Manufacturing method for Fe-Co alloy rod and Fe-Co alloy rod

Abstract

Provided are an Fe-Co-based alloy rod and a method for manufacturing same, whereby excellent magnetic properties can be reliably obtained.　The method for manufacturing an Fe-Co-based alloy rod comprises a heating straightening step for applying tensile stress to a hot-rolled material of an Fe-Co-based alloy while heating the hot-rolled material to a temperature of 500-900°C. Preferably, ohmic heating is used as a heating means in the heating straightening step. In addition, the Fe-Co-based alloy rod has 20% or more by area ratio of crystal grains having a grain orientation spread (GOS) value of at least 0.5°.

Description

[Technical Field]

[0001] The present invention relates to a method for producing an Fe—Co alloy rod and an Fe—Co alloy rod. [Background technology]

[0002] Fe-Co alloy rods, such as Permendur, which are known to have excellent magnetic properties, are used in a variety of products, including sensors, cylindrical magnetic shields, solenoid valves, magnetic cores, etc. Patent Document 1, for example, describes a method for producing Fe-Co alloy rods, in which an ingot is heated to 1000°C to 1100°C, hot worked into a billet of about φ90 mm, surface scratches and the like are removed using a lathe, and the billet is heated to 1000°C to 1100°C and hot rolled into a billet of about φ6 to φ9 mm to produce a material (rod). [Prior art documents] [Patent documents]

[0003] [Patent Document 1] Japanese Patent Application Publication No. 7-166239 Summary of the Invention [Problem to be solved by the invention]

[0004] As the performance of the above-mentioned products improves, further improvements in the magnetic properties of the materials are also required. However, it is difficult to obtain consistently high magnetic properties using conventional manufacturing methods such as those described in Patent Document 1, and there is still room for further investigation. SUMMARY OF THE INVENTION It is therefore an object of the present invention to provide an Fe-Co alloy rod that can stably provide excellent magnetic properties, and a method for producing the same. [Means for solving the problem]

[0005] One aspect of the present invention is a method for producing an Fe-Co alloy bar, comprising a heating and straightening step of applying tensile stress to a hot-rolled material of an Fe-Co alloy while heating the hot-rolled material to a temperature of 500 to 900°C. Preferably, the temperature of the hot-rolled material is set to 500 to 850°C. Preferably, the heating means used in the heating and straightening step is electrical heating. Preferably, a solution treatment is carried out before the heating and straightening step.

[0006] Another aspect of the present invention is an Fe—Co alloy bar having crystal grains with a GOS (Grain Orientation Spread) value of 0.5° or more in an area ratio of 20% or more. Preferably, the average grain size number is 6.0 or more and 9.5 or less. Preferably, the average grain size number is 6.0 or more and 8.5 or less. [Effects of the Invention]

[0007] According to the present invention, it is possible to stably obtain an Fe—Co alloy rod having excellent magnetic properties. DETAILED DESCRIPTION OF THE INVENTION

[0008] An embodiment of the present invention will be described below. First, a method for producing an Fe—Co alloy bar of the present invention will be described. The Fe—Co alloy bar of the present invention is a straight rod-shaped bar having a circular (including elliptical) or rectangular cross-sectional shape. Unless otherwise specified, the bar of this embodiment is a round bar having a circular cross-sectional shape. <Hot-rolled material composition> First, in this embodiment, a hot-rolled material of an Fe-Co alloy is prepared. The Fe-Co alloy in the present invention refers to an alloy material containing, by mass %, 95% or more of Fe and Co, and 25 to 60% of Co. This allows the material to exhibit high magnetic flux density.

[0009] Next, elements that may be contained in the Fe-Co alloy of the present invention will be described. To improve workability and magnetic properties, the Fe-Co alloy of the present invention may contain one or more of the following elements: 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. Examples of other impurity elements that are inevitably contained include C, S, P, and O, and the upper limit of each of these elements is preferably set to 0.1%.

[0010] In this embodiment, a hot-rolled billet is obtained from an Fe—Co alloy steel ingot having the above-described composition as an intermediate material for the Fe—Co alloy bar by hot rolling. Since an oxide layer is formed on this intermediate material due to the hot rolling, a polishing step may be introduced to remove the oxide layer mechanically or chemically. This hot-rolled material has the shape of a "hot-rolled bar" equivalent to an Fe-Co alloy bar, for example. Taking into consideration workability in subsequent processes, the diameter may be 5 to 20 mm. For bars other than round bars, the equivalent circular diameter of the cross section may be 5 to 20 mm.

[0011] <Solution treatment process> In this embodiment, the hot-rolled material may be subjected to at least one solution treatment before the heating and straightening process described below. This solution treatment is preferable because it is expected to remove component segregation from the hot-rolled material, improve magnetic properties, and improve workability. A heating temperature during this solution treatment tends to deteriorate workability if it is too low, while a heating temperature that is too high can lead to deterioration of magnetic properties. Therefore, the solution treatment is preferably performed at a temperature of 800 to 1050°C. A more preferable lower limit of the temperature is 850°C. A more preferable upper limit of the temperature is 950°C, and an even more preferable upper limit of the temperature is 900°C. The heating time can also be set to 10 to 60 minutes. Furthermore, in the solution treatment process, rapid cooling is performed after heating to dissolve the material without precipitating harmful precipitates, suppress ordering, and improve workability. Even if the solution treatment process is omitted, the effects of the present invention can be achieved by adjusting the heating temperature in the heating and straightening process described below.

