JP2015196838A - PRODUCTION METHOD OF Fe-Ni ALLOY MATERIAL, METHOD OF MANUFACTURING SOFT MAGNETIC COMPONENT, Fe-Ni ALLOY AND SOFT MAGNETIC COMPONENT MATERIAL - Google Patents

Abstract

PROBLEM TO BE SOLVED: To maintain good magnetic properties of a soft magnetic component composed of an Fe-Ni alloy and furthermore to prevent sticking of workpiece and other members to each other during annealing.SOLUTION: A production method of an Fe-Ni alloy material is provided in which: hot forging, hot rolling and cold rolling under prescribed processing conditions are performed on a steel ingot having a prescribed component composition containing Ni:40 to 51 mass%; a cold rolled rolling target material is heated to 800 to 1200°C and is magnetically annealed for 0.15 to 120 min. to obtain a magnetically annealed rolling target material having an average particle diameter of crystal particles of a 25 μm or more; and the magnetically annealed rolling target material is subjected to final cold rolling with a rolling ratio of 0 to 20%.

Description

  The present invention relates to a method for producing an Fe—Ni alloy material used as a soft magnetic material, a method for producing a soft magnetic component using the Fe—Ni alloy material, an Fe—Ni alloy, and a soft magnetic component material.

  Ni: 40 to 51 mass%, balance: Fe and Ni alloy material (so-called PB permalloy) composed of Fe and inevitable impurities is used as a material for soft magnetic parts such as a yoke for a watch, a transformer core, and a magnetic shielding case. It is done.

  Soft magnetic parts are subjected to predetermined pressing and bending processes on Fe-Ni alloy materials obtained through a series of manufacturing processes such as casting, forging, rolling, and annealing, and then magnetic annealing of the workpiece is performed. Manufactured by applying. In this specification, “magnetic annealing” refers to the strain inside the material that promotes recrystallization and grain growth of the material, improves the magnetic properties, and is applied by mechanical processing such as rolling to lower the magnetic properties. It refers to annealing whose main purpose is to be removed by recovery.

  As a conventional method for producing an Fe—Ni alloy material, for example, there is a method described in Patent Document 1. The method described in Patent Document 1 is a method in which the magnetic annealing of the Fe—Ni alloy material is performed in a pre-process such as press working, but the magnetic annealing time is as short as 10 to 65 seconds, and the magnetic annealing is further performed in the post-process. Do not do. This may cause the magnetic properties of the soft magnetic component to be insufficient.

  On the other hand, Patent Document 2 describes a method of performing magnetic annealing of an Fe—Ni alloy material at 1100 ° C. for 3 hours. Patent Document 2 also describes that deoxidation and desulfurization are promoted by adding limestone, alumina, or the like to the molten metal, and magnetic properties are improved by increasing the cleanliness.

  Similarly to Patent Document 2, Patent Document 3 also describes a method of performing magnetic annealing of an Fe—Ni alloy material at 1100 ° C. for 3 hours. Patent Document 3 also describes that Ni segregation is suppressed by homogenizing the slab, thereby improving the magnetic characteristics.

  However, when performing magnetic annealing that also serves to remove distortion of the workpiece after performing processing such as press processing on the Fe—Ni alloy material, magnetic annealing is performed under the processing conditions as in Patent Document 2 and Patent Document 3. Then, the workpiece will be in contact with other members for a long time while being in a high temperature state. In this case, there is a possibility that the workpieces stick to each other, the workpiece and the metal container stick to each other, and thermal deformation due to contact load occurs. When sticking between the workpiece and the other member occurs, it takes time to separate the stuck members and the like, and productivity is lowered.

  In order to avoid this problem, there is a method of performing magnetic annealing by applying a coating for annealing separation to an Fe—Ni alloy material as disclosed in Patent Document 4.

JP 2009-114511 A JP 2002-161328 A JP 2011-68998 A JP-A-4-142705

  However, applying the annealing separation coating to the Fe—Ni alloy material increases the manufacturing cost of the Fe—Ni alloy material, and consequently increases the manufacturing cost of the soft magnetic component.

  In addition, by reducing the magnetic annealing time, it may be possible to suppress the sticking between the workpiece and other members to some extent, but in this case, the magnetic annealing time is shortened, thereby reducing the Fe-Ni alloy. This will reduce the magnetic properties of the material.

