LAMINATED MOLDED ARTICLE MADE OF FeCo-BASED ALLOY

Abstract

The purpose of the present invention is to provide a laminated molded article made of an FeCo-based alloy that exhibits excellent soft magnetic properties. The present invention provides a laminated molded article that is laminated and molded using FeCo-based alloy powder, and is characterized by including a B2 regular phase and an ɑ phase in the constituent phase.

Description

Additive manufacturing of FeCo alloy

[0001] The present invention relates to an additively manufactured object using an FeCo-based alloy suitable for a rapid melting and rapid solidification process such as a three-dimensional additive manufacturing method.

[0002] Permendur, whose representative composition is Fe49Co2V (mass %), is an FeCo-based alloy known as a soft magnetic material with low coercivity and high saturation magnetic flux density. Permendur is used in small, high-power motors, solenoid valves requiring high magnetic force, pole pieces for electronic devices, and the like. Permendur is a difficult-to-process material that becomes embrittled due to the precipitation of the B2 ordered phase, so it is not easy to process steel containing the B2 ordered phase into parts.

[0003] It would be advantageous to be able to manufacture near-net-shape parts using metal additive manufacturing, but simply using additive manufacturing with the component composition of Permendur does not necessarily result in the original soft magnetic properties. For example, in a summary of research presentations on the application of metal additive manufacturing to Fe50Co (see Non-Patent Document 1), X-ray diffraction data for the additively manufactured product is shown, and although unidentified peaks other than the α phase are observed, the B2 ordered phase is not recognized within those peaks, and the soft magnetic properties of the ingot material of Permendur are not exhibited, which cannot be said to be sufficient.

[0004] Tetsuji Kuze et al., "Effects of Forming and Heat Treatment Conditions on the Properties of Soft Magnetic Materials," Japan Society of Powder and Powder Metallurgy Lecture Abstracts 2-29A (Spring Meeting 2023)

[0005] Permendur is a soft magnetic material with low coercivity and high saturation magnetic flux density, and the B2 ordered phase is responsible for improving its soft magnetic properties. However, if the B2 ordered phase is present in the metal structure, it will be brittle, resulting in poor toughness and making it difficult to process in practice. Therefore, from the viewpoint of mechanical properties such as toughness, attempts have been made to control the formation of the B2 ordered phase in ingot materials by heat treatment or by actively adding V to control the content of the B2 ordered phase.

[0006] Since additive manufacturing is a manufacturing method suitable for forming complex three-dimensional shapes, it is possible to manufacture additively manufactured objects that can be processed to near-net shapes in advance. This would at first glance seem to make it easier to reduce the weight given to toughness in the processing aspect.

[0007] However, when additive manufacturing is attempted using powder of components with the permendur composition, the B2 ordered phase is not contained, as described in Non-Patent Document 1. As a result, although the component composition itself is the same as permendur, additive manufacturing products formed by additive manufacturing methods involving rapid melting and rapid solidification do not exhibit the expected excellent soft magnetic properties, even though they use nearly 50% expensive Co, and are not sufficient to achieve the desired soft magnetic properties.

[0008] Even if the component composition is the same, the crystalline structure of the object manufactured by metal additive manufacturing is different from that of the ingot material, and because the object is manufactured by repeatedly performing the step of rapidly cooling and solidifying locally melted powder, the object is manufactured without forming the B2 ordered phase simply by additive manufacturing.

[0009] The peaks not identified in Non-Patent Document 1 are thought to be due to either the γ phase, the oxide phase, or a peak derived from strain specific to the metal lamination, and are different from the B2 ordered phase.

[0010] Therefore, the problem to be solved by the present invention is to provide an additively manufactured product made of an FeCo alloy formed by an additive manufacturing method, which exhibits excellent soft magnetic properties. Note that an "FeCo-based alloy" refers to an alloy whose main components are Fe and Co, with the remainder consisting of unavoidable impurities. "FeCo-based alloys" also include alloys that further contain a small amount of V as an optional additional component.