[0012] <Heating straight process> In this embodiment, the hot-rolled material is subjected to a heating and straightening process in which tensile stress is applied while being heated. If the hot-rolled material is in the shape of a "bar," the hot-rolled bar is pulled in the longitudinal direction to apply the tensile stress. This process allows the hot-rolled material to have excellent magnetic properties and straightness while imparting residual strain. The heating temperature is set to 500 to 900°C. If the temperature is lower than 500°C, workability decreases, and the bar may break when tensile stress is applied. On the other hand, if the heating temperature is higher than 900°C, it is difficult to impart desirable residual strain to the hot-rolled material. The lower limit of the heating temperature in the heating and straightening process is preferably 600°C, more preferably 700°C. The upper limit of the heating temperature is preferably 850°C, more preferably 830°C, and even more preferably 800°C. When the above-mentioned solution treatment step is omitted, the lower limit of the heating temperature is preferably 700°C, more preferably 730°C, and even more preferably 740°C. While heating methods such as electrical heating and induction heating can be used in this heating and straightening process, electrical heating is preferred because it facilitates the alignment of the easy axes of magnetization of the crystal grains in the hot-rolled material and allows the material to be heated to the target temperature quickly (e.g., within one minute) and uniformly. Furthermore, the tension during the heating and straightening process is preferably adjusted to 1 to 4 MPa to more reliably obtain the desired residual strain. Furthermore, it is preferable to adjust the elongation to 3 to 10% of the total length before the heating and straightening process.

[0013] In this embodiment, the bar stock that has undergone the heating and straightening process may be subjected to centerless grinding using, for example, a centerless grinder. This removes the black scale from the surface of the bar stock, thereby improving the roundness and tolerance accuracy of the shape. In the present invention, since the straightness of the bar stock is improved by the heating and straightening process, even long bar stock with a length of 1000 mm or more can be subjected to centerless grinding without cutting.

[0014] Next, we will explain the Fe-Co alloy bar of the present invention, which can be obtained by the above-mentioned manufacturing method of the present invention. The Fe-Co alloy bar of the present invention has 20% or more crystal grains with a GOS (Grain Orientation Spread) value of 0.5° or more in area ratio. This GOS value can be measured using the conventionally known "SEM-EBSD method (Electron Backscatter Diffraction)" and can be derived by calculating the misorientation of the points (pixels) that make up the crystal grains. The crystal misorientation obtained by the GOS value is an index of the strain imparted to the alloy by processing. When 20% or more crystal grains with a GOS value of 0.5° or more in area ratio are present in the bar, the driving force for grain growth is introduced, which is advantageous in obtaining good magnetic properties. When the area ratio of the GOS value of 0.5° or more is less than 20%, the driving force for grain growth is insufficient, and good magnetic properties cannot be obtained. Among crystal grains with a GOS value of 0.5° or more, the area ratio is preferably 40% or more, more preferably 50% or more, even more preferably 60% or more, even more preferably 70% or more, particularly preferably 80% or more, and most preferably 90% or more. The crystal grains with a GOS value of 0.5° or more can be observed in the cross section of the rod in the direction perpendicular to the axis. The cross section for observing the area ratio can be either the cross section perpendicular to the axis or the axial cross section. However, the area ratio is preferably 20% or more (more preferably 40% or more, even more preferably 50% or more, even more preferably 60% or more, particularly preferably 70% or more, and most preferably 80% or more) in both the cross section perpendicular to the axis and the axial cross section of the rod. This is because the influence of strain due to rolling marks generated in the base metal during the hot rolling process is easily observed in the axial cross section of the rod, and the area ratio observed in the axial cross section may be smaller than the area ratio observed in the cross section perpendicular to the axis. Therefore, even in an axial cross section where the area ratio tends to be small, the effects of the present invention can be more reliably achieved as long as the above-mentioned area ratio values ​​are satisfied.

