Directional electromagnetic stainless steel welded laminated structure and electromagnetic component

Abstract

To provide a grain-oriented electromagnetic stainless steel having excellent soft magnetic properties, and having a<100>orientation aligned in a specific direction, and an electromagnetic component.SOLUTION: A grain-oriented electromagnetic stainless steel is provide which has a predetermined chemical composition, has a plurality of layers 6 stacked together, and comprises crystals with an angle difference of 20° or less between a stacking direction 12 of layers 6 and a crystal<100>orientation, the area ratio of the crystals being 0.70 or more. Also a magnetic component is provided which is made from a stainless steel having a predetermined chemical composition, and comprises crystals with an angle difference of 20° or more between an applied magnetic field direction(intended applied magnetic field direction) at being used as a magnetic component and a crystal<100>orientation, wherein the area ratio of the crystals is 0.70 or more. Excellent grain-oriented electromagnetic properties can be achieved since the crystal<100>orientation is oriented in the stacking direction or the intended applied magnetic field direction.SELECTED DRAWING: Figure 1

Description

Technical Field

[0001] The present invention relates to a directionally electromagnetic stainless steel and electromagnetic components.

Background Art

[0002] Electromagnetic steel (electromagnetic steel sheets and electromagnetic bar steels) is widely used as a core material for electrical equipment. Electromagnetic steel sheets are roughly classified into grain-oriented electromagnetic steel sheets and non-grain-oriented electromagnetic steel sheets. In a grain-oriented electromagnetic steel sheet, the <100> direction in the crystal arrangement is aligned in a specific direction (the rolling direction in a rolled steel sheet), and the magnetic properties in that direction are very excellent. On the other hand, in a non-grain-oriented electromagnetic steel sheet, the crystal arrangement is random in an unspecified direction, and the directionality of the magnetic properties is small.

[0003] Conventionally, 13% or 18% Cr-Fe-based stainless steel has been used as an electromagnetic valve component such as an electromagnetic fuel injection pump that requires corrosion resistance. In such an electromagnetic stainless steel, it is desirable that the magnetic properties (magnetic flux density, coercive force, etc.) are good and that the cold forging property and machinability are good from the viewpoint of processing. Here, it has been conventionally known that the magnetic properties of electromagnetic stainless steel can be improved by reducing C and N.

[0004] In order to further improve the magnetic properties of electromagnetic stainless steel and to provide an electromagnetic stainless steel having good cold forging property and machinability from the viewpoint of processing, the inventions described in Patent Documents 1 and 2 are disclosed. In Patent Document 1, the deterioration of magnetic properties due to P, C, N, etc. is suppressed by adding B. In Patent Document 2, the magnetic properties such as magnetic flux density (B80) and coercive force (Hc) are improved by making P less than 0.010%. Patent Documents 1 and 2 do not describe the directionality of electromagnetic properties.

[0005] In recent years, metal 3D printers have been expected as innovative production technologies, and various technologies have been proposed. As the main technical methods, the use of metal powder and the use of metal wire have been proposed. When using metal wire, for example, a method of forming a three-dimensional part by laminating welding beads with a metal wire has been disclosed (Patent Document 3). In addition, a manufacturing method of controlling the arc or plasma to weld a stainless steel metal wire and laminating it three-dimensionally has been disclosed (Patent Document 4).

[0006] Patent Document 5 discloses an invention that can exhibit the effects of excellent thermal deformation resistance, internal crack resistance, material and metal structure uniformity, stress corrosion cracking resistance in the molding of a metal 3D printer, and can improve the reliability of parts and significantly reduce costs by using a ferrite stainless steel wire containing Cr, Mo, and W as a metal wire for welding deposition forming by a metal 3D printer.

Prior Art Documents

Patent Documents

[0007]

Patent Document 1

Patent Document 2

Patent Document 3

Patent Document 4

Patent Document 5

Summary of the Invention

Problems to be Solved by the Invention

[0008] An object of the present invention is to provide a directionally electromagnetic stainless steel excellent in soft magnetic properties, in which the <100> directions are aligned in a specific direction, and electromagnetic components.