  The present invention has been made in view of the above circumstances, and aims to prevent sticking between a workpiece and another member during annealing while maintaining good magnetic properties of the Fe-Ni alloy material. To do.

The present invention for solving the above problems is a method for producing an Fe-Ni alloy material,
Ni: 40-51 mass%,
Ti: 0 to 1.0 mass%,
Cr: 0 to 1.0 mass%,
Co: 0 to 2.0 mass%,
Sn: 0 to 1.0 mass%,
Zn: 0 to 1.0 mass%,
Mg: 0 to 0.10 mass%,
Zr: 0 to 1.0 mass%,
Al: 0 to 1.0 mass%,
Si: 0 to 1.0 mass%,
B: 0 to 0.05 mass%,
Cr: 0 to 1.0 mass%,
Mn: 0 to 2.0 mass%,
V: 0 to 1.0 mass%,
Cu: 0 to 10 mass%,
Mo: 0-10 mass%,
Ca: 0 to 0.10 mass%,
REM (rare earth element): 0 to 0.10 mass%,
S: 0.0035 mass% or less,
O: 0.10 mass% or less,
N: 0.10 mass% or less,
C: 0.10 mass% or less,
P: limited to 0.10 mass% or less,
The rest: hot ingot, hot rolling, and cold rolling are performed on the steel ingot made of Fe under predetermined processing conditions, and the cold-rolled material to be rolled is heated to 800 to 1200 ° C. to 0.15 It is characterized in that magnetic annealing is performed for ˜120 minutes so that the average grain size of the crystal grains of the material to be annealed is 25 μm or more, and then final cold rolling at a rolling rate of 0 to 20% is performed.

  According to the present invention, the magnetic annealing of the alloy material is performed for several minutes before the Fe-Ni alloy material forming step, so that the magnetic annealing after the forming step can be performed under conditions where the processing temperature is low or the processing temperature is high. It is possible to carry out under conditions where the processing time is short. “Molding” refers to processing such as press punching or bending, and “molding step” refers to a step of molding an alloy material for the production of soft magnetic parts. Thereby, sticking with a workpiece and other members can be controlled. In the present invention, by limiting the content of S in the Fe—Ni alloy, the cleanliness of the A-based inclusions in the alloy material can be lowered. Thereby, crystal grain growth is likely to occur, and magnetic characteristics can be improved.

  According to another aspect of the present invention, a soft magnetic component that performs magnetic annealing for 60 to 180 minutes by heating the workpiece to 500 to 1000 ° C. after the Fe-Ni alloy material is subjected to predetermined molding processing. A manufacturing method is provided.

  As another aspect of the present invention, after the Fe-Ni alloy material is subjected to a predetermined molding process, the workpiece is heated to more than 1000 to 1200 ° C and further subjected to magnetic annealing for 1 to 60 minutes. A method of manufacturing a soft magnetic component is also provided.

As another aspect of the present invention,
Ni: 40-51 mass%,
Ti: 0 to 1.0 mass%,
Cr: 0 to 1.0 mass%,
Co: 0 to 2.0 mass%,
Sn: 0 to 1.0 mass%,
Zn: 0 to 1.0 mass%,
Mg: 0 to 0.10 mass%,
Zr: 0 to 1.0 mass%,
Al: 0 to 1.0 mass%,
Si: 0 to 1.0 mass%,
B: 0 to 0.05 mass%,
Cr: 0 to 1.0 mass%,
Mn: 0 to 2.0 mass%,
V: 0 to 1.0 mass%,
Cu: 0 to 10 mass%,
Mo: 0-10 mass%,
Ca: 0 to 0.10 mass%,
REM (rare earth element): 0 to 0.10 mass%,
S: 0.0035 mass% or less O: 0.10 mass% or less,
N: 0.10 mass% or less,
C: 0.10 mass% or less,
P: limited to 0.10 mass% or less,
The balance: Fe—Ni alloy comprising Fe, having an average grain size of 25 μm or more, cleanliness of A-based inclusions of 0.010% or less, and Vickers hardness of 120 to 200 HV is also provided. Is done.