[0011] The inventors have found that, because the B2 ordered phase in an FeCo-based alloy is formed when cooling is slow, in an object formed by an additive manufacturing method in which fine powder is rapidly melted and rapidly solidified, the B2 ordered phase does not form in the state in which it is rapidly melted, rapidly solidified, and left in its current state; and that, because the structure immediately after additive manufacturing is fine, the object in the rapidly solidified state immediately after additive manufacturing has an excessively high coercive force, making it difficult to obtain soft magnetic properties equivalent to those of the commonly used ingot material, Permendur. Based on this knowledge, the inventors have conducted further intensive research and have found that, by devising the heat treatment conditions for an additive manufactured object formed by an additive manufacturing method involving rapid melting and rapid solidification using an FeCo-based alloy powder (which may contain V as an optional additional component), an additive manufactured object containing the B2 ordered phase and the α phase in the constituent phases that form the metal structure can be obtained, and that an additive manufactured object exhibiting excellent soft magnetic properties equivalent to those of native Permendur can be obtained.

[0012] In other words, the inventors discovered that, in FeCo-based alloys, the coercive force generally increases when the crystal grains are fine, and therefore, when rapidly melted and rapidly solidified, the alloy forms a fine structure and does not exhibit its original magnetic properties. However, by annealing the additively manufactured product at a high temperature above 1000°C, which is the γ single phase region, the crystal grains become coarse and a structure containing the B2 ordered phase is obtained, and as a result, an additively manufactured product is obtained that has excellent soft magnetic properties comparable to those of ingot-formed Permendur material.

[0013] Therefore, a first means for solving the problems of the present invention is an additively manufactured product obtained by additive manufacturing using an alloy powder made of an FeCo-based alloy, characterized in that the constituent phases include a B2 ordered phase and an α phase. Note that the "FeCo-based alloy" refers to an alloy whose main components are Fe and Co, which may optionally contain a small amount of V as an optional component, and the remainder being unavoidable impurities.

[0014] The second means for solving the problems of the present invention is to measure the layered manufactured product by X-ray diffraction using a Co tube, and determine whether the peak intensity ratio of the peak intensity B2(100) of the (100) plane of the B2 ordered phase to the peak intensity α(200) of the (200) plane of the α phase satisfies the following condition: B2(100) / α(200)≧2.5×10－２ The layered object according to the first aspect of the present invention is characterized in that the following is satisfied:

[0015] A third means for solving the problems of the present invention is the additively manufactured article according to the first or second means, characterized in that the FeCo-based alloy is an alloy consisting of, by mass%, 45.0 to 55.0% Co, 0 to 2.5% V, and the balance Fe and unavoidable impurities. V is an optional component, and the amount of V may be 0% or more than 0%.

[0016] A fourth means for solving the problems of the present invention is the layered object according to any one of the first to third means, in which the average crystal grain size of the layered object is 15 μm or more.

[0017] According to the present invention, it is possible to provide an additively manufactured product made of an FeCo-based alloy that has a high saturation magnetic flux density, a low coercive force, and excellent soft magnetic properties. As shown in Figure 2, the additively manufactured product does not contain the B2 ordered phase in the as-added state (as-existing state after rapid melting and rapid solidification), so the addition of V is optional. Furthermore, by devising the heat treatment conditions (e.g., annealing conditions) of the additively manufactured product formed by the additively manufactured method involving rapid melting and rapid solidification, it is possible to include the B2 ordered phase in the constituent phases that form the metal structure, thereby obtaining soft magnetic properties similar to those of ingot materials, and also allowing for appropriate adjustment of mechanical properties such as toughness.

[0018] Fig. 1 is an X-ray diffraction chart showing the results of X-ray diffraction measurement using a Co tube on an additively manufactured product that was additively manufactured using an FeCo-based alloy powder and then annealed from 1100°C, where the horizontal axis shows 2θ and the vertical axis shows intensity on a logarithmic scale. Fig. 2 is an X-ray diffraction chart showing the results of X-ray diffraction measurement using a Co tube on an additively manufactured product that was additively manufactured using an FeCo-based alloy powder, where the horizontal axis shows 2θ and the vertical axis shows intensity on a logarithmic scale.

[0019] The additively manufactured product of the present invention is an additively manufactured product produced by additive manufacturing using an alloy powder made of an FeCo-based alloy (hereinafter referred to as "FeCo-based alloy powder"). The additively manufactured product of the present invention is characterized by including a B2-ordered phase and an α-phase among its constituent phases. The additively manufactured product of the present invention is made of an FeCo-based alloy, similar to the FeCo-based alloy powder. An additively manufactured product of the present invention containing the B2-ordered phase in addition to the α-phase can be obtained by annealing an additively manufactured product (hereinafter referred to as an "unheat-treated product") produced by additive manufacturing using an FeCo-based alloy (which may optionally contain V) as the material, and then slowly cooling it.