Means for Solving the Problems

[0009] That is, the gist of the present invention is as follows. [1] The chemical composition is, by mass%, C: 0.001 to 0.030%, Si: 0.01 to 4.00%, Mn: 0.01 to 2.00%, Ni: 0.01 to 4.00%, Cr: 6.0 to 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.050%, Ti: 0 to 2.00%, Nb: 0 to 2.00%, V: 0 to 2.0%, B: 0 to 0.1%, Al: 0 to 7.000%, W: 0 to 3.0%, Ga: 0 to 0.05%, Co: 0 to 2.5%, Sn: 0 to 2.5%, Sb: 0 to 2.5%, Ta: 0 to 2.5%, Ca: 0 to 0.05%, Mg: 0 to 0.012%, Zr: 0 to 0.012%, REM: 0 to 0.05%, Pb: 0 to 0.30%, Se: 0 to 0.80%, Te: 0 to 0.30%, Bi: 0 to 0.50%, S: 0 to 0.50%, P: 0 to 0.30%, the balance: Fe and impurities, comprising a plurality of layers laminated, a directionally electromagnetic stainless steel having an area ratio of crystals of 0.70 or more, wherein an angular difference between a lamination direction of the layers and a crystal <100> orientation is 20° or less. [2] The chemical composition further comprises, by mass%, Ti: 0.001 to 2.00%, Nb: 0.001 to 2.00%, V: 0.001 to 2.0%, B: 0.0001 to 0.1%, Al: 0.001 to 7.000%, W: 0.05 to 3.0%, Ga: 0.0004 to 0.05%, Co: 0.05 to 2.5%, Sn: 0.01 to 2.5%, Sb: 0.01 to 2.5%, and Ta: 0.01 to 2.5%, and contains one or more selected therefrom, the directionally electromagnetic stainless steel according to [1]. [3] The chemical composition further comprises, by mass%, Ca: 0.0002 to 0.05%, Mg: 0.0002 to 0.012%, Zr: 0.0002 to 0.012%, and REM: 0.0002 to 0.05%, and contains one or more selected therefrom, the directionally electromagnetic stainless steel according to [1] or [2]. [4] The chemical composition further comprises, by mass%, The directionally electromagnetic stainless steel according to any one of [1] to [3], containing one or more selected from Pb: 0.0001 to 0.30%, Se: 0.0001 to 0.80%, Te: 0.0001 to 0.30%, Bi: 0.0001 to 0.50%, S: 0.0001 to 0.50%, P: 0.0001 to 0.30%. An electromagnetic component made of the directionally electromagnetic stainless steel according to any one of [1] to [4].

[0010] [6] The chemical composition is in mass%. C: 0.001 to 0.030%, Si: 0.01 to 4.00%, Mn: 0.01 to 2.00%, Ni: 0.01 to 4.00%, Cr: 6.0 to 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.050%. Ti: 0 to 2.00%, Nb: 0 to 2.00%, V: 0 to 2.0%, B: 0 to 0.1%, Al: 0 to 7.000%, W: 0 to 3.0%, Ga: 0 to 0.05%, Co: 0 to 2.5%, Sn: 0 to 2.5%, Sb: 0 to 2.5%, Ta: 0 to 2.5%, Ca: 0 to 0.05%, Mg: 0 to 0.012%, Zr: 0 to 0.012%, REM: 0 to 0.05%, Pb: 0 to 0.30%, Se: 0 to 0.80%, Te: 0 to 0.30%, Bi: 0 to 0.50%, S: 0 to 0.50%, P: 0 to 0.30%. An electromagnetic component made of a directionally electromagnetic stainless steel, the balance being Fe and impurities. An electromagnetic component in which the area ratio of crystals with an angle difference of 20° or less between the direction of the applied magnetic field (hereinafter referred to as the "planned applied magnetic field direction") when used as an electromagnetic component and the crystal <100> orientation is 0.70 or more. [7] The chemical composition is further in mass%. The electromagnetic component according to [6], containing one or more selected from Ti: 0.001 to 2.00%, Nb: 0.001 to 2.00%, V: 0.001 to 2.0%, B: 0.0001 to 0.1%, Al: 0.001 to 7.000%, W: 0.05 to 3.0%, Ga: 0.0004 to 0.05%, Co: 0.05 to 2.5%, Sn: 0.01 to 2.5%, Sb: 0.01 to 2.5%, and Ta: 0.01 to 2.5%. [8] The chemical composition further includes, in mass percentage, Ca: 0.0002 to 0.05%, Mg: 0.0002 to 0.012%, Zr: 0.0002 to 0.012%, and REM: 0.0002 to 0.05%, containing one or more selected therefrom, the electromagnetic component according to [6] or [7]. [9] The chemical composition further includes, in mass percentage, Pb: 0.0001 to 0.30%, Se: 0.0001 to 0.80%, Te: 0.0001 to 0.30%, Bi: 0.0001 to 0.50%, S: 0.0001 to 0.50%, P: 0.0001 to 0.30%, containing one or more selected therefrom, the electromagnetic component according to any one of [6] to [8].

