]Fe-based alloys having compositions of Table 1 were melted, cast, hot-rolled and cold-rolled to a plate thickness: 0.5 mm. Further, the Fe-based alloys were solution-treated at 1000° C. for 60 minutes. For alloy designs in Table 1, alloys A1 to A5 are based on an Fe—Al-based alloy; alloys S1 to S4 based on an Fe—Si-based alloy; alloys C1 to C4 based on an Fe—Cr-based alloy; and alloys N1 to N4 based on an Fe—Ni-based alloy. Alloys A5, A6, S5, S6, C5, C6, N5 and N6 are obtained by combining a plurality of fundamental Fe-based alloys.

TABLE 1Prepared Fe-based alloyalloy component, contentalloy(% by mass)No.AlSiCrNiFeA12———balanceA25———balanceA37———balanceA410 ———balanceA553——balanceA65—12—balanceS1—0.5——balanceS2—1.5——balanceS3—3——balanceS4—6——balanceS5—312—balanceS6—3—45balanceC1—— 5—balanceC2——12—balanceC3——18—balanceC4——22—balanceC5——1245balanceC62—12—balanceN1———36balanceN2———40balanceN3———45balanceN4———50balanceN52——45balanceN6—0.51245balance

[0041]Table 2 shows results obtai...

example 2

[0046]Alloys A2, S3, C2 and N3 of Table 1, which were selected as a Fe—Al-based, Fe—Si-based, Fe—Cr-based and Fe—Ni-based alloys, were cold-worked and aging-treated after being solution-treated.

[0047]The relationship between producing conditions and property values is shown in Table 3. In test No. 1, cold rolling was not carried out after being solution-treated, and twin crystals did not exist. Test No. 2 is obtained by applying cold-rolling of 40% to the test No. 1, and the elastic deformation amount was also large. Test No. 3 was rolled at a cold working rate of 80%, and the area ratio of the twin crystal interface and the elastic deformation amount increased with the increase in the working rate. However, the magnetization intensity had no change and magnetic property was well maintained.

[0048]Test Nos. 7 to 12 are aging-treated after being solution-treated and cold-rolled. In the test Nos. 7-8 and 10-11, the area ratio of the twin crystal interface is 0.2 or more, and the suitab...

example 3

[0051]Alloys A3, S2, C3 and N3 of Table 1 respectively have a Fe—Al-based, Fe—Si-based, Fe—Cr-based and Fe—Ni-based fundamental compositions. Various Fe-based alloys were prepared by adding a third component of claim 2 or 4. The Fe-based alloys were cast, hot-rolled and cold-rolled to a plate thickness: 0.5 mm in the same manner as in Example 1 after being melted. The Fe-based alloys were cold-rolled and aging-treated after being solution-treated.

[0052]Table 4 (Fe—Al-based), Table 5 (Fe—Si-based), Table 6 (Fe—Cr-based) and Table 7 (Fe—Ni-based) show results obtained by measuring the elastic deformation amount and magnetization intensity of each of the obtained Fe-based alloys.

[0053]As shown in search results of Tables 4 to 7, each of Fe-based alloys having enhanced magnetism, a corrosion resistance, strength and ductility or the like obtained adding a third element exhibited an area ratio of a twin crystal interface of 0.6 or more. The Fe-based alloy had an elastic deformation amoun...

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Abstract

It is an object of the present invention to provide a ferromagnetic Fe-based alloy having a large reversible strain obtained by application and removal of a magnetic field gradient.The Fe-based alloy contains one or two or more types selected from Al: 0.01 to 11%, Si: 0.01 to 7% and Cr: 0.01 to 26%, or Al: 0.01 to 11%, Si: 0.01 to 7%, Cr: 0.01 to 26% and Ni: 35 to 50%. A twin crystal interface is introduced by working the Fe-based alloy at a working rate: 10% or more. An area ratio of the twin crystal interface to a crystal grain boundary is 0.2 or more. One or two or more types of Ti: 0.01 to 5%, V: 0.01 to 10%, Mn: 0.01 to 5%, Co: 0.01 to 30%, Ni: 0.01 to 10%, Cu: 0.01 to 5%, Zr: 0.01 to 5%, Nb: 0.01 to 5%, Mo: 0.01 to 5%, Hf: 0.01 to 5%, Ta: 0.01 to 5%, W: 0.01 to 5%, B: 0.001 to 1%, C: 0.001 to 1%, P: 0.001 to 1% and S: 0.001 to 1% may be added to the Fe-based alloy if needed.

Description

TECHNICAL FIELD[0001]The present invention relates to a ferromagnetic Fe-based alloy having a large reversible strain obtained by application and removal of a magnetic field gradient, the Fe-based alloy capable of being displaced, and a method for producing the same.BACKGROUND ART[0002]Attentions have been focused on a titanium alloy as a material having a low Young's modulus and exhibiting high elastic deformability. The titanium alloy is used for an artificial tooth root, an artificial bone and a glass frame or the like. For example, it is known that a titanium alloy containing a IVa group or Va group element is a material having a low Young's modulus and exhibiting high elastic deformability (Patent Documents 1 and 2).[0003]Patent Documents 1 and 2 describe the deformation behavior of the titanium alloy to external stress. Examples of external factors which cause a deformation include a temperature and a magnetic field in addition to the stress.[0004]A shape-memory alloy displaca...

Claims

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Application Information

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Patent Type & Authority Applications(United States)
IPC IPC(8): C21D8/00C21D6/00C22C38/00C22C38/18C22C38/08
CPCC21D6/00C21D7/02H01F1/14791C21D10/00C22C38/00C21D8/12C22C38/06H01F1/147C22C38/18
Inventor ISHIDA, KIYOHITOKAINUMA, RYOSUKEOIKAWA, KATUNARISUTOU, YUJIOMORI, TOSHIHIROANDO, KEISUKE
Owner JAPAN SCI & TECH CORP
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