Fe-Co alloy rods

Abstract

Provided is a Fe-Co-based alloy rod material which can achieve excellent magnetic properties reliably.　The Fe-Co-based alloy rod material contains crystal grains having a GOS (Grain Orientation Spread) value of 0.5° or more at an area ratio of more than 80%, in which the difference between the area ratio of crystal grains having a GOS value of 0.5° or more as observed in a cross-sectional surface taken in a direction perpendicular to the axis of the rod material and the area ratio of crystal grains having a GOS value of 0.5° or more as observed in a cross-sectional surface taken in a direction of the axis of the rod material falls within 10%. Preferably, the average crystal grain size number is 6.0 to 8.5 inclusive.

Description

Technical Field

[0001] The present invention relates to Fe-Co alloy bars.

Background Art

[0002] Bars of Fe-Co alloys typified by Permender (Permendur), known as alloys having excellent magnetic properties, are used in various products such as sensors, cylindrical magnetic shields, solenoid valves, and magnetic cores. As a method for manufacturing this Fe-Co alloy bar, for example, in Patent Document 1, after heating an ingot to 1000°C to 1100°C, hot working is performed into a billet of about φ90 mm, removal of surface scratches and the like is performed with a lathe, and after heating to 1000°C to 1100°C, a material (bar) hot-rolled to about φ6 to φ9 mm is produced.

Prior Art Documents

Patent Documents

[0003]

Patent Document 1

Summary of the Invention

Problems to be Solved by the Invention

[0004] With the high performance of the above-described products, further improvement in the magnetic properties of the material is required. Therefore, an object of the present invention is to provide an Fe-Co alloy bar capable of stably obtaining excellent magnetic properties.

Means for Solving the Problems

[0005] The present invention has been made in view of the above-mentioned problems. Specifically, the present invention is an Fe-Co alloy rod in which more than 80% of the area ratio of crystal grains exhibiting a GOS value (Grain Orientation Spread) of 0.5° or higher is present, and the difference between the area ratio of crystal grains exhibiting a GOS value of 0.5° or higher observed in a cross section perpendicular to the axis of the rod and the area ratio of crystal grains exhibiting a GOS value of 0.5° or higher observed in an axial cross section of the rod is within 10%. Preferably, the average grain size number is 6.0 or higher and 8.5 or lower. [Effects of the Invention]

[0006] According to the present invention, Fe-Co alloy rods with excellent magnetic properties can be reliably obtained. [Modes for carrying out the invention]

[0007] Embodiments of the present invention are described below. The Fe-Co alloy rod of the present invention is a straight rod with a cross-sectional shape including circular (including elliptical) and square shapes. When the Fe-Co alloy rod is a round rod, the diameter is 5 to 20 mm. For rods other than round rods, the equivalent diameter of the cross-section is 5 to 20 mm. Unless otherwise specified, the rod in this embodiment is a round rod with a circular cross-sectional shape. <Composition of hot-rolled material> First, in this embodiment, a hot-rolled Fe-Co alloy is prepared. In this invention, the Fe-Co alloy refers to an alloy material in which Fe+Co accounts for 95% or more by mass, and Co is present at 25-60%. This allows for the expression of a high magnetic flux density.

[0008] Next, elements that may be included in the Fe-Co alloy of the present invention will be described. In order to improve workability and magnetic properties, the Fe-Co alloy of the present invention may contain one or more elements of V, Si, Mn, Al, Zr, B, Ni, Ta, Nb, W, Ti, Mo, and Cr in a total amount of up to 5.0% by mass. Other unavoidable impurity elements include, for example, C, S, P, and O, and it is preferable to set the upper limit of each of these to 0.1%.

