JP2022140960A - Grain-oriented electromagnetic stainless steel and electromagnetic component - Google Patents

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

The present invention relates to grain-oriented electromagnetic stainless steel and electromagnetic components.

Electromagnetic steel (magnetic steel sheets and magnetic steel bars) is widely used as iron core materials for electrical equipment. Electrical steel sheets are broadly classified into grain-oriented electrical steel sheets and non-oriented electrical steel sheets. A grain-oriented electrical steel sheet has a <100> direction aligned in a specific direction (the rolling direction in a rolled steel sheet) in the crystal arrangement, and has extremely excellent magnetic properties in that direction. On the other hand, a non-oriented electrical steel sheet has a random crystal orientation in an unspecified direction, and has little directionality in magnetic properties.

Conventionally, 13% or 18% Cr--Fe stainless steel is used as electromagnetic valve parts for electromagnetic fuel injection pumps, etc., which require corrosion resistance. Such an electromagnetic stainless steel preferably has good magnetic properties (magnetic flux density, coercive force, etc.) and good cold forgeability and machinability in terms of workability. Here, it is conventionally known that the magnetic properties of electromagnetic stainless steel can be improved by reducing C and N.

The inventions described in Patent Documents 1 and 2 are disclosed for the purpose of providing an electromagnetic stainless steel having better cold forgeability and machinability in terms of workability while further improving the magnetic properties of the electromagnetic stainless steel. there is In Patent Document 1, the addition of B suppresses deterioration of magnetic properties due to P, C, N, and the like. In Patent Document 2, magnetic properties such as magnetic flux density (B80) and coercive force (Hc) are improved by setting P to less than 0.010%. Patent Documents 1 and 2 do not describe the directionality of electromagnetic characteristics.

In recent years, metal 3D printers are expected to be an innovative production technology, and various technologies have been proposed. A case of using metal powder and a case of using metal wire have been proposed as main technical methods. In the case of using a metal wire, for example, a method of forming a three-dimensional part by laminating welding beads of the metal wire is disclosed (Patent Document 3). Moreover, a manufacturing method is disclosed in which metal wires of stainless steel are welded by controlling an arc or plasma and laminated three-dimensionally (Patent Document 4).

In Patent Document 5, by using a ferritic stainless steel wire containing Cr, Mo, and W as a metal wire for welding additive manufacturing by a metal 3D printer, in molding of a metal 3D printer, thermal deformation, internal crack resistance, An invention has been disclosed that is excellent in material/metallographic uniformity and resistance to stress corrosion cracking, and can exhibit the effect of improving the reliability of parts and significantly reducing costs.

JP-A-6-49605 JP-A-6-49606 JP 2003-266174 A JP 2018-507317 A JP 2020-158842 A

An object of the present invention is to provide a grain-oriented electromagnetic stainless steel having excellent soft magnetic properties, in which the <100> directions are aligned in a specific direction, and an electromagnetic component.

That is, the gist of the present invention is as follows.
[1] The chemical composition is % by mass,
C: 0.001-0.030%, Si: 0.01-4.00%, Mn: 0.01-2.00%, Ni: 0.01-4.00%, Cr: 6.0- 35.0%, Mo: 0.01-5.00%, Cu: 0.01-2.00%, N: 0.001-0.050%,
Ti: 0-2.00%, Nb: 0-2.00%, V: 0-2.0%, B: 0-0.1%, Al: 0-7.000%, W: 0-3 .0%, Ga: 0-0.05%, Co: 0-2.5%, Sn: 0-2.5%, Sb: 0-2.5%, Ta: 0-2.5%, Ca : 0-0.05%, Mg: 0-0.012%, Zr: 0-0.012%, REM: 0-0.05%, Pb: 0-0.30%, Se: 0-0. 80%, Te: 0-0.30%, Bi: 0-0.50%, S: 0-0.50%, P: 0-0.30%,
balance: Fe and impurities,
Multiple layers are laminated,
A grain-oriented electromagnetic stainless steel having an area ratio of 0.70 or more for crystals having an angular difference of 20° or less between the stacking direction of the layers and the crystal <100> orientation.
[2] The chemical composition is further, in mass %,
Ti: 0.001-2.00%, Nb: 0.001-2.00%, V: 0.001-2.0%, B: 0.0001-0.1%, Al: 0.001- 7.000%, W: 0.05-3.0%, Ga: 0.0004-0.05%, Co: 0.05-2.5%, Sn: 0.01-2.5%, Sb : 0.01 to 2.5%, and Ta: 0.01 to 2.5%.
[3] Further, the chemical composition is % by mass,
One selected from 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% The grain-oriented electromagnetic stainless steel according to [1] or [2], containing the above.
[4] The chemical composition is further, in mass%,
Pb: 0.0001-0.30%, Se: 0.0001-0.80%, Te: 0.0001-0.30%, Bi: 0.0001-0.50%, S: 0.0001- The grain-oriented electromagnetic stainless steel according to any one of [1]1 to [3], containing one or more selected from 0.50% and P: 0.0001 to 0.30%.
[5] An electromagnetic component using the grain-oriented electromagnetic stainless steel according to any one of [1] to [4].