As another aspect of the present invention,
Ni: 40-51 mass%,
Ti: 0 to 1.0 mass%,
Cr: 0 to 1.0 mass%,
Co: 0 to 2.0 mass%,
Sn: 0 to 1.0 mass%,
Zn: 0 to 1.0 mass%,
Mg: 0 to 0.10 mass%,
Zr: 0 to 1.0 mass%,
Al: 0 to 1.0 mass%,
Si: 0 to 1.0 mass%,
B: 0 to 0.05 mass%,
Cr: 0 to 1.0 mass%,
Mn: 0 to 2.0 mass%,
V: 0 to 1.0 mass%,
Cu: 0 to 10 mass%,
Mo: 0-10 mass%,
Ca: 0 to 0.10 mass%,
REM (rare earth element): 0 to 0.10 mass%,
S: 0.0035 mass% or less O: 0.10 mass% or less,
N: 0.10 mass% or less,
C: 0.10 mass% or less,
P: limited to 0.10 mass% or less, balance: Fe,
Magnetic grains having an average grain size of 25 μm or more, a coercive force H _c of 16 A / m or less, an initial permeability μi of 3000 or more, and a maximum permeability μm of 30000 or more in magnetic annealing performed after molding. A soft magnetic component material having properties is also provided.

  ADVANTAGE OF THE INVENTION According to this invention, sticking with the to-be-processed material and other member at the time of annealing can be prevented, maintaining the magnetic characteristic of the soft-magnetic component which consists of Fe-Ni alloys favorably.

  Hereinafter, embodiments of the present invention will be described based on a method for producing an Fe—Ni alloy material.

  First, the Fe—Ni alloy material of this embodiment will be described. The Fe—Ni alloy material of this embodiment is a so-called PB permalloy containing Ni: 40 to 51 mass%.

<Ingredient composition>
In addition to Ni: 40 to 51 mass%, the Fe—Ni alloy material of the present embodiment includes Ti: 0 to 1.0 mass%, Cr: 0 to 1.0 mass%, Co: 0 to 2.0 mass%, and Sn: 0. ~ 1.0 mass%, Zn: 0 to 1.0 mass%, Mg: 0 to 0.10 mass%, Zr: 0 to 1.0 mass%, Al: 0 to 1.0 mass%, Si: 0 to 1.0 mass% , B: 0 to 0.05 mass%, Cr: 0 to 1.0 mass%, Mn: 0 to 2.0 mass%, V: 0 to 1.0 mass%, Cu: 0 to 10 mass%, Mo: 0 to 10 mass% , Ca: 0 to 0.10 mass%, REM (rare earth element): 0 to 0.10 mass% of each element may be contained, and the content of S as an impurity element is 0.0035 mass% ( 35 ppm) or less, O: 0.10 mass% or less, N: 0.10 mass% or less, C: 0.10 mass% or less, and P: 0 to 0.10 mass% or less. In addition, when "content is 0%" in each element, it means that the element does not contain.

  S is a kind of inevitable impurities, but in this embodiment, the content is limited by addition of S remover or slag refining. When the content of S exceeds 0.0035 mass%, during magnetic annealing described later, A-based (Mn-S-based) inclusions that inhibit the growth of crystal grains are likely to be generated, and the magnetic properties of the alloy material are deteriorated. To do.

  Moreover, when the content of S is 0.0035 mass% or less, the cleanliness of the A-based inclusions in the alloy material is 0.010% or less by forging the alloy material described in the manufacturing method described later. Has been. If the cleanliness of the A-based inclusions in the alloy material exceeds 0.010%, the magnetic properties of the alloy material will deteriorate.

  Here, other elements will be described.

  O, N, C, P: contained as an inevitable impurity. Exceeding the specified amount may cause cracking during processing and generation of harmful inclusions that form scratches on the product surface. Preferably, O, N ≦ 0.001 mass%, C, P ≦ 0.02 mass%.

   Si, Mn, Mg, Ca: mainly added with the purpose of fixing deoxidizer or contained S to prevent cracking during hot working, or used as slag during refining, but magnetic properties are mixed It is a small desired element for me. If it is contained in a large amount, it may cause a solid solution and delay the recrystallization speed, or may cause harmful defects such as surface scratches. In addition, A-based (Mn-S-based) inclusions inhibit the recrystallization of the material and as a result, deteriorate the magnetic properties. However, the amount of Mn-S generated depends on the S content, and it is considered that there is almost no influence of the Mn amount. Preferably, Si ≦ 1 mass%, Mn ≦ 1.5 mass%, Mg, Ca ≦ 0.01 mass%.