[0009] The Fe-Co alloy rod of the present invention has grains with a GOS (Grain Orientation Spread) value of 0.5° or higher that account for more than 80% of the area ratio. This GOS value can be measured by the conventionally known "SEM-EBSD method (electron beam backscatter diffraction)" and can be derived by calculating the orientation difference of the points (pixels) that make up the grains. The crystal orientation difference obtained from the GOS value is an indicator of the strain imparted to the alloy by processing. When grains with a GOS value of 0.5° or higher account for more than 80% of the area ratio, the driving force for grain growth is introduced into the rod, which has the advantage of stably obtaining good magnetic properties. When the area ratio of grains with a GOS value of 0.5° or higher is 80% or less, the driving force for grain growth is insufficient in the rod, and stably obtaining good magnetic properties is not possible. Preferably, the area ratio of grains with a GOS value of 0.5° or higher is 82% or higher, and more preferably 84% or higher. There is no particular upper limit to the area ratio of crystal grains with a GOS value of 0.5° or higher; for example, it can be 99%. Crystal grains with a GOS value of 0.5° or higher can be observed in a cross-section perpendicular to the axis of the bar. While the area ratio can be observed in both the perpendicular-axis and axial sections, it is preferable that the area ratio exceeds 80% (more preferably 82% or higher, and even more preferably 84% or higher) in both the perpendicular-axis and axial sections of the bar. This is because the effect of strain caused by rolling marks in the base material during the hot rolling process is more easily observed in the axial section of the bar, and the area ratio observed in the axial section may be smaller than that observed in the perpendicular-axis section. Therefore, even in the axial section, where the area ratio tends to be smaller, the effects of the present invention can be more reliably achieved if the above area ratio value is met.

[0010] The Fe-Co diameter alloy rod of the present invention is also characterized in that the difference between the area ratio of crystal grains showing a GOS value of 0.5° or more observed in a cross section perpendicular to the rod's axis and the area ratio of crystal grains showing a GOS value of 0.5° or more observed in an axial cross section of the rod is within 10%. This is because a large difference (anisotropy) between the area ratio observed in a cross section perpendicular to the axis and the area ratio observed in an axial cross section suggests that the variation in strain distribution increases, and this variation in the grain size of a sample subjected to annealing to impart magnetic properties will inevitably suppress crystal grain growth and become a factor in the deterioration of magnetic properties. A preferred difference in area ratio is within 7%, more preferably within 5%, and even more preferably within 3%.

[0011] Furthermore, the Fe-Co alloy rod of the present invention preferably has an average grain size number of 6.0 or higher and 8.5 or lower. This makes it easier to exhibit high magnetic properties after magnetic annealing and also tends to improve machinability. A more preferable lower limit for the average grain size number is 6.5 or higher, and a more preferable upper limit for the average grain size number is 8.0 or lower. The average grain size number can be measured according to JIS G 0551. It can be measured in a cross section perpendicular to the axis or in the axial cross section of the rod.

[0012] Next, an example of a manufacturing method for obtaining the Fe-Co alloy rod of the present invention is shown. In this embodiment, a billet obtained from an Fe-Co alloy steel ingot having the above-mentioned components is subjected to hot rolling to obtain a hot-rolled material as an intermediate material for the Fe-Co alloy rod. Since an oxide layer is formed on this intermediate material due to hot rolling, a polishing process to remove the oxide layer mechanically or chemically may be introduced, for example. This hot-rolled material has the shape of a "hot-rolled bar," for example, equivalent to an Fe-Co alloy bar. Furthermore, considering machinability in subsequent processes, the diameter may be 5 to 20 mm. For bar materials other than round bars, the equivalent diameter of the cross-section may be 5 to 20 mm.

[0013] <Solution treatment process> In this embodiment, the hot-rolled material is subjected to at least one solution treatment before the heating and straightening process described later. This solution treatment removes segregation of components in the hot-rolled material, improving its magnetic properties and also improving its workability. The heating temperature during this solution treatment is preferably between 800 and 1050°C, as too low a temperature tends to degrade workability, and too high a temperature leads to deterioration of magnetic properties. A more preferable lower temperature limit is 850°C. A more preferable upper temperature limit is 950°C, and an even more preferable upper temperature limit is 900°C. The heating time can also be set to 10 to 60 minutes. Furthermore, in the solution treatment process, a rapid cooling treatment is performed after heating to solidify the material without precipitating harmful precipitates, suppressing regularization and improving workability.

