Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D7/00—Modifying the physical properties of iron or steel by deformation
  • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
  • H01F1/147—Alloys characterised by their composition
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
  • H01F1/147—Alloys characterised by their composition
  • H01F1/14766—Fe-Si based alloys
  • H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust

Definitions

• the present invention relates to a ferromagnetic Fe-based alloy capable of controlling displacement by obtaining a large reversible strain by applying and removing a magnetic field gradient, and a method for producing the same.
• Titanium alloys are attracting attention as a material having a low Young's modulus and a high elastic deformability, and are used for artificial tooth roots, artificial bones, spectacle frames, and the like.
• titanium alloys containing IVa and Va elements are known to be low elastic modulus materials with low Young's modulus! (Patent Documents 1 and 2).
• Patent Documents 1 and 2 describe the deformation behavior of titanium alloys with respect to external stress. External factors that cause deformation include temperature, magnetic field, and the like in addition to stress.
• Shape memory alloys are known for temperature-based displacement control, and dimensional changes on the order of several percent have been obtained.
• the shape memory effect is a phenomenon in which the original shape is recovered by utilizing the martensite reverse transformation that occurs when a deformed material is heated to a certain temperature or higher.
• the force that can be used as a heat-driven actuator Temperature control is required.
• the shape change during cooling is controlled by thermal diffusion, resulting in poor responsiveness!
• Ferromagnetic shape memory alloys are also attracting attention as activator materials!
• a dimensional change of several percent over conventional magnetostrictive materials can be obtained by applying an external magnetic field, and the low responsiveness that is a drawback of heat-driven shape memory alloys is also eliminated.
• the ferromagnetic shape memory alloy for example, there is a Ni—Mn—Ga system, and an actuator material that causes a shape change by applying a magnetic field is known (Patent Document 3).
• Ni-Mn-Ga-based materials are inferior in ductility, and it is difficult to give complex and precise shapes required for machine parts.
• Patent Document 1 Japanese Patent Application Laid-Open No. 2002-332531
• Patent Document 2 Japanese Patent Laid-Open No. 2002-249836
• Patent Document 3 US Patent 5,958,154 Disclosure of the invention
• the present invention is based on force and knowledge, and in a component system in which an appropriate amount of one or more of Al, Si, Cr, Ni is added, a large reversible strain is obtained by removing the magnetic field gradient, and ductility is achieved.
• the objective is to provide a good Fe-based ferromagnetic alloy.
• Fe-based alloy of the present invention A1: 0.01 ⁇ ; 11 mass 0/0, Si:! 0.0 ; ⁇ 7 mass 0/0, Cr: 0.01 ⁇ 26 wt% of one or comprise two or more Yes.
• Fe base alloy of the present invention ⁇ 1: 0 ⁇ 01 ⁇ ; 11 wt%, Si:! 0.0; ⁇ 7 wt%, Ji 0.0; ⁇ 26 mass 0/0, Ni:! 35 -50 mass% of one kind or two or more kinds can be included.
• This Fe-based alloy is ferromagnetic at least at room temperature, and there exist deformation twins generated by processing.
• twin is the ratio of the area of the twin interface to the grain boundary area (hereinafter simply referred to as “twin”).
• the area ratio of the crystal interface is adjusted to 0.2 or more.
• the metal structure in which twins exist is processed after a solution treatment of Fe-based alloy with a prescribed composition at 600 to 1350 ° C. Rate: Formed by processing at 10% or more, and may be further aged at 200 to 800 ° C.
• the inventors of the present invention added various alloying elements to Fe, which is a ferromagnetic element, for the purpose of a material capable of obtaining a large reversible strain by removing the magnetic field gradient and removing the magnetic field gradient.
• Fe which is a ferromagnetic element
• the relationship between the processing rate and the amount of elastic deformation and magnetic properties was investigated.
• a Fe-based alloy containing appropriate amounts of Al, Si, Cr, and Ni can produce a ferromagnetic highly elastic deformable alloy with large reversible strain and high ductility due to the removal of the magnetic field gradient. did it.
• a Fe is a ferromagnetic element having a large magnetic moment, force S, and pure Fe causes plastic deformation immediately and has a small amount of elastic deformation.
• the addition of Al, Si, Cr, Ni, etc. to Fe increases the elastic deformation while exhibiting high magnetic properties. We were able to confirm that it was improved.
• a displacement control element with a magnetic field gradient it is preferable to show a strong magnetizing ability with respect to a relatively low magnetic field.
• T 0.5 Tesla
• the elastic limit strain of annealed metallic materials such as Fe is normally about 0.3%. It is found that the yield stress and elastic limit increase with increasing hardness and tensile strength. It was.
• the Fe alloy of the present invention for example, a strain of 0.4% or more exceeding the normal elastic strain amount is recovered for a bending deformation of 1%.
• Fig. 1 summarizes the relationship between the strength of magnetization to an external magnetic field of 0.5T and the amount of elastic strain to a bending deformation of 1%. All the alloys of the present invention have a magnetization strength of lOOem u / g or more. 0. Indicates elastic deformation of 4% or more. Such properties can be applied over a wide temperature range from liquid nitrogen temperature (1196 ° C) to 400 ° C.
• the Fe alloy of the present invention has a force S that exhibits a large amount of elastic strain with a relatively small Young's modulus, and the respective factors include the ⁇ effect and the reversible movement of twins.
• Young's modulus is a physical property value related to the cohesive force between atoms, and is considered difficult to control by processing or heat treatment.
• a ferromagnetic material has a ⁇ E effect that lowers the Young's modulus due to the rotation of the magnetic moment when stress is applied.