[6] The chemical composition is mass %,
C: 0.001-0.030%, Si: 0.01-4.00%, Mn: 0.01-2.00%, Ni: 0.01-4.00%, Cr: 6.0- 35.0%, Mo: 0.01-5.00%, Cu: 0.01-2.00%, N: 0.001-0.050%,
Ti: 0-2.00%, Nb: 0-2.00%, V: 0-2.0%, B: 0-0.1%, Al: 0-7.000%, W: 0-3 .0%, Ga: 0-0.05%, Co: 0-2.5%, Sn: 0-2.5%, Sb: 0-2.5%, Ta: 0-2.5%, Ca : 0-0.05%, Mg: 0-0.012%, Zr: 0-0.012%, REM: 0-0.05%, Pb: 0-0.30%, Se: 0-0. 80%, Te: 0-0.30%, Bi: 0-0.50%, S: 0-0.50%, P: 0-0.30%,
Balance: An electromagnetic component made of grain-oriented electromagnetic stainless steel as Fe and impurities,
1. An electromagnetic component having a crystal area ratio of 0.70 or more in which the angular difference between the direction of the applied magnetic field (hereinafter referred to as the "intended direction of the applied magnetic field") and the <100> orientation of the crystal is 20° or less when used as an electromagnetic component.
[7] The chemical composition is further, in mass %,
Ti: 0.001-2.00%, Nb: 0.001-2.00%, V: 0.001-2.0%, B: 0.0001-0.1%, Al: 0.001- 7.000%, W: 0.05-3.0%, Ga: 0.0004-0.05%, Co: 0.05-2.5%, Sn: 0.01-2.5%, Sb : 0.01 to 2.5%, and Ta: 0.01 to 2.5%.
[8] The chemical composition is further, in mass %,
One selected from 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% The electromagnetic component according to [6] or [7], containing the above.
[9] The chemical composition is further, in mass %,
Pb: 0.0001-0.30%, Se: 0.0001-0.80%, Te: 0.0001-0.30%, Bi: 0.0001-0.50%, S: 0.0001- The electromagnetic component according to any one of [6] to [8], containing one or more selected from 0.50% and P: 0.0001 to 0.30%.
[10] The electromagnetic component according to any one of [6] to [9] manufactured by lamination molding.

The grain-oriented electromagnetic stainless steel and electromagnetic parts of the present invention are excellent because the area ratio of the crystals in which the angle difference between the lamination direction or the planned applied magnetic field direction and the crystal <100> orientation is 20° or less is 0.70 or more. soft magnetic properties can be realized.

FIG. 10 is a diagram showing a layered structure that has been welded and laminated.

As described in Patent Literature 5, welding additive manufacturing was performed by a metal 3D printer using metal wires. Using a robot MIG arc welder, using a stainless steel wire welding material, repeatedly welding while continuously laminating in a spiral shape, and laminating in the lamination direction 12 shown in FIG. A laminated structure 1 composed of hollow cylinders as shown in FIG. 1 was manufactured.