  Ti, B, Zr, V, REM: May be added to aid deoxidation or adjust material properties. If the amount is small, there is no problem, and if it exceeds the specified amount, cracking during processing may occur. Preferably, Ti ≦ 0.1 mass%, B, Zr, V, REM ≦ 0.05 mass%.

  Sn, Zn: Sometimes added to adjust surface properties such as plating properties. If the amount is small, there is no problem, but if the amount exceeds the specified amount, cracking during processing may occur. Preferably, Sn and Zn ≦ 0.1 mass%.

  Cr, Co: may be added to adjust the surface oxide film and improve weldability and rust resistance. If the amount is small, there is no problem. However, if the amount exceeds the specified amount, discoloration due to surface oxidation and weldability may be impaired. Preferably, Cr ≦ 0.5 mass% and Co ≦ 1 mass%.

  Cu, Mo: May be added for the purpose of controlling magnetic annealing conditions. If the amount exceeds the specified amount, the magnetic properties may be deteriorated. Preferably, Cu ≦ 2 mass% and Mo ≦ 5 mass%.

  Regarding the above, the total amount of elements other than Si, Mn, Cu, and Mo is preferably 2 mass% or less, and more preferably 1 mass% or less. For Si, Mn, Cu, and Mo, it depends on the prescribed amount of each element.

  The balance of the component composition is composed of Fe and inevitable impurities.

<Metallic structure>
In the Fe—Ni alloy of this embodiment, the average grain size of the alloy crystal grains is 25 μm or more. When the average grain size of the crystal grains is less than 25 μm, the magnetic properties of the alloy material cannot be sufficiently obtained. Note that if the average grain size of the crystal grains exceeds 1000 μm, partial softening of the material at the crystal grain boundaries or the like occurs, and the molding process becomes difficult. For this reason, the upper limit of the average grain size of the crystal grains is 1000 μm, and the upper limit of the preferred average grain size is 200 μm, more preferably 150 μm. Moreover, the minimum of a preferable average particle diameter is 30 micrometers, More preferably, it is 40 micrometers.

<Characteristic>
The Vickers hardness of the Fe—Ni alloy of this embodiment is 125 to 200 HV. If it is less than 125 HV, the material strength (hardness) is remarkably lower than that of ordinary PB permalloy, making it difficult to perform molding with the same equipment and processing conditions. If it exceeds 200 HV, the work strain remaining in the alloy material is not sufficiently recovered in the magnetic annealing after the forming process, and as a result, sufficient magnetic properties cannot be obtained. More preferably, it is 160 HV or less.

  The above is the Fe—Ni alloy material according to the present embodiment. Next, a method for manufacturing the Fe—Ni alloy material will be described.

  First, we examined to suppress the S content in the melting raw material, and in addition to this, by removing S by adding S remover or refining slag by vacuum melting, Ni: 40-51 mass% is contained, and also necessary Accordingly, Ti: 0 to 1.0 mass%, Cr: 0 to 1.0 mass%, Co: 0 to 2.0 mass%, Sn: 0 to 1.0 mass%, Zn: 0 to 1.0 mass%, Mg: 0 to 0.10 mass%, Zr: 0 to 1.0 mass%, Al: 0 to 1.0 mass%, Si: 0 to 1.0 mass%, B: 0 to 0.05 mass%, Cr: 0 to 1.0 mass %, Mn: 0 to 2.0 mass%, V: 0 to 1.0 mass%, Cu: 0 to 10 mass%, Mo: 0 to 10 mass%, Ca: 0 to 0.10 mass%, REM (rare earth element): 0 ˜0.10 mass% of each element is contained, S: 0.0035 mass% or less, O: 0.10 mass% or less, N: 0.10 mass% or less, C: 0 10 mass% or less, P: 0~0.10mass% was below the limit, the remainder to produce a steel ingot consisting of Fe. The “steel ingot” in the present specification includes a slab produced by continuous casting or the like.

  Next, hot forging, hot rolling, and cold rolling are performed on the steel ingot under predetermined processing conditions. In addition, the manufacturing method of the Fe-Ni alloy material of this embodiment is the same as the conventional manufacturing method until the below-mentioned magnetic annealing process after preparation of a steel ingot. That is, the above-mentioned “predetermined processing conditions” refers to processing conditions adopted in the conventional manufacturing method.