[0020] [Powder] The FeCo-based alloy powder used in additive manufacturing will be described. FeCo-based alloy powder can be obtained by various methods, including water atomization, single-roll quenching, twin-roll quenching, gas atomization, disk atomization, and centrifugal atomization. From the viewpoint of spheroidization, the FeCo-based alloy powder is preferably a gas-atomized powder. Furthermore, from the viewpoint of the fluidity and packing rate of the FeCo-based alloy powder, the average particle diameter of the FeCo-based alloy powder is preferably 10 μm or more and 100 μm or less in terms of volume average particle diameter (D50). D50 is the particle diameter at the point where the cumulative volume is 50% on a volume-based cumulative frequency distribution curve calculated assuming the total volume of the powder to be 100%. D50 is measured by a laser diffraction scattering method. An example of a suitable device for this measurement is Nikkiso's laser diffraction / scattering particle size distribution measuring device, the "Microtrac MT3000." Powder is poured into the cell of this device together with pure water, and the particle size is detected based on the light scattering information of the particles. Below, we will explain this using gas atomized powder as an example.

[0021] [Modeling] A specific example of a method for producing a modeled object is a rapid melting and rapid solidification process involving melting and solidifying FeCo-based alloy powder. Specific examples of this process include three-dimensional additive manufacturing (3D AM), thermal spraying, laser coating, and build-up welding. A modeled object manufactured using FeCo-based alloy powder is preferably manufactured using a three-dimensional AM method. Specific examples of three-dimensional AM methods include powder bed fusion (PBL) and directed energy deposition (PD). Specific examples of powder bed fusion (PBL) methods include selective laser sintering (SLS), selective laser melting (SLM), and electron beam melting (EBM). FeCo-based alloy powder is suitable for three-dimensional AM, particularly powder bed fusion, and can produce large, high-density models.

[0022] Three-dimensional additive manufacturing can be performed using, for example, a 3D printer, and can produce complex, three-dimensional, near-net-shape additively manufactured objects. In powder bed fusion (powder bed) additive manufacturing, a laser beam or electron beam is irradiated onto a spread FeCo-based alloy powder. The irradiation causes the particles to rapidly heat and melt. The molten particles then rapidly solidify. This melting and solidification process bonds the particles together. Irradiation is selectively performed on a portion of the spread FeCo-based alloy powder. The unirradiated portions of the spread powder do not melt. A bonding layer is formed only in the irradiated portions.

[0023] A thin layer of FeCo-based alloy powder is spread on the bonding layer. A laser beam or an electron beam is irradiated onto a portion of the FeCo-based alloy powder. The irradiation causes the particles to rapidly melt. The molten particles then rapidly solidify. This melting and solidification process bonds the particles in the powder together, forming a new bonding layer. The new bonding layer also bonds with the existing bonding layer.

[0024] By repeating the bonding process through irradiation, the aggregate of bonding layers gradually grows. This growth results in an additively manufactured object with a three-dimensional shape. This additive manufacturing method makes it easy to obtain additively manufactured objects with complex shapes.

[0025] [Heat treatment] The unheat-treated object formed by additive manufacturing using FeCo-based alloy powder is not used as is, but rather undergoes a process of annealing heat treatment to obtain an additive manufacturing object of the present invention having the desired properties.

[0026] By setting the cooling rate during annealing of the unheat-treated shaped product to 2000°C / hr or less, a layered shaped product containing the B2 ordered phase can be obtained. Furthermore, by lowering the cooling rate, the amount of the B2 ordered phase can be increased, thereby improving the soft magnetic properties. The cooling rate is preferably 600°C / hr or less, and more preferably 100°C / hr or less. The lower limit of the cooling rate can be adjusted as appropriate, and may be, for example, 30°C / hr or more or 60°C / hr or more. Each of these lower limits may be combined with any of the upper limits described above.

[0027] When used in conventional processes such as forging, FeCo-based alloys are annealed at temperatures below 900°C, which is in the α single-phase region. However, additive manufacturing processes using additive manufacturing methods involving rapid melting and rapid solidification have a rapidly solidified microstructure in the as-manufactured state, resulting in excessively high coercivity. Therefore, annealing at temperatures above 900°C coarsens the crystal grains, thereby achieving excellent soft magnetic properties with low coercivity. Furthermore, annealing at temperatures above 1000°C, which is in the γ single-phase region, can promote the precipitation of the B2 ordered phase. Annealing is performed by cooling from the γ single-phase region, and the annealing temperature is preferably above 1000°C, more preferably above 1050°C, and even more preferably above 1100°C. The upper limit of the annealing temperature can be adjusted as appropriate, and may be, for example, below 1200°C or below 1150°C. Each of these upper limits may be combined with any of the above-mentioned lower limits.