[10] The electromagnetic component according to any one of [6] to [9], which is manufactured by additive manufacturing.

Advantages of the Invention

[0011] The directional electromagnetic stainless steel and the electromagnetic component of the present invention can achieve excellent soft magnetic properties because the area ratio of the crystals with an angle difference of 20° or less between the lamination direction or the planned applied magnetic field direction and the crystal <100> orientation is 0.70 or more.

Brief Description of the Drawings

[0012]

Figure 1

Embodiments for Carrying Out the Invention

[0013] As described in Patent Document 5, additive manufacturing by welding and laminating was performed using a metal 3D printer using a metal wire. Using the MIG arc welder of a robot, with the welding material of a stainless steel wire, while continuously laminating in a spiral shape and repeatedly welding, it was laminated in the lamination direction 12 shown in FIG. 1, and three-dimensional modeling was performed to manufacture a laminated structure 1 composed of a hollow cylinder as shown in FIG. 1.

[0014] Here, the "lamination direction 12" in welding deposition forming is defined. In the coordinate system fixed to the formed product, the moving direction of the welding machine is the welding direction 11, and the weld beads 3 are linearly arranged in the welding direction 11 to form a layer 6. Welding is repeatedly performed on the already welded linear layer 6 (weld beads 3). In the case shown in FIG. 1, new weld beads 3 are formed on the previously welded weld beads 3. By sequentially repeating this, a laminated structure in which the layers 6 (weld beads 3) are stacked is formed. Here, the direction in which the layers 6 (weld beads 3) are sequentially stacked is called the "lamination direction 12". The laminated structure 1 is usually formed in a "plane" shape, and this plane is called the "lamination plane 4" here. In the example shown in FIG. 1, the lamination plane 4 forms a cylindrical surface. Both the welding direction 11 and the lamination direction 12 are parallel to the lamination plane 4, and the lamination direction 12 is orthogonal to the welding direction 11.

[0015] In welding deposition forming, the components of the stainless steel wire as the welding material were variously changed, the types of the substrate 2 serving as the base for the first layer of lamination were variously changed, and further the welding speed of welding was variously changed. After the forming was completed, the crystal orientation of the metal crystals in the formed product was evaluated, and in particular, the orientation of the crystals in the lamination direction 12 was evaluated.

[0016] As a result of the welding deposition forming test, when a stainless steel wire was used as the welding material, a substrate with high cooling capacity was used as the substrate 2, and the welding speed was within a specific range, it was found that the area ratio of the crystals with an angular difference of 20° or less between the lamination direction 12 and the crystal <100> orientation increased to 0.70 or more, and the orientation of the crystal <100> orientation in the lamination direction 12 was improved. As a result, it was confirmed that extremely excellent magnetic properties were possessed in the lamination direction 12. This will be described in detail below.

[0017] Using a metal 3D printer that uses a metal wire, welding deposition forming was performed. Using the MIG arc welder of a robot, with a welding material of stainless steel wire, continuously laminating in a spiral shape and repeatedly welding while laminating in the lamination direction 12 shown in Fig. 1, three-dimensional forming was carried out, and a laminated structure 1 composed of a hollow cylinder as shown in Fig. 1 was manufactured. A wire rod with a diameter of 1 mm having the component composition shown in Table 1 was used as the welding material. The cylindrical laminated structure 1 formed by laminated forming has an outer diameter of φ100 mm, a height of 80 mm, and a thickness of 8 mm. The welding speed (torch scanning speed) was changed in the range of 0.1 m / min to 30 m / min. The height of the weld deposit 3 per layer was about 5 mm.