  For example, a steel ingot having the above component composition is hot forged after heating at 1200 to 1350 ° C. for 1 to 12 hours. By hot forging the steel ingot, A-based inclusions can be reduced. Subsequently, the forged material is hot-rolled at 1000 ° C to 1200 ° C. The thickness of the material to be rolled after hot rolling is reduced to 3 to 30% of the thickness of the steel ingot. Thereafter, cold rolling is performed until a predetermined plate thickness is obtained. In addition, you may implement hot rolling and cold rolling in multiple times, respectively. Further, when cold rolling is performed a plurality of times, annealing for removing work strain may be performed between the cold rolling passes as necessary.

  In the present embodiment, after the cold rolling is completed, magnetic annealing (hereinafter, also referred to as “pre-molding magnetic annealing”) is performed on the cold-rolled material. The pre-molding magnetic annealing in the present embodiment is performed by heating the material to be rolled to 800 to 1200 ° C. and holding the temperature state for 0.15 (9 seconds) to 120 minutes. At this time, if the temperature of the material to be rolled is less than 800 ° C., recrystallization of crystal grains and grain growth become insufficient, and the magnetic properties of the alloy material cannot be sufficiently improved. On the other hand, if the temperature of the material to be rolled exceeds 1200 ° C., it will exceed the operating temperature of a general heat treatment atmosphere annealing furnace of the material to be rolled, and the life of the furnace will be shortened. Incurs a substantial cost increase. For this reason, the annealing temperature at the time of magnetic annealing before shaping | molding was 800-1200 degreeC or more. The minimum of the preferable annealing temperature is 900 degreeC, and the minimum of the more preferable annealing temperature is 1000 degreeC. Moreover, the upper limit of a preferable annealing temperature is 1100 degreeC, and the upper limit of a more preferable annealing temperature is 1050 degreeC.

  Further, if the annealing time in the pre-molding magnetic annealing is less than 0.15 minutes, recrystallization of crystal grains and grain growth do not proceed sufficiently, and the magnetic properties of the alloy material cannot be sufficiently improved. On the other hand, if the annealing time exceeds 120 minutes, the effect of improving the magnetic properties is reduced, so that it is not preferable to perform annealing for a longer time from the viewpoint of productivity. For this reason, the time for magnetic annealing before molding was specified to be 0.15 to 120 minutes. A more preferable annealing time is 1 to 60 minutes, and may be 2 to 20 minutes.

  Subsequently, final cold rolling is performed at a rolling rate of 0 to 20% on the material to be rolled that has been subjected to pre-molding magnetic annealing. This rolling is introduced as necessary in order to prevent burrs and sagging that occur at the time of cutting such as a press by introducing a slight surface compressive stress to the material surface. In this rolling, if the rolling rate exceeds 20%, work hardening of the material to be rolled becomes excessive, and the hardness of the alloy material becomes too high. If the hardness is too high, the magnetic properties will be reduced. “Final cold rolling with a rolling rate of 0%” means that the final cold rolling is not performed. That is, the final cold rolling may be performed as necessary when it is desired to increase the hardness of the material to be rolled after the magnetic annealing before molding. The upper limit of the rolling rate is preferably 15% or less, and more preferably 10% or less.

  The Fe—Ni alloy material in this embodiment is manufactured through the above steps. Since the Fe—Ni alloy material of the present embodiment performs magnetic annealing (magnetic annealing before molding) at the stage of manufacturing the alloy material, the magnetic characteristics have some degree of magnetic properties before processing for manufacturing soft magnetic parts. It is in an improved state.

  For this reason, in the magnetic annealing performed after the molding process (hereinafter also referred to as “post-molding magnetic annealing”), annealing is performed at a high temperature for a long time so as to improve the magnetic properties at once like the conventional post-molding magnetic annealing. It is not necessary. That is, the annealing process can be performed in a state where the temperature of the workpiece is low. Even when the temperature of the material to be rolled is high, the annealing time can be shortened because the magnetic properties have already been improved to some extent. This prevents the workpiece from coming into contact with other members for a long time in a high temperature state. Thereby, sticking with a workpiece and other members can be controlled.