• deformation twins present in a large amount in the processed structure reversibly move with respect to deformation and unloading after deformation.
• the reversible movement phenomenon of twins shows a greater amount of elastic deformation than materials without twins.
• a large amount of elastic strain was obtained, and the abundance of twins was determined by measuring the length of the twin interface and the length of the crystal grain boundary based on the metal structure observed with an optical microscope. It can be expressed as an area ratio of the interface.
• the difference between the high elastic deformation obtained in the present invention and the superelasticity of the shape memory alloy will be described.
• the crystallographic orientation relationship between the two regions at the boundary of the twin interface becomes a twin crystal relationship by processing, whereas in superelasticity, the martensite is transformed from the parent phase by stress. Stress-induced martensitic transformation occurs with a change in crystal structure to the phase. In this respect, there is a clear difference between the two.
• Fe-based alloy of the present invention A1: 0. 01 ⁇ ; 11 wt%, Si:! 0. 0; ⁇ 7 wt%, Cr: 0. 01 ⁇ 26 wt 0/0 or A1,: 0 . 01; 11 mass 0/0, Si:! 0. 0; ⁇ 7 mass 0/0, Cr: 0. 01- 26 wt%, Ni: 35 to 50 over selected from the mass% species or two species It is based on Fe alloy including the above.
• Al, Si, Cr, and Ni have the effect of increasing the magnetic permeability by increasing the amount of elastic deformation after cold working while having high magnetization strength. Such an effect becomes prominent when 0.01% by mass or more of Al, Si or Cr is added. However, excessive addition causes significant deterioration of workability and magnetic properties.
• the upper limit was 8:11 mass%, 31: 7 mass%, and the same: 26 mass%.
• Ni has the effect of increasing the amount of elastic deformation after cold working while having a high magnetization strength when added in an amount of 35% by mass or more. However, excessive addition causes remarkable deterioration of workability and magnetic properties, so Ni: 50 mass% was made the upper limit.
• Ti, V, Zr, Nb, Mo, Hf, Ta, and W are effective components for forming carbides, sulfides, etc. to refine crystal grains and increasing toughness.
• Mn is a component that is effective in improving the machinability by generating sulfides.However, excessive addition causes a significant deterioration in magnetic properties, so when adding Mn: 0. Select content in the range of 0;! To 5 mass%.
• Cu is an effective component for improving the weather resistance. Excessive addition causes significant deterioration of magnetic properties! / When it is added, Cu: 0.0; Select content in the range of 5 to 5% by mass. To do.
• Co is a force that is an effective component for raising the Curie temperature, and excessive addition causes deterioration of ductility. Therefore, when adding Co, the content should be selected in the range of Co: 0.0; To do.
• Ni is an effective component for improving the corrosion resistance even if it is less than 35% by mass, so it can be added as an optional component within a range that does not cause significant deterioration or deterioration of the magnetic properties. In this case, it is preferable to select the content within the range of Ni: 0.01 to 10% by mass.
• B, C, and P are force S, which is an effective component for grain refinement, and excessive addition leads to significant deterioration of ductility. Therefore, when adding B, C, and P, select the content in the range of ⁇ : 0 ⁇ 001 ⁇ ;! Mass%, C: 0.001 ⁇ ;! Mass%, P: 0.001 ⁇ ;! Mass% .
• S is a force S that is an effective component for improving machinability, and excessive addition causes deterioration of workability. Therefore, when adding S, the content is selected in the range of S: 0.001 ⁇ ;
• the Fe-based alloy After melting the Fe-based alloy adjusted to a predetermined composition, it is formed into a plate, wire, tube, or the like having a target size by cold rolling, drawing, or the like through forging, forging, hot rolling, and the like.
• Cold-worked Fe-based alloy at a temperature of 600 ⁇ ;
• the material introduced in the process up to processing is removed to homogenize the material.
• the solution temperature should be 600 ° C or higher because it requires the recrystallization temperature or higher, and it must be sufficiently below the melting temperature (specifically, 1350 ° C or lower), preferably 700 to 1100 °. Set to C range.
• the solution time is 0.1 hour or more because diffusion for recrystallization or solution is necessary, and 6 hours or less is necessary to prevent significant oxidation of the material, preferably 0.2 hours to Set to a range of 2 hours.
• the solution-treated Fe-based alloy may be heat-treated at 200 to 600 ° C as necessary.
• This heat treatment has the effect of tempering hard and brittle martensite. A temperature of 200 ° C or higher is required to obtain this effect. At temperatures exceeding 600 ° C, martensite transformation may occur again during cooling, so the temperature is set to 600 ° C or lower.
• This heat treatment time is 0.01 hours or more because diffusion necessary for tempering is necessary, and heat treatment for a long time requires 24 hours or less to reduce the elastic deformability, and is preferably 0. It is set in the range of 1 hour to 4 hours.
• the solution-treated Fe-based alloy is subjected to processing such as rolling, forging, bending and drawing at room temperature or at a temperature of 700 ° C or lower. Processing at room temperature or below 700 ° C is not preferable for hot working that may cause dynamic recrystallization, which is effective for increasing the number of twins and increasing the elastic range. Considering the fact that processing in the temperature range of 0.6T (T: melting point) or higher is defined as hot processing, the processing temperature should be set to 0.6T or less, specifically 700 ° C or less.
• the processing rate requires a processing rate of 10% or more because the area of the twin interface is 0.2 or more of the grain boundary area, and 95% to avoid a heavy burden on the equipment. It is necessary to do the following.
• twins The influence of twins on the improvement of elastic deformability becomes significant when the area of the twin interface is set to a ratio of 0.2 or more with respect to the grain boundary area in the entire metal structure.