[0018] As the substrate 2 for performing laminated forming, two types were used: a stainless steel thick plate (10 mm thick) (intensive cooling substrate) and a stainless steel thin plate (0.5 mm thick) (slow cooling substrate).

[0019] From the cylinder formed by forming, a sample with a circumference of 10 mm, a full height in the height direction (80 mm), and a full thickness in the thickness direction (8 mm) was cut out. Using the cut-out sample, crystal orientation measurement and evaluation of soft magnetic properties were performed.

[0020] Regarding the crystal orientation, EBSD (Electron Back-Scattering Deflection Pattern) evaluation was performed on the inspection surface parallel to the cylindrical surface at the central position in the height direction and the central position in the thickness direction of the sample. The crystal orientation was evaluated in the range of 2.7 mm in the circumferential direction and 8.0 mm in the height direction. The area ratio of the crystals with an angle difference of 20° or less between the lamination direction and the crystal <100> orientation is called the "lamination direction / / <100> fraction" (-).

[0021] Regarding the soft magnetic properties, using the above cut-out sample, evaluation was performed with the magnetic flux density (T) (B50) when a magnetizing force of 50 Oe (3979 A / m) with the magnetization direction facing the lamination direction 12 was applied.

[0022] As a result, when a rapid-cooling substrate was used as the substrate 2 and the welding speed was set to 20 m / min or less, the <100> fraction in the stacking direction became as large as 0.70 (-) or more, and at the same time, good soft magnetic properties with a B50 of 1.4 T or more were obtained. For the laminated products manufactured under the same conditions, the <100> fraction in the stacking direction similar to that at the central position in the height direction was obtained also at the positions of the lowermost end and the uppermost end after lamination. It is more preferable that the soft magnetic property (B50) is 1.5 T or more.

[0023] From the above phenomena, it is presumed that crystal growth occurs as follows. That is, when a rapid-cooling substrate is used as the substrate 2 and the welding speed is set to 20 m / min or less, first, when the weld deposit 3 of the first layer in contact with the substrate 2 is laminated, the direction of solidification becomes the stacking direction 12 due to the rapid cooling by the substrate 2, whereby the <100> fraction in the stacking direction of the first layer becomes a high value. When the second layer is laminated on the first layer, the crystal orientation of the first layer is inherited by the second layer as it is. It is presumed that crystal growth similar to epitaxial growth occurs. As a result, it is presumed that the <100> fraction in the stacking direction becomes a high value. The welding speed is preferably 0.5 m / min or more and 20 m / min or less. More preferably, it is 1.0 m / min or more and 10 m / min or less.

[0024] The stainless steel of the present invention has a <100> fraction in the stacking direction of 0.70 or more, and since the <100> magnetization easy direction is aligned in the stacking direction, it has excellent magnetic properties in the stacking direction 12 and can be called a directional electromagnetic steel. It is more preferable that the <100> fraction in the stacking direction is 0.90 or more.

[0025] Further, an electromagnetic component made of the above-described directional electromagnetic stainless steel can be made into an electromagnetic component in which the area ratio of crystals having an angle difference of 20° or less between the direction of the applied magnetic field (planned applied magnetic field direction) when used as an electromagnetic component and the stacking direction 12 and the crystal <100> orientation is 0.70 or more by aligning the stacking direction 12 with the planned applied magnetic field direction.

[0026] In the laminated structure 1, regarding the lamination interface 5, after mirror-polishing and etching the longitudinal section, it can be confirmed as a black contrast with an optical microscope.

[0027] The component composition of the directional electromagnetic steel of the present invention will be described. % means mass %. First, the essential components will be described.

[0028] C and N are to stably obtain a ferrite single phase during welding and lamination to homogenize the material, and to suppress the precipitation of Cr carbonitrides at the grain boundaries to prevent sensitization and stress corrosion cracking and ensure soft magnetic properties. Therefore, C is limited to 0.030% or less and N is limited to 0.050% or less. The lower limit is 0.001%.