[0015] Furthermore, the Fe-Co alloy bar of the present invention preferably has an average grain size number of 6.0 or more and 9.5 or less. This makes it easier to exhibit high magnetic properties after magnetic annealing and also tends to further improve workability. A more preferred lower limit of the average grain size number is 6.5 or more, and a more preferred upper limit of the average grain size number is 9.0 or less. An even more preferred upper limit of the average grain size number is 8.5 or less, and even more preferably 8.0 or less. The average grain size number can be measured in accordance with JIS G 0551. It can be measured on a cross section perpendicular to the axis or on an axial cross section of the bar. [Example]

[0016] Example 1 An Fe-Co alloy steel ingot having the composition shown in Table 1 was bloomed and then hot rolled to prepare a hot rolled bar having a diameter of 11.5 mm. <Sample No. 1, Sample No. 2> The above-mentioned hot-rolled bar was subjected to a solution treatment in which it was heated to 850°C and then rapidly cooled. Then, a heating and straightening process was carried out in which the hot-rolled bar was pulled in its length direction under a tension of 2.7 MPa while being heated so that the temperature of the bar reached 750°C, thereby producing Fe—Co-based alloy bars as Samples No. 1 and 2, which are examples of the present invention. <Sample No. 3> The hot-rolled bar described above was not subjected to solution treatment, but instead subjected to a heating and straightening process to produce an Fe—Co alloy bar as an example of the present invention, Sample No. 3. The heating and straightening process conditions were the same as those for Sample No. 1. <Sample No. 4> The above-mentioned hot-rolled bar was subjected to solution treatment under the same conditions as those of Sample No. 1, and an Fe—Co alloy bar of Sample No. 4 was also produced as a comparative example, in which the heating and straightening step was not performed and the other steps were the same as those of the present invention.

[0017] [Table 1]

[0018] Next, the average grain size, GOS value, and DC magnetic properties of the inventive and comparative samples were measured. The average grain size was measured by observing ten 500 μm × 350 μm fields of view on the cross sections (cross sections perpendicular to the axis) using an Olympus optical microscope. Grain size numbers were determined using the grain size standard plate I in accordance with JIS G 0551. The GOS value was measured using a ZEISS field-emission scanning electron microscope and a TSL EBSD measurement and analysis system, OIM (Orientation-Imaging-Micrograph). For samples No. 1 and No. 4, the cross sections (cross sections perpendicular to the axis) were observed. For samples No. 2 and No. 3, both the cross sections and longitudinal sections (axial sections passing through the central axis) were observed. The measurement field of view was 100 μm × 100 μm, and the step distance between adjacent pixels was 0.2 μm. Observations were also conducted under conditions that allowed for boundaries with a misorientation of 5° or more between adjacent pixels to be identified as grain boundaries, and the area ratio of grains with a GOS value of 0.5° or more to the entire observation field was calculated from the resulting GOS value map. For DC magnetic properties, samples were taken from the resulting rods and subjected to magnetic annealing at 850°C for 3 hours. The maximum magnetic permeability and coercivity were then measured using a DC magnetization specific testing device. The observation results are shown in Table 2.

[0019] [Table 2]

[0020] From Table 2, it can be seen that Samples No. 1 and No. 2, which are examples of the present invention, have smaller average grain size numbers than the comparative examples (larger grain sizes than the comparative examples), while Sample No. 3, which was not solution-treated, has the same average grain size number as the comparative example. It was confirmed that the area ratio of crystal grains with a GOS value of 0.5° or more was significantly higher in the examples of the present invention than in the comparative examples. With regard to magnetic properties, Samples No. 1 to No. 3 had higher permeability and lower coercivity than the comparative examples. This confirmed that all of the examples of the present invention had better magnetic properties than the comparative examples.

[0021] Example 2 An Fe-Co alloy steel ingot having the composition shown in Table 3 was bloomed and then hot-rolled to prepare a hot-rolled bar with a diameter of 11.5 mm. The bar was then heated to the temperature shown in Table 4 without solution treatment, and subjected to a heating and straightening process under a tension of 2.7 MPa, to produce Fe-Co alloy bars Nos. 5 to 7. The results in Table 4 confirm that all of Samples 5 to 7, which underwent the heating and straightening process at bar temperatures of 500 to 900°C, had low coercive force and excellent magnetic properties.

[0022] [Table 3]

[0023] [Table 4]

Claims

1. A hot-rolled material of an Fe-Co alloy containing 25 to 60% Co by mass and having a total content of Fe and Co of 95% or more, A heating and straightening step of applying tensile stress to the hot-rolled material while heating the material to a temperature of 500 to 900°C, A method for producing an Fe—Co-based alloy rod, which produces an Fe—Co-based alloy rod having an area ratio of 20% or more of crystal grains exhibiting a GOS (Grain Orientation Spread) value of 0.5° or more.

2. 2. The method for producing an Fe—Co alloy rod according to claim 1, wherein the temperature of the hot-rolled material is 500 to 850° C.

3. 3. The method for producing an Fe—Co alloy rod according to claim 1, wherein the heating means in the heating and straightening step is electrical heating.

4. The method for producing an Fe—Co alloy rod according to any one of claims 1 to 3, wherein a solution treatment is carried out before the heating and straightening step.

5. A steel sheet containing 25 to 60% Co by mass, with the total content of Fe and Co being 95% or more, An Fe—Co alloy bar having an area ratio of 20% or more of crystal grains exhibiting a GOS (Grain Orientation Spread) value of 0.5° or more.

6. 6. The Fe—Co alloy rod according to claim 5, wherein the average grain size number is 6.0 or more and 9.5 or less.

7. 6. The Fe—Co alloy rod according to claim 5, wherein the average grain size number is 6.0 or more and 8.5 or less.

Images