  Moreover, since the content of S contained in the alloy material is limited to be low, the Fe—Ni alloy material according to this embodiment enhances the effect of reducing the cleanliness of the A-based compound during hot forging. It becomes possible. For this reason, crystal grain growth is likely to occur during magnetic annealing, and the improvement of the magnetic properties of the alloy material can be promoted.

  In addition, when producing soft magnetic parts such as a timepiece yoke and a transformer core using the Fe—Ni alloy material of the present embodiment, a predetermined process such as pressing or bending is performed according to the parts to be produced. The molding process is performed. Since the molding method is the same as the conventional method, the description is omitted in this specification.

  And as above-mentioned, the post-molding magnetic annealing is implemented with respect to the to-be-processed material to which the predetermined shaping | molding process was given. Thereby, a material for soft magnetic component manufacture (soft magnetic component material) is produced. In addition, the preferable annealing temperature of post-molding magnetic annealing is 500-1000 degreeC, More preferably, it is 700-950 degreeC, It is more preferable that the preferable annealing time at this time is 60-180 minutes, Furthermore, it is 60-120 minutes. . Also, the annealing temperature may be more than 1000 to 1200 ° C, more preferably 1050 to 1150 ° C, and the preferable annealing time in this case is 5 to 60 minutes, more preferably 10 to 40 minutes.

  Then, a soft magnetic component is manufactured by a conventional method using the soft magnetic component material.

  As mentioned above, although preferred embodiment of this invention was described, this invention is not limited to this example. It is obvious for those skilled in the art that various changes or modifications can be conceived within the scope of the technical idea described in the claims. It is understood that it belongs to.

  The Fe—Ni alloy material according to the present invention was manufactured and the characteristics of the alloy material were evaluated. The manufacturing method of the Fe—Ni alloy material is as follows.

  First, in a 5 ton melting furnace, 45.0-45.3 mass% of Ni is contained, S is limited to the content shown in Table 1, and the remainder is Fe and several 5-ton steel ingots composed of the components contained in Table 1 It was made. Test materials of Test Nos. 1 to 31 cut out to a predetermined size from these steel ingots are produced. Each specimen was heated to the forging temperature shown in Table 1 for 5 hours, and each heated specimen was stretched by hot forging until the cross-sectional area became 30% (500 mm × 500 mm to 200 mm × 400 mm). Thereafter, the surface oxide layer was removed by cutting. In addition, the component composition of each test material was identified by performing ICP analysis with respect to the Fe-Ni alloy material manufactured through the following processes.

  Subsequently, each of the heated specimens was hot-rolled so that the hot rolling rate was 90%, and wound into a coil shape. After this coil was cooled to room temperature, cold rolling was performed on each plate-shaped specimen drawn from the coil until the plate thickness became 2.0 mm. Thereafter, in the continuous annealing furnace in which the inside of the furnace was in a hydrogen atmosphere, each of the cold-rolled specimens was annealed at 1040 ° C. for 3 minutes to remove processing strain.

  After annealing, each sample material was further cold rolled until a desired plate thickness was obtained. Thereafter, annealing was performed again in a continuous annealing furnace having a hydrogen atmosphere in the furnace. The annealing performed here was magnetic annealing (magnetic annealing before molding), the annealing temperature was 1040 ° C., and the annealing time was performed under the conditions shown in Table 1. Subsequently, among the test materials subjected to magnetic annealing, some of the test materials were subjected to final cold rolling at the rolling rates shown in Table 1. By the final cold rolling, each specimen is rolled to a plate thickness of 0.5 mm. In addition, about the test material which does not implement final cold rolling, it is in the state rolled to 0.5 mm in the cold rolling process just before magnetic annealing before shaping | molding.

  The Fe-Ni alloy material of test No. 1-31 is manufactured through the above process. Here, the average grain size of the crystal grains of each alloy material was measured. The average particle size was measured using the cutting method in JIS H 0501. Moreover, the Vickers hardness of each alloy material was also measured. The Vickers hardness was measured according to JIS G 0255 with a test load of 500 g.

  Further, the cleanliness of the A-based inclusions of each alloy material was measured by a method based on JIS G 0555. Further, a sample of 100 mm in the rolling direction and 10 mm in the width direction of each alloy material was collected, one surface was uniformly etched stepwise, and the thickness of the plate and the generated warp were measured to measure the surface stress. These measurement results are shown in Table 2. As for the surface stress shown in Table 2, a positive value indicates a compressive stress, and a negative value indicates a tensile stress.