[0029] Si is effective for improving soft magnetic properties and deoxidation during welding. However, if added excessively, it promotes the precipitation of Cr carbonitrides at the ferrite grain boundaries during repeated welding, heating, and cooling processes, resulting in sensitization and stress corrosion cracking, and the soft magnetic properties also deteriorate. Therefore, it is limited to 4.00% or less. Preferably, it is 0.01% or more and 1.5% or less.

[0030] Mn is effective for deoxidation during welding. However, if added excessively, austenite or martensite structures are generated during repeated welding, heating, and cooling processes, and a stable ferrite single-phase structure cannot be obtained. This not only impairs the material uniformity but also deteriorates the stress corrosion cracking resistance and soft magnetic properties. Therefore, it is limited to 2.00% or less. Preferably, it is 0.01% or more and 1.5% or less.

[0031] Ni is effective for improving the toughness of the ferrite phase. However, if added excessively exceeding 4.00%, austenite or martensite structures are generated during repeated welding, heating, and cooling processes, and a stable ferrite single-phase structure cannot be obtained. This not only impairs the material uniformity but also deteriorates the stress corrosion cracking resistance and soft magnetic properties. Therefore, it is limited to 4.00% or less. Preferably, it is 0.01% or more and 1.5% or less.

[0032] Cr is added in an amount of 6.0% or more to stably obtain a single-phase ferrite and ensure heat resistance (heat distortion resistance) and corrosion resistance (durability) by solid solution in the matrix. However, when added in excess of 35.0%, intermetallic compounds are formed during repeated welding, heating, and cooling processes, resulting in deterioration of material uniformity, intergranular corrosion resistance, stress corrosion cracking resistance, and soft magnetic properties. Therefore, the upper limit is limited to 35.0%. Preferably, it is 12.0 - 25.0%.

[0033] Mo is added in an amount of 0.01% or more to ensure heat resistance (heat distortion resistance) by solid solution in the matrix. However, when added in excess of 5.00%, the toughness of the ferrite phase deteriorates and internal cracks occur. Also, the soft magnetic properties deteriorate. Therefore, the upper limit is limited to 5.00%.

[0034] Cu is an effective element for improving the toughness of the matrix and is added in an amount of 0.01% or more. On the other hand, when added in excess of 2.00%, austenite or martensite structures are formed during repeated welding, heating, and cooling processes, and a single-phase ferrite structure cannot be stably obtained, not only impairing the material uniformity but also deteriorating the stress corrosion cracking resistance. Also, the soft magnetic properties deteriorate. Therefore, it is limited to 2.00% or less. Preferably, it is 1.0% or less.

[0035] The metal wire of the present invention preferably contains the following components selectively.

[0036] Nb, Ti, and V are added to suppress the precipitation of Cr carbonitrides at ferrite grain boundaries during repeated welding, heating, and cooling processes to prevent sensitization and stress corrosion cracking. Also, they fix the dissolved C and N and improve the soft magnetic properties. However, when added in excess of 2.00% each, the toughness of the ferrite phase deteriorates and internal cracks occur. Also, the soft magnetic properties deteriorate. Therefore, the upper limit is limited to 2.00% each. Preferably, each is 0.001% or more and 1.50%.

[0037] B may be added as necessary to improve the soft magnetic properties and the toughness of the matrix. However, if the content of B exceeds 0.1%, internal cracks are likely to occur, and the soft magnetic properties will deteriorate. Therefore, the upper limit of B is limited to 0.1%. Preferably, it is 0.0001% or more.

[0038] Al is effective for soft magnetic properties and heat resistance, and is also effective for deoxidation during welding. However, if added excessively, the toughness of the ferrite phase will deteriorate, and internal cracks are likely to occur. Also, the soft magnetic properties will deteriorate. Therefore, the upper limit is set to 7.000%. Preferably, it is 0.001 - 2.500%.

[0039] W is added to ensure heat resistance (heat deformation resistance) by dissolving in the matrix. However, if added in excess of 3.0%, the toughness of the ferrite phase will deteriorate and internal cracks will occur. Also, the soft magnetic properties will deteriorate. Therefore, the upper limit is limited to 3.0%. Preferably, it is 0.05 - 3.0%.