[0028] [X-ray diffraction peak intensity ratio B2(100) / α(200)] When the layered object of the present invention is measured by X-ray diffraction using a Co tube, the peak intensity ratio of the peak intensity B2(100) of the (100) plane of the B2 ordered phase to the peak intensity α(200) of the (200) plane of the α phase is B2(100) / α(200)≧2.5×10 －２ The above condition is satisfied. "Peak intensity" means the value obtained by subtracting the background intensity from the peak top intensity (i.e., the height from the baseline to the peak top). "Peak top" means the peak apex showing the maximum intensity value. X-ray diffraction analysis can be performed using a commercially available X-ray diffraction device. The conditions for X-ray diffraction analysis can be those described in the Examples. Peak intensity can be measured by removing the background (baseline) intensity from the X-ray diffraction pattern obtained by X-ray diffraction analysis, separating peaks, etc., using software provided with the commercially available X-ray diffraction device. Peak separation can be performed by fitting using a fitting function such as a Lorentzian function.

[0029] From the data obtained by X-ray diffraction using a Co tube, the peak intensity ratio of B2(100) / α(200) can be calculated to quantify the content of the B2 ordered phase. Since an FeCo-based alloy containing the B2 ordered phase exhibits excellent soft magnetic properties, the peak intensity ratio B2(100) / α(200) is preferably 2.5×10 －２ or more, more preferably 3.3 × 10 －２ More preferably, 3.9 × 10 －２ The upper limit is not particularly limited, and is, for example, 10.0 × 10 －２ or less, or 8.0 × 10 －２ Each of these upper limits may be combined with any of the lower limits mentioned above.

[0030] [Crystalline Grain Size] Layer-by-layer-manufactured products using fine FeCo-based alloy powders tend to have finer crystal grain sizes and higher coercivity than conventional ingot materials. However, the larger the crystal grain size, the lower the coercivity and the better the soft magnetic properties. Therefore, by heat-treating the unheat-treated shaped product, the layer-by-layer-manufactured product of the present invention has an average crystal grain size of 15 μm or more, excellent soft magnetic properties can be obtained. Therefore, the average crystal grain size of the layer-by-layer-manufactured product of the present invention is preferably 15 μm or more, more preferably 21 μm or more, even more preferably 42 μm or more, and even more preferably 81 μm or more. The crystal grain size can be measured by the method described in the examples.

[0031] [Coercive force] Since FeCo alloys are used as soft magnetic materials, low coercive force is preferable. Therefore, the coercive force of the layered object of the present invention is preferably 280 A / m or less, more preferably 181 A / m or less, and even more preferably 75 A / m or less. The coercive force can be measured by the method described in the examples.

[0032] [Saturation magnetic flux density] The saturation magnetic flux density of the layered object of the present invention is preferably high. The saturation magnetic flux density of the layered object of the present invention is preferably 2.1 T or more, more preferably 2.15 T or more, and even more preferably 2.20 T or more. The saturation magnetic flux density can be measured by the method described in the examples.

[0033] [Components] The following describes the preferred component compositions of the FeCo-based alloy powder used in additive manufacturing and the FeCo-based alloy that constitutes the additively manufactured product using the powder. Note that % for each component is by mass %.

[0034] Co: 45.0 to 55.0% Co is a basic component for obtaining a magnetic material. Therefore, the Co content is preferably 45.0 to 55.0%. If the Co content is less than 45%, the magnetic permeability will be low and the coercivity will be high. From this perspective, the lower limit of the Co content is preferably 45.0% or more, more preferably 47.0% or more, even more preferably 48.0% or more, and even more preferably 49.0% or more. On the other hand, if the Co content exceeds 55%, the saturation magnetic flux density will be low and the coercivity will be high. From this perspective, the upper limit of Co is preferably 55.0% or less, more preferably 53.0% or less, even more preferably 52.0% or less, and even more preferably 51.0% or less. Each of these upper limits may be combined with any of the above-mentioned lower limits.

[0035] V: 0 to 2.5% V is a component that can be optionally added to FeCo-based alloys as a component that improves workability. The amount of V added may be 0% or more than 0%. If the B2 ordered phase is excessive, toughness deteriorates and workability deteriorates, so adding V improves workability. However, if V is excessive, not only will the saturation magnetic flux density decrease, but the coercive force will also increase. Therefore, the V content is preferably 0 to 2.5% (including 0%).