  Subsequently, each alloy material after the final rolling (alloy material after magnetic annealing in the case where the final rolling is not performed) is pressed to measure four magnetic properties per alloy material. An O-ring (inner diameter 33 mmφ, outer diameter 45 mmφ) was produced. Further, for some alloy materials, each O-ring was subjected to 90 ° bending with R = 1.0 mm by JIS Z 4428 V block method, and then returned to flatness with a press sandwiched between flat plates for correction. Note that “◯” attached to the item “Molding method” in Table 1 means that a predetermined molding process (press, bending) has been performed.

  After molding, four O-rings are stacked and placed in a case to produce a measurement sample A for measuring magnetic properties. Subsequently, the DC magnetic characteristics (coercivity, permeability) of each measurement sample A were measured using a DC magnetic characteristic measuring apparatus. The measuring method was based on JIS C 2531 DC magnetic property test. The measurement results are shown in Table 2.

Thereafter, post-molding magnetic annealing was performed on each O-ring. The post-molding magnetic annealing is performed by heating each O-ring to the annealing temperature shown in Table 2 in the continuous annealing furnace in which the inside of the furnace is in a hydrogen atmosphere, and maintaining that temperature for the time shown in Table 2. Then, four O-rings that have been subjected to magnetic annealing after molding are again laminated and placed in a case, thereby producing a measurement sample B for measuring magnetic properties. Subsequently, the DC magnetic characteristics (coercivity, permeability) of each measurement sample B were measured using a DC magnetic characteristic measuring apparatus. The measurement results are shown in Table 1. The soft magnetic component material preferably has magnetic properties such that the coercive force _Hc is 16 A / m or less, the initial permeability μi is 3000 or more, and the maximum permeability μm is 30000 or more.

  As shown in Table 2, the magnetic properties of test samples Nos. 1 to 25 satisfying the component composition and processing conditions defined in the present invention were good. Further, at the time of the magnetic annealing after the molding process, the crystal grain size was in the range of 32 to 145 μm measured after the magnetic annealing before molding processing, and there was no problem that the O-rings adhered to each other.

  On the other hand, in the measurement sample of test No. 27, the magnetic annealing time before molding of the alloy material was 0.1 minutes (less than 0.15 minutes), so the average grain size of the alloy material crystal grains was 7 μm (less than 25 μm). ) And magnetic properties were low. Moreover, in the measurement samples of Test Nos. 26 and 29, the S content in the alloy exceeded 0.0035 mass% at 0.0045 mass% and 0.0040 mass%, respectively. It is had. As a result, the magnetic properties of the measurement sample were lowered. Moreover, in the measurement sample of test No. 28, since the rolling rate in the final cold rolling exceeded 20%, the hardness of the alloy material exceeded 200 HV, and as a result, the magnetic properties of the measurement sample were lowered. .

  In Test No. 30, the pre-molding magnetic annealing temperature was lower than the predetermined value, and sufficient heating was not performed. Therefore, even if the post-molding magnetic annealing was performed, the magnetic characteristics did not improve.

  In Test No. 31, magnetic post-molding annealing was performed at a high temperature (1100 ° C.) for a long time (120 minutes). That is, the post-molding magnetic annealing in Test No. 31 is an annealing that improves the magnetic properties at once after the molding process, and is a magnetic annealing using a conventional method. As shown in Table 2, the magnetic properties of the measurement sample of Test No. 31 are good, but the surface of each O-ring constituting this measurement sample is subjected to sticking prevention treatment such as application of alumina powder. . That is, when an alloy material is manufactured under the manufacturing conditions as in Test No. 31, the magnetic characteristics are good, but the cost increases as the sticking prevention treatment is performed.

  On the other hand, the alloy material manufactured under the same conditions as in Test No. 31 without performing the sticking prevention treatment causes remarkable peeling between the O-rings during magnetic annealing after molding, and cannot be used for measurement of magnetic properties. It has become a state.

The present invention can be applied to the manufacture of an Fe—Ni alloy material used as a soft magnetic material.