[0040] Ga may be contained as necessary because it has the effect of improving corrosion resistance. However, if Ga is contained in excess, the hot workability will decrease. The upper limit is set to 0.05%. Preferably, it is 0.0004% or more.

[0041] Co may be added as necessary to improve the soft magnetic properties and the toughness of the matrix. However, if the content of Co exceeds 2.5%, martensite structure or austenite structure will be generated in the repeated welding, heating, and cooling processes, and not only the material uniformity of obtaining a single - phase ferrite structure will deteriorate but also the stress corrosion cracking resistance will decrease. Also, the soft magnetic properties will deteriorate. Therefore, the upper limit of Co is set to 2.5%. Preferably, it is 0.05% or more.

[0042] Sn and Sb may be added as necessary to improve the corrosion resistance of the matrix. However, if each is added in excess of 2.5%, internal cracks are likely to occur and the soft magnetic properties deteriorate. Therefore, the upper limit is set at 2.5%. Preferably, it is 0.01% or more.

[0043] Ta may be added as necessary to form fine precipitates in the matrix in repeated welding, heating, and cooling processes to enhance the heat resistance (heat deformation resistance). However, if added in excess of 2.5%, coarse precipitates are formed, promoting internal cracks and deteriorating the soft magnetic properties. Therefore, the upper limit is set at 2.5%. Preferably, it is 0.01% or more.

[0044] Ca, Mg, and REM may be added as necessary as they are effective for deoxidation during welding. However, if added in excess, coarse oxides are formed in repeated welding processes, making internal cracks more likely to occur and deteriorating the soft magnetic properties. Therefore, Ca and REM are each limited to 0.05% or less, and Mg is limited to 0.012% or less. Preferably, they are each 0.0002% or more.

[0045] Zr may be added as necessary to form fine precipitates in the matrix in repeated welding, heating, and cooling processes to enhance the heat resistance (heat deformation resistance). However, if added in excess of 0.012%, coarse precipitates are formed, promoting internal cracks and deteriorating the soft magnetic properties. Therefore, the upper limit is set at 0.012%. Preferably, it is 0.0002% or more.

[0046] Pb, Se, Te, and Bi may be added as necessary to impart machinability after 3D shaping. However, if Pb contains more than 0.30%, Se contains more than 0.80%, Te contains more than 0.30%, and Bi contains more than 0.50%, internal cracks are promoted and the soft magnetic properties deteriorate. Therefore, the upper limits are 0.30% for Pb, 0.80% for Se, 0.30% for Te, and 0.50% for Bi. Preferably, they are each 0.0001% or more.

[0047] S may be added as necessary to impart machinability after 3D printing. However, if the content exceeds 0.50%, internal cracks are likely to occur, and the soft magnetic properties will deteriorate. Therefore, the upper limit is set at 0.50%. The lower the content of S, the better, and no lower limit is set.

[0048] P is limited to 0.30% or less to suppress internal cracks, stress corrosion cracking, and deterioration of soft magnetic properties during welding. Preferably, it is 0.05% or less. The lower the content of P, the better, and no lower limit is set.

[0049] The component composition of the metal wire of the present invention is composed of a chemical composition consisting of Fe and impurities, except for the elements described above.

[0050] Typical inevitable impurities include Ge, Na, Be, F, Ga, etc. Usually, they may be mixed in the range of 0.01% or less as inevitable impurities in the steel manufacturing process.

Examples

[0051] (Example 1) Steel with the chemical compositions shown in Tables 1 and 2 was melted in a 45 kg vacuum melting furnace and processed into a steel bar with a diameter of 11 mm by hot forging and hot extrusion. Then, wire drawing and annealing were repeated to prototype a metal wire with a diameter of 1.0 mm. In Tables 1 and 2, the blank parts mean that they were not actively added. Also, numerical values outside the scope of the present invention are underlined.