[0036] Since the layered object of the present invention is an layered object produced by the layered manufacturing method, a near-net shape can be pre-formed. Therefore, the amount of V added can be reduced, prioritizing soft magnetic properties over processability. From this perspective, the V content is preferably 2.0% or less, more preferably 1.0% or less, and even more preferably 0.5% or less. The V content may be 0% or more than 0%.

[0037] Remainder: Fe and unavoidable impurities. Fe is generally a component with a high saturation magnetic moment, and by adding Co to Fe, it is possible to realize an excellent saturation magnetic flux density as an FeCo-based alloy.

[0038] Tables 1 and 2 show the chemical compositions of the alloy powders used in the examples and comparative examples. In Tables 1 and 2, "%" represents mass %, and "Bal." represents the remainder. The chemical compositions of the additively manufactured objects using each alloy powder are almost the same as the chemical compositions of the alloy powders used.

[0039] [Preparation of Alloy Powder] The alloy powder was prepared by vacuum melting inert gas atomization. Specifically, raw materials having the predetermined compositions listed in Tables 1 and 2 were heated and melted in a vacuum in an alumina crucible using high-frequency induction heating. The molten metal was then dropped from a 5 mm diameter nozzle located below the crucible, and high-pressure argon gas was sprayed onto the molten metal to obtain alloy powder. The molten metal was then classified using a sieve with a mesh size of -63 μm, and the resulting undersized powder was used as alloy powder for additive manufacturing. Note that "-63 μm" indicates that the mesh size is less than 63 μm.

[0040] [Additive Manufacturing] Using each alloy powder for additive manufacturing as a raw material, additive manufacturing was performed using a three-dimensional additive manufacturing device (EOS-M280 manufactured by EOS Corporation) to obtain an additive manufacturing object consisting of a 10 mm x 10 mm x 10 mm rectangular parallelepiped. The additive manufacturing method was performed under the modeling conditions, based on the standard device parameters MS1 (layer thickness 40 μm), with the output changed to 300 W and the scanning speed changed to 1100 mm / s. The obtained additive manufacturing object was used as a test piece for coercive force measurement.

[0041] [Heat Treatment Conditions] Tables 1 and 2 show the heat treatment conditions for the additive manufacturing products of the Examples and Comparative Examples. Annealing was performed under one of the following conditions: furnace cooling in a vacuum atmosphere, gas cooling in an Ar atmosphere, or water cooling in an air atmosphere, and differences in cooling rate were evaluated. In Examples 1 to 3 and 5 and Comparative Examples 1 to 3, furnace cooling in a vacuum atmosphere was used, in Examples 4 and 6, gas cooling in an Ar atmosphere was used, and in Comparative Example 4, water cooling in an air atmosphere was used.

[0042] [X-ray diffraction peak intensity ratio B2(100) / α(200)] The heat-treated shaped object (10mm x 10mm x 10mm) was cut along a plane perpendicular to the lamination direction, mechanically polished, and X-ray diffraction measurements were performed on the polished surface. X-ray diffraction measurements were performed using a Rigaku RAPID II X-ray diffractometer and a Co tube as the X-ray source. The ratio of the peak intensity α(200) of the reflection of the (200) plane of the α phase (PDF number: 01-087-0722) to the peak intensity B2(100) of the reflection of the (100) plane of the B2 ordered phase (PDF number: 01-071-5029) (peak intensity B2(100) / peak intensity α(200)) was calculated and used as the X-ray diffraction peak intensity ratio B2(100) / α(200). The peak intensities were measured by using the software provided with the X-ray diffractometer to remove the background (baseline) intensity from the obtained X-ray diffraction pattern, separate the peaks, etc. Peak separation was performed by fitting using a Lorentz function.

[0043] The conditions for the X-ray diffraction analysis were as follows: X-ray source: Co tube, tube voltage: 40 kV, tube current: 40 mA, measurement angle: 20° to 110°, measurement step width: 0.045°, width scan speed: 0.225° / sec.

[0044] [Structural Observation: Determination of Crystal Grain Size] The heat-treated molded product (10 mm × 10 mm × 10 mm) was cut along a plane perpendicular to the lamination direction and mechanically polished. The polished surface was then subjected to aqua regia corrosion treatment, and the center of the embedded sample was observed with an optical microscope at a magnification of 400. Observation was performed at five randomly selected locations, and the average value of the crystal grain size calculated by the line segment method was taken as the average crystal grain size of the sample.