[0014] <Heating straight process> In this embodiment, a heating and straightening process is performed on the hot-rolled material described above, in which tensile stress is applied while heating. At this time, if the hot-rolled material is in the shape of a "bar", the tensile stress is applied by pulling it in the longitudinal direction of the hot-rolled bar. Through this process, a bar with very good magnetic properties and straightness can be obtained while applying residual strain to the hot-rolled material. The heating temperature at this time is set to 500 to 900°C. If it is lower than 500°C, the workability will decrease, and there is a risk that the bar will break when tensile stress is applied. On the other hand, if the heating temperature exceeds 900°C, it is not possible to apply the desired residual strain to the hot-rolled material. The lower limit of the preferred heating temperature in the heating and straightening process is 600°C, more preferably 700°C. The upper limit of the preferred heating temperature is 850°C, more preferably 830°C, and even more preferably 800°C. If the solution treatment step described above is omitted, the preferred lower limit of the heating temperature is 700°C, more preferably 730°C, and even more preferably 740°C. In this heating and straightening process, heating methods such as electrotherapy, which involves directly passing an electric current through a conductive object to be heated and heating it by Joule heating due to the object's internal resistance, or induction heating can be used. However, electrotherapy is preferred because it has the advantage of making it easier to align the easy magnetization axes of the crystal grains in the hot-rolled material in a certain direction, and it can heat the material to the target temperature rapidly (e.g., within 1 minute) and uniformly. Furthermore, the tension during the heating and straightening process is preferably adjusted to 1 to 4 MPa in order to more reliably obtain the desired residual strain. It is also preferable to adjust the elongation to 3 to 10% of the total length before the heating and straightening process.

[0015] In this embodiment, centerless grinding may be performed on the rod material after the heating and straightening process, for example, using a centerless grinder. This removes the mill scale from the surface of the rod material, further improving the roundness and tolerance accuracy of the shape. In this invention, since the straightness of the rod material is improved by the heating and straightening process, centerless grinding can be performed on long rod materials of 1000 mm or more in length without cutting them. [Examples]

[0016] (Example 1) After dividing the Fe-Co alloy steel ingots having the compositions shown in Table 1, hot rolling was performed to prepare hot-rolled bars with a diameter of Φ11.5 mm. <Sample No. 1> After performing a solution treatment on the aforementioned hot-rolled bar material by heating it to 850°C and then rapidly cooling it, a heating and straightening process was carried out in which the hot-rolled bar material was pulled in its longitudinal direction under a tension of 2.7 MPa while heating it to a temperature of 750°C, thereby producing the Fe-Co alloy bar material of Sample No. 1, which is an example of the present invention. <Sample No. 2> A comparative example, Sample No. 2, an Fe-Co alloy rod, was prepared by performing a heating and straightening process on the aforementioned hot-rolled rod without solution treatment. The conditions for the heating and straightening process were the same as for Sample No. 1.

[0017] [Table 1]

[0018] Subsequently, the average crystal grain size, GOS value, and DC magnetic properties of the samples of the present invention example and the comparative example were confirmed. For the average crystal grain size, in the cross-section (section perpendicular to the axis), using an Olympus optical microscope, a 500 μm × 350 μm field of view was observed for 10 fields of view, and in accordance with JIS G 0551, the grain size number was determined using the crystal grain size standard chart plate I. For the GOS value, it was carried out using a field emission scanning electron microscope manufactured by ZEISS and an EBSD measurement / analysis system OIM (Orientation-Imaging-Micrograph) manufactured by TSL, and the cross-section (section perpendicular to the axis) and longitudinal section (section in the axial direction passing through the central axis) of the sample were observed. The measurement field of view was 100 μm × 100 μm, and the step distance between adjacent pixels was 0.2 μm. Also, observation was carried out under the condition of discriminating the boundary where the azimuth difference between adjacent pixels is 5° or more as the crystal grain boundary, and from the obtained GOS value map, the area ratio of the crystal grains with a GOS value of 0.5° or more to the entire observed field of view was determined. For the DC magnetic properties, after sampling a sample from the obtained bar material, magnetic annealing was performed at 850 °C for 3 hours, and the maximum permeability and coercive force were measured using a DC magnetization specific test device. The observation results are shown in Table 2.

[0019]

Table 2

[0020] From Table 2, it was found that for Sample No. 1, which is an example of the present invention, the average crystal grain size number was smaller (the crystal grain diameter was larger than that of the comparative example) than that of Sample No. 2, which is a comparative example. Regarding the area ratio of crystal grains with a GOS value of 0.5° or more, it was confirmed that the example of the present invention had a much larger value than the comparative example and that the difference between the cross-section and the longitudinal section was small. Also regarding the magnetic properties, Sample No. 1, which is an example of the present invention, had a higher permeability and lower coercive force than Sample No.

Claims

[Claim 1] The material has grains with a GOS (Grain Orientation Spread) of 0.5° or higher, accounting for more than 80% of the area ratio, and the difference between the area ratio of grains with a GOS value of 0.5° or higher observed in a cross section perpendicular to the axis of the rod and the area ratio of grains with a GOS value of 0.5° or higher observed in an axial cross section of the rod is within 10%. Fe-Co alloy rod material with an average grain size number of 6.0 or higher and 8.5 or lower.

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