[0052]

Table 1

[0053]

Table 2

[0054] As the substrate 2 for performing layered manufacturing, a stainless steel thick plate (10 mm thick) (forced cooling substrate) was used. Using a MIG arc welding machine of a robot, the above-prototyped metal wire was continuously and spirally laminated on the substrate 2 while repeatedly welding, and three-dimensional manufacturing was performed by laminating in the lamination direction 12 shown in Fig. 1, and a laminated structure 1 (electromagnetic component) (outer diameter: 100 mm, height: 80 mm, thickness: 8 mm) composed of a hollow cylinder as shown in Fig. 1 was manufactured. As the welding conditions by arc, a shielding gas of Ar + 3% oxygen was used, the welding current was 229 A, the arc voltage was 17.1 V, and the welding speed was 1.1 m / min.

[0055] From the cylinder formed by manufacturing, a sample with a circumference of 10 mm, the full height in the height direction (80 mm), and the full thickness in the thickness direction (8 mm) was cut out. Using the cut-out sample, crystal orientation measurement, evaluation of soft magnetic properties, and pitting potential were performed.

[0056] Regarding the crystal orientation, EBSD (Electron Back-Scattering Deflection Pattern) evaluation was performed on the inspection surface parallel to the cylinder surface at the central position in the height direction and the central position in the thickness direction of the sample. The evaluation conditions were the same as those described above. When the <100> fraction in the lamination direction / / was 0.90 or more, it was regarded as particularly good (◎), when it was 0.70 or more and less than 0.90, it was regarded as good (○), and otherwise it was regarded as × (unqualified).

[0057] Regarding the soft magnetic properties, using the above-cut-out sample, evaluation was performed by the magnetic flux density (T) (B50) when a magnetizing force of 50 Oe with the magnetization direction facing the lamination direction was applied. When B50 was 1.5 T or more, it was regarded as particularly good (◎), when it was 1.4 T or more and less than 1.5 T, it was regarded as good (○), and otherwise it was regarded as × (unqualified). Regarding the pitting potential, measurement was performed in accordance with JIS G0577. When the pitting potential was 50 mV or more, it was regarded as good (○), and otherwise it was regarded as ×.

[0058] The evaluation results are shown in Tables 3 and 4. Table 1 and Table 3 are examples of the present invention. The component composition is within the scope of the present invention, and both the stacking direction / / <100> fraction and B50 showed good results. In Examples 14 to 20 of the present invention, both the stacking direction / / <100> fraction and B50 were ◎, indicating particularly good performance. On the other hand, Table 2 and Table 4 are comparative examples. The component composition is outside the scope of the present invention, and both the stacking direction / / <100> fraction and B50 failed (×).

[0059]

Table 3

[0060]

Table 4

[0061] (Example 2) When manufacturing the laminated structure 1 with the shape shown in FIG. 1, wires of the components shown in the steel type P in Table 1 of Example 1 were used. As the cooling substrate, a rapidly cooled substrate (stainless steel thick plate (thickness 10 mm)) and a slowly cooled substrate (stainless steel thin plate (thickness 0.5 mm)) were used, and laminated manufacturing was performed at the welding speeds shown in Table 5.

[0062]

Table 5

[0063] The results are shown in Table 5. For Nos. 55 to 60 of the present invention, when using a strong example substrate and the welding speed being within the suitable range, both the stacking direction / / <100> fraction and B50 were good. In particular, for Nos. 57 to 60, the welding speed was within a particularly suitable range, and both the stacking direction / / <100> fraction and B50 were ◎. On the other hand, for Comparative Examples Nos. 61 and 62, the welding speed was outside the suitable range of the present invention. For Nos. 63 to 66, since the cooling substrate was a slowly cooled substrate, both the stacking direction / / <100> fraction and B50 were ×.

[0064] (Example 3) Here, a comparison of the evaluation results of the crystal orientation characteristics and soft magnetic properties (B50) of shaped objects according to different manufacturing methods is carried out. As the material, stainless steel with the component composition shown in steel type S in Table 1 above is used in all cases. For the laminated shaped product, when manufacturing the laminated structure 1 with the shape shown in FIG. 1, two types of welding speeds (torch scanning speeds) were used, 5 m / min and 1 m / min, and two types of substrates 2 were used, a stainless steel thick plate (10 mm) (intensively cooled substrate) and a stainless steel thin plate (0.5 mm) (slowly cooled substrate). For the forged product, it was forged into a cylindrical shape with a diameter of 100 mm and a height of 80 mm, and then cut to have a cylindrical shape with a thickness of 8 mm. For the wire, a wire with a diameter of 10 mm was manufactured by wire rolling. For both the laminated shaped product and the forged product, the orientation evaluation direction of the crystal orientation ("<100> fraction" in Table 6) and the magnetization direction during B50 evaluation were both in the direction of the central axis of the cylinder (coinciding with the lamination direction 12 for the laminated shaped product), and for the wire, it was in the longitudinal direction of the wire.