Claims (5)

A method for producing an Fe-Ni alloy material,
Ni: 40-51 mass%,
Ti: 0 to 1.0 mass%,
Cr: 0 to 1.0 mass%,
Co: 0 to 2.0 mass%,
Sn: 0 to 1.0 mass%,
Zn: 0 to 1.0 mass%,
Mg: 0 to 0.10 mass%,
Zr: 0 to 1.0 mass%,
Al: 0 to 1.0 mass%,
Si: 0 to 1.0 mass%,
B: 0 to 0.05 mass%,
Cr: 0 to 1.0 mass%,
Mn: 0 to 2.0 mass%,
V: 0 to 1.0 mass%,
Cu: 0 to 10 mass%,
Mo: 0-10 mass%,
Ca: 0 to 0.10 mass%,
REM (rare earth element): 0 to 0.10 mass%,
S: 0.0035 mass% or less,
O: 0.10 mass% or less,
N: 0.10 mass% or less,
C: 0.10 mass% or less,
P: limited to 0.10 mass% or less,
The rest: hot ingot, hot rolling, and cold rolling are performed on the steel ingot made of Fe under predetermined processing conditions, and the cold-rolled material to be rolled is heated to 800 to 1200 ° C. to 0.15 A method for producing an Fe—Ni alloy material, in which magnetic annealing is performed for 120 minutes so that the average grain size of crystal grains of the material to be annealed is 25 μm or more, and then final cold rolling is performed at a rolling rate of 0 to 20% . After a predetermined molding process is performed on the Fe—Ni alloy material according to claim 1,
A method for producing a soft magnetic component, comprising heating a workpiece to 500 to 1000 ° C. and further performing magnetic annealing for 60 to 180 minutes. After a predetermined molding process is performed on the Fe—Ni alloy material according to claim 1,
A method for producing a soft magnetic component, comprising heating a workpiece to over 1000 to 1200 ° C. and further performing magnetic annealing for 5 to 60 minutes. Ni: 40-51 mass%,
Ti: 0 to 1.0 mass%,
Cr: 0 to 1.0 mass%,
Co: 0 to 2.0 mass%,
Sn: 0 to 1.0 mass%,
Zn: 0 to 1.0 mass%,
Mg: 0 to 0.10 mass%,
Zr: 0 to 1.0 mass%,
Al: 0 to 1.0 mass%,
Si: 0 to 1.0 mass%,
B: 0 to 0.05 mass%,
Cr: 0 to 1.0 mass%,
Mn: 0 to 2.0 mass%,
V: 0 to 1.0 mass%,
Cu: 0 to 10 mass%,
Mo: 0-10 mass%,
Ca: 0 to 0.10 mass%,
REM (rare earth element): 0 to 0.10 mass%,
S: 0.0035 mass% or less O: 0.10 mass% or less,
N: 0.10 mass% or less,
C: 0.10 mass% or less,
P: limited to 0.10 mass% or less,
The balance: Fe-Ni alloy made of Fe, having an average grain size of 25 μm or more, a cleanliness of A-based inclusions of 0.010% or less, and a Vickers hardness of 120 to 200 HV. Ni: 40-51 mass%,
Ti: 0 to 1.0 mass%,
Cr: 0 to 1.0 mass%,
Co: 0 to 2.0 mass%,
Sn: 0 to 1.0 mass%,
Zn: 0 to 1.0 mass%,
Mg: 0 to 0.10 mass%,
Zr: 0 to 1.0 mass%,
Al: 0 to 1.0 mass%,
Si: 0 to 1.0 mass%,
B: 0 to 0.05 mass%,
Cr: 0 to 1.0 mass%,
Mn: 0 to 2.0 mass%,
V: 0 to 1.0 mass%,
Cu: 0 to 10 mass%,
Mo: 0-10 mass%,
Ca: 0 to 0.10 mass%,
REM (rare earth element): 0 to 0.10 mass%,
S: 0.0035 mass% or less O: 0.10 mass% or less,
N: 0.10 mass% or less,
C: 0.10 mass% or less,
P: limited to 0.10 mass% or less, balance: Fe,
Magnetic grains having an average grain size of 25 μm or more, a coercive force H _c of 16 A / m or less, an initial permeability μi of 3000 or more, and a maximum permeability μm of 30000 or more in magnetic annealing performed after molding. Soft magnetic component material with properties.