• a piston-type pump can be cited.
• the principle of a piston-type pump using a magnetically driven actuator is that the volume of a chamber used for feeding a fluid, usually a liquid, changes due to a magnetic field gradient induced shape change of the actuator element.
• the movement of the piston is generated by a wide range of shape changes in the actuator element.
• the magnetic field generation source can be installed outside the chamber.
• A1 to A5 are Fe-A1 series
• S1 to S4 are Fe-Si series
• C1 to C4 are Fe-Cr series
• N1 to N4 are Fe-Ni series
• A5, A6, S5, S6, C5, C6, N5, and N6 are alloy designs that combine multiple basic systems.
• Table 2 shows the results of investigating the amount of elastic deformation and the strength of magnetization at room temperature when each Fe alloy after solution treatment was cold-rolled at 40% at room temperature.
• the amount of inertial deformation was defined as the amount of geometric strain that was unloaded after a 1% bending strain was applied in a three-point bending test and then returned.
• the magnetization strength was the magnetization strength at 0.5T when a magnetic field was applied using a vibrating sample magnetometer.
• the area ratio of the twin interface was determined based on the average value of the grain boundary and twin interface obtained from the optical micrographs of 5 fields of view.
• the area ratio of the twin interface is 0.6 or more in any of the alloy systems of Fe-Al, Fe-Si, Fe-Cr, and Fe-Ni.
• the area ratio of the metal tended to increase with increasing amounts of Al, Si, Cr, and Ni.
• the amount of elastic deformation also tends to increase as the area ratio of the twin interface increases, and as shown in the response curve of alloy A2 (Fig. 3), unloading is applied for 1% strain application. Sometimes it shows an elastic deformation of 0.55%. With other alloys, an inertia deformation amount of 0.4% or more was obtained. Another characteristic is that it is more linear than super-elastic materials.
• the strength of magnetization is a force that decreases with the increase of the additive element. In any system, the strength of magnetization is as high as lOOemu / g or more.
• Comparative Example Ol (Fe) and Comparative Example 0 2 (Fe—Co) although having strong magnetism, have few twins and have a lower elastic deformation than the present invention. It was. Comparative Example 03 (SUS316U shows a high twin interface ratio and elastic deformation, but the magnetization strength at 0.5 T is almost zero.
• Table 2 the area ratio of the interface of the cold, ⁇ shape amount, orchid ⁇ of (cold ⁇ 3 ⁇ 4 ⁇ ⁇ rate: 40%)
• Example 2 [0030] Select A2, S3, C2, and N3 in Table 1 as Fe-Al, Fe-Si, Fe-Cr, and Fe-Ni alloys, and perform cold working and aging treatment after solution treatment. did.
• Table 3 shows the relationship between manufacturing conditions and physical properties.
• test No. 1 cold rolling was not performed after solution treatment, and twins were not present.
• Test No. 2 was obtained by applying 40% cold rolling to Test No. 1, and the amount of elastic deformation was also increasing.
• Test No. 3 was rolled at a cold work rate of 80%. As the work rate increased, the area ratio of the twin interface and the amount of elastic deformation increased, but there was no change in the strength of magnetization. Good magnetic properties are maintained!
• Test Nos. 7 to 12 aging treatment was performed after solution treatment and cold rolling.
• test Nos. 7-8, 10-; 11 the area ratio of the twin interface was 0.2 or more, and each of the test Nos. 9 and 12 had a high aging temperature. Therefore, the material was annealed, and the amount of elastic deformation was decreasing. In any case, the magnetic properties were good.
• Test Nos. 4 to 6 the solution temperature was changed. In Test Nos. 4 and 5, the area ratio, the amount of elastic deformation, and the strength of magnetization were good in the twin interface. In Test No. 6, because the solution temperature was high, the liquid phase appeared and partially melted. Oops.
• A3, S2, C3, and N3 in Table 1 have a basic composition of Fe-Al, Fe-Si, Fe-Cr, and Fe-Ni, respectively, and the third component of claim 2 or claim 4
• Various Fe-based alloys were prepared by adding. After melting, it was forged and hot-rolled in the same manner as in Example 1 and cold-rolled to a sheet thickness of 0.5 mm. After the solution treatment, cold-rolling and aging treatment were performed.
• Table 4 (Fe—A1 system), Table 5 (Fe—Si system), Table 6 (Fe—Cr system), Table 7 ( Fe-Ni system).
• the area ratio of the twin interface, the amount of elastic deformation, and the strength of magnetization at temperatures of 50 ° C, 25 ° C, 100 ° C, and 200 ° C were determined.
• the amount of elastic deformation is the amount of shape strain that is unloaded after applying a strain amount of 1% in a tensile test at each temperature and then returns.
• the area ratio of the twin interface and the strength of magnetization are In the same manner as in Example 1, it was obtained. [0040]
• the area ratio of the twin interface and the amount of elastic deformation did not depend much on changes in the test temperature, and remained large even at 200 ° C.
• the deformation stress varies greatly with temperature.
• the apparent temperature dependence of the yield stress is about 5 MPa / ° C.
• the change in stress with temperature is about 0.5 MPa / ° C, which is about one-tenth of that of Ti-Ni alloys. Therefore, it is also suitable for use in a wide temperature range from below room temperature to high temperature. Also, since the Curie temperature was sufficiently high, it showed a high magnetization strength even at 200 ° C.
• A2 and S3 in Table 1 and Ol (Fe) as a comparative example were selected, and after forging and hot rolling, the sheet thickness was 0.
• the obtained Fe-based alloy was given a magnetic field gradient in an electromagnet coil, an initial displacement of 2.8 mm, and then the amount of elastic deformation and the recovery rate when the magnetic field was removed were determined.
• the recovery rate (%) is defined by the formula: (elastic deformation / initial displacement) X 100.
• FIG.2 Micrograph of Fe-5 mass% A1 alloy with a metal structure in which deformation twins are dispersed