[0065]

Table 6

[0066] The results are shown in Table 6. As is clear from Table 6, for the laminated structure 1 formed by laminated shaping, when an intensively cooled substrate was used as the substrate 2 and the welding speed was 20 m / min or less (the conditions of the present invention), the <100> fraction in the lamination direction was ○ or ◎, and at the same time, good soft magnetic properties with ○ or ◎ for the soft magnetic properties (B50) could be obtained. When the laminated shaping conditions deviated from the above-mentioned conditions of the present invention, in the case of the forged product and the case of the wire, in both cases, compared with the above-mentioned conditions of the present invention, both the <100> fraction and B50 were inferior to those of the laminated shaped product manufactured under the conditions of the present invention.

Explanation of Reference Signs

[0067] 1 Laminated Structure 2 Substrate 3 Weld Deposit 4 Lamination Plane 5 Lamination Interface 6 Layer 11 Welding Direction 12 Lamination Direction

Claims

1. A welded laminate of a plurality of layers, wherein the chemical composition of the layer is, by mass%, C: 0.001 to 0.030%, Si: 0.01 to 4.00%, Mn: 0.01 to 2.00%, Ni: 0.01 to 4.00%, Cr: 6.0 to 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.050%, Ti: 0 to 2.00%, Nb: 0 to 2.00%, V: 0 to 2.0%, B: 0 to 0.1%, Al: 0 to 7.000%, W: 0 to 3.0%, Ga: 0 to 0.05%, Co: 0 to 2.5%, Sn: 0 to 2.5%, Sb: 0 to 2.5%, Ta: 0 to 2.5%, Ca: 0 to 0.05%, Mg: 0 to 0.012%, Zr: 0 to 0.012%, REM: 0 to 0.05%, Pb: 0 to 0.30%, Se: 0 to 0.80%, Te: 0 to 0.30%, Bi: 0 to 0.50%, S: 0 to 0.50%, P: 0 to 0.30%, the balance being Fe and impurities, and a directionally electromagnetic stainless steel welded laminate structure in which the area ratio of crystals with an angular difference of 20° or less between the lamination direction of the layer and the <100> crystal orientation is 0.70 or more.

2. The chemical composition further comprises, by mass%, Ti: 0.001 to 2.00%, Nb: 0.001 to 2.00%, V: 0.001 to 2.0%, B: 0.0001 to 0.1%, Al: 0.001 to 7.000%, W: 0.05 to 3.0%, Ga: 0.0004 to 0.05%, Co: 0.05 to 2.5%, Sn: 0.01 to 2.5%, Sb: 0.01 to 2.5%, and Ta: 0.01 to 2.5%, containing one or more selected from the directionally electromagnetic stainless steel welded laminate structure according to Claim 1.

3. The chemical composition further comprises, by mass%, Ca: 0.0002 to 0.05%, Mg: 0.0002 to 0.012%, Zr: 0.0002 to 0.012%, and REM: 0.0002 to 0.05%, containing one or more selected from the directionally electromagnetic stainless steel welded laminate structure according to Claim 1 or Claim 2.

4. The chemical composition further comprises, by mass%, Pb: 0.0001 to 0.30%, Se: 0.0001 to 0.80%, Te: 0.0001 to 0.30%, Bi: 0.0001 to 0.50%, S: 0.0001 to 0.50%, P: 0.0001 to 0.30%, containing one or more selected from the directionally electromagnetic stainless steel welded laminate structure according to any one of Claims 1 to 3.

5. An electromagnetic component using the directional electromagnetic stainless steel welded and laminated structure according to any one of claims 1 to 4.

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