Here, the "stacking direction 12" in the welding layered manufacturing is defined. In a coordinate system fixed to the model, the direction of movement of the welder is the deposition direction 11 and the deposits 3 are linearly arranged in the deposition direction 11 to form the layer 6 . Welding is further repeated on the already welded linear layer 6 (welded material 3). In the case shown in FIG. 1, a new weld 3 is formed on the previously welded weld 3 . By sequentially repeating this, a laminated structure in which the layers 6 (welded deposits 3) are stacked is formed. Here, the direction in which the layers 6 (welded deposits 3) are sequentially stacked is referred to as "stacking direction 12". The laminate structure 1 is usually formed in the shape of a "plane", and this plane is referred to herein as the "laminate plane 4". In the example shown in FIG. 1, the lamination surface 4 forms a cylindrical surface. Both the welding direction 11 and the stacking direction 12 are parallel to the stacking surface 4 , and the stacking direction 12 is orthogonal to the welding direction 11 .

In the welding layered manufacturing, the composition of the stainless steel wire as the welding material was varied, the type of the substrate 2 serving as the base of the first layer was varied, and the welding speed was varied. After the molding was finished, the crystal orientation of the metal crystals in the molded product was evaluated, and in particular, the orientation of the crystals in the stacking direction 12 was evaluated.

As a result of the welding additive manufacturing test, when a stainless steel wire is used as the welding material, a substrate with a high cooling capacity is used as the substrate 2, and the welding speed is within a specific range, the angle difference between the lamination direction 12 and the crystal <100> orientation is It has been found that the area ratio of the crystals having the angle of 20° or less increases to 0.70 or more, and the orientation of the crystal <100> orientation in the stacking direction 12 is improved. As a result, it was confirmed that the magnetic properties in the lamination direction 12 were extremely excellent. Details will be described below.

Welding additive manufacturing was performed by a metal 3D printer using metal wires. Using a robot MIG arc welder, using a stainless steel wire welding material, repeatedly welding while continuously laminating in a spiral shape, and laminating in the lamination direction 12 shown in FIG. A laminated structure 1 composed of hollow cylinders as shown in FIG. 1 was manufactured. A wire having a diameter of 1 mm and having the composition shown in Table 1 was used as a welding material. A cylindrical laminated structure 1 formed by lamination molding 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 varied in the range of 0.1 m/min to 30 m/min. The height of the welded material 3 per layer was about 5 mm.

As the substrate 2 for lamination molding, two types of thick stainless steel plate (10 mm thick) (strongly cooled substrate) and thin stainless steel plate (0.5 mm thick) (slowly cooled substrate) were used.

A sample of 10 mm in the circumferential direction, total height (80 mm) in the height direction, and total thickness (8 mm) in the thickness direction was cut out from the cylinder formed by molding. Crystal orientation measurement and evaluation of soft magnetic properties were performed using the cut sample.

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

The soft magnetic properties were evaluated by magnetic flux density (T) (B50) when a magnetizing force of 50 Oe (3979 A/m) was applied with the magnetization direction oriented in the lamination direction 12 using the cut sample.

As a result, when a hard-cooled substrate is used as the substrate 2 and the welding speed is set to 20 m/min or less, the lamination direction //<100> fraction becomes as large as 0.70 (-) or more, and at the same time the soft magnetic properties (B50 ) was 1.4 T or more, and good soft magnetic properties could be obtained. In addition, regarding the laminated product manufactured under the same conditions, the same ratio of //<100> in the lamination direction as in the center position in the height direction was obtained at the bottom and top positions after lamination. It is more preferable that the soft magnetic property (B50) is 1.5 T or more.

From the above phenomenon, it is inferred that the crystal grows as follows. That is, when a hard-cooled substrate is used as the substrate 2 and the welding speed is set to 20 m/min or less, when the first layer of deposit 3 in contact with the substrate 2 is first laminated, the hard cooling by the substrate 2 causes the direction of solidification to change. stack direction 12, which results in a high value for the stack direction//<100> fraction of the first layer. When the second layer is laminated on the first layer, the crystal orientation of the first layer is directly inherited by the second layer. It is presumed to be crystal growth similar to epitaxial growth. As a result, it is presumed that the stacking direction//<100> fraction became 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.

The stainless steel of the present invention has a lamination direction//<100> fraction of 0.70 or more, and the <100> direction of easy magnetization is aligned in the lamination direction, so it has excellent magnetic properties in the lamination direction 12. and can be called grain-oriented electrical steel. Lamination direction//<100> fraction is more preferably 0.90 or more.