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Mechanical Engineering (AREA)
• Organic Chemistry (AREA)
• Metallurgy (AREA)
• Materials Engineering (AREA)
• Physics & Mathematics (AREA)
• Crystallography & Structural Chemistry (AREA)
• Thermal Sciences (AREA)
• Electromagnetism (AREA)
• Power Engineering (AREA)
• Dispersion Chemistry (AREA)
• Manufacturing & Machinery (AREA)
• Soft Magnetic Materials (AREA)
• Hard Magnetic Materials (AREA)

Priority Applications (3)

Applications Claiming Priority (2)

Related Child Applications (1)

Publications (1)

Family

ID=39106819

Family Applications (1)

Country Status (5)

Cited By (1)

Families Citing this family (26)

Citations (10)

Family Cites Families (9)

• 2007
  • 2007-08-22 WO PCT/JP2007/066284 patent/WO2008023734A1/ja active Search and Examination
  • 2007-08-22 JP JP2008530943A patent/JP5215855B2/ja not_active Expired - Fee Related
  • 2007-08-22 EP EP07792874.5A patent/EP2055797A4/de not_active Withdrawn
  • 2007-08-22 KR KR1020097003467A patent/KR20090038016A/ko not_active Application Discontinuation
• 2009
  • 2009-02-20 US US12/389,971 patent/US20090178739A1/en not_active Abandoned

Patent Citations (10)

Non-Patent Citations (1)

Also Published As

Similar Documents

Legal Events