[0045] [Coercive Force Measurement] The coercive force was measured using a coercive force meter (HC-1031, manufactured by Denshijiki Kogyo Co., Ltd.) The heat-treated shaped object (10 mm × 10 mm × 10 mm) was placed in the coercive force meter, and a magnetic field was applied to a plane perpendicular to the stacking direction to measure the coercive force.

[0046] [Measurement of Saturation Magnetic Flux Density] The saturation magnetic flux density was measured using a vibrating sample magnetometer (VSM). A magnetic field was applied to the heat-treated shaped object (2 mm × 2 mm × 2 mm) in a plane perpendicular to the stacking direction, and the saturation magnetic flux density was measured.

[0047] The results of each measurement are shown in Tables 1 and 2. In Table 2, the underlined parts indicate that the component composition or peak intensity ratio is outside the range of the present invention, and that the effect is less than that of the present invention.

[0048]

[0049]

[0050] In the examples, the samples were annealed from a high temperature of 1000°C or higher and then slowly cooled, resulting in the observation of a B2 ordered phase, as shown in Figure 1. The coercive force of each of the examples was 200 A / m or less, demonstrating excellent coercive force. Furthermore, the saturation magnetic flux density of each of the examples was 2.10 T or higher, demonstrating excellent soft magnetic properties.

[0051] The peak intensity ratio B2(100) / α(200) in Example 6 is 2.2 × 10 －２ This was low, and was below the peak intensity ratio of 2.5 or more specified in the second aspect of the present invention. This indicates that the content of the B2 ordered phase was somewhat low, but the coercive force was somewhat higher than in the other examples.

[0052] In the examples, no unidentifiable peaks were observed other than the α phase described in Non-Patent Document 1. In Non-Patent Document 1, the B2 ordered phase was not observed, and the layer thickness during molding was 20 μm, whereas in the examples, the layer thickness was 40 μm, and different molding conditions were applied from those in Non-Patent Document 1, so the difference in thermal history during rapid solidification caused a difference in the constituent phases.

[0053] In the non-patent document, annealing was performed in the α single phase region below 1000°C, whereas in the examples, annealing was performed in the γ single phase region, and this high-temperature annealing also promotes the precipitation of the B2 ordered phase.

[0054] The examples have a different constituent phase from that of Non-Patent Document 1, and contain a B2 ordered phase, which results in a coercive force of 200 A / m or less. Therefore, it was confirmed that the soft magnetic properties of bulk permendur in the ingot material can also be achieved in the additively manufactured product.

[0055] On the other hand, the coercive force of all the comparative examples exceeded 300 A / m, resulting in poor coercive force. The saturation magnetic flux density was also 2.08 T or less, lower than that of the examples. Comparative Example 1 contained an excessive amount of V, resulting in a too high coercive force and a low saturation magnetic flux density. Comparative Example 2 contained an insufficient amount of Co, resulting in a too high coercive force and a low saturation magnetic flux density. Comparative Example 3 contained an excessive amount of Co, resulting in a too high coercive force and a low saturation magnetic flux density. Comparative Example 4 was water-cooled, and therefore did not contain the B2 ordered phase, which would not form unless cooling was slow, resulting in a high coercive force and a low saturation magnetic flux density.

[0056] The additively manufactured products using the FeCo-based alloy according to the present invention exhibit excellent soft magnetic properties, and can therefore be used in components such as small, high-power motors, solenoid valves that require high magnetic force, and pole pieces for electronic devices.

Claims

1. An additively manufactured object produced by additive manufacturing using alloy powder made of an FeCo-based alloy, characterized in that the constituent phases include a B2 ordered phase and an α phase.

2. When the layered product is measured by X-ray diffraction using a Co tube, the peak intensity ratio of the peak intensity B2(100) of the (100) plane of the B2 ordered phase to the peak intensity α(200) of the (200) plane of the α phase is B2(100) / α(200)≧2.5×10 －２ The layered object according to claim 1 , which satisfies the following:

3. The layered product according to claim 1 or 2, characterized in that the FeCo-based alloy is an alloy consisting of, in mass%, Co: 45.0 to 55.0%, V: 0 to 2.5%, and the remainder: Fe and unavoidable impurities.

4. The layered product according to claim 1 or 2, wherein the average crystal grain size of the layered product is 15 μm or more.

5. The layered product according to claim 3, wherein the average crystal grain size of the layered product is 15 μm or more.

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