In the electromagnetic component made of grain-oriented electromagnetic stainless steel, the direction of the applied magnetic field (planned applied magnetic field direction) during use as an electromagnetic component is matched with the stacking direction 12, so that the expected applied magnetic field direction and the crystal <100> orientation The electromagnetic component can have an area ratio of 0.70 or more for crystals having an angle difference of 20° or less between the two.

In the laminated structure 1, the lamination interface 5 can be confirmed as a black contrast with an optical microscope after the longitudinal section is mirror-polished and etched.

The chemical composition of the grain-oriented electrical steel of the present invention will be described. % means % by mass.
First, the essential ingredients will be explained.

C and N stably obtain a ferrite single phase at the time of welding and lamination to homogenize the material, and suppress precipitation of Cr carbonitride to grain boundaries to prevent sensitization and stress corrosion cracking. In order to secure soft magnetic properties, C is limited to 0.030% or less and N is limited to 0.050% or less. The lower limit is 0.001%.

Si is effective in improving soft magnetic properties and deoxidizing during welding. However, when excessively added, it promotes precipitation of Cr carbonitrides on ferrite grain boundaries during repeated welding, heating, and cooling processes, resulting in sensitization. stress corrosion cracking occurs, 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.

Mn is effective for deoxidizing during welding, but if it is added excessively, an austenite or martensite structure is generated in repeated welding, heating, and cooling processes, and a ferrite single-phase structure cannot be stably obtained. In addition to impairing the uniformity, the stress corrosion cracking resistance deteriorates, and the soft magnetic properties deteriorate. Therefore, it is limited to 2.00% or less. Preferably, it is 0.01% or more and 1.5% or less.

Ni is effective in improving the toughness of the ferrite phase, but if it is added in excess of 4.00%, an austenite or martensite structure is generated in repeated welding, heating, and cooling processes, and the ferrite single phase structure becomes stable. In addition to impairing the uniformity of the material, the stress corrosion cracking resistance deteriorates and the soft magnetic properties deteriorate. Therefore, it is limited to 4.00% or less. Preferably, it is 0.01% or more and 1.5% or less.

Cr is added in an amount of 6.0% or more in order to obtain a ferrite single phase stably and to ensure heat resistance (heat deformation) and corrosion resistance (durability) by dissolving in the matrix. However, if the addition exceeds 35.0%, intermetallic compounds are formed during repeated welding, heating, and cooling processes, which deteriorates material uniformity, intergranular corrosion resistance, and stress corrosion cracking resistance, and soft magnetic properties deteriorate. to degrade. Therefore, the upper limit is limited to 35.0%. Preferably, it is 12.0 to 25.0%.

Mo is added in an amount of 0.01% or more in order to ensure heat resistance (heat deformation) by dissolving in the matrix. However, if the addition exceeds 5.00%, the toughness of the ferrite phase deteriorates and internal cracks occur. Also, soft magnetic properties deteriorate. Therefore, the upper limit is limited to 5.00%.

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, if it is added in excess of 2.00%, an austenite or martensite structure is formed in repeated welding, heating, and cooling processes, and a ferrite single-phase structure cannot be stably obtained, and the homogeneity of the material is only impaired. or the stress corrosion cracking resistance deteriorates. Also, soft magnetic properties deteriorate. Therefore, it is limited to 2.00% or less. Preferably, it is 1.0% or less.

Preferably, the metal wire of the present invention selectively contains the following components.

Nb, Ti, and V are added to suppress the precipitation of Cr carbonitrides to ferrite grain boundaries in repeated welding, heating, and cooling steps, thereby preventing sensitization and stress corrosion cracking. In addition, solid solution C and N are fixed to improve the soft magnetic properties. However, if each content exceeds 2.00%, the toughness of the ferrite phase deteriorates and internal cracks occur. Also, soft magnetic properties deteriorate. Therefore, the upper limit is limited to 2.00%. Preferably, they are 0.001% or more and 1.50%, respectively.

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

Al is effective for soft magnetic properties and heat resistance, and is also effective for deoxidizing during welding. Also, soft magnetic properties deteriorate. Therefore, the upper limit is set to 7.000%. Preferably, it is 0.001 to 2.500%.

W is added in order to secure heat resistance (heat deformation) by forming a solid solution in the matrix. However, if the addition exceeds 3.0%, the toughness of the ferrite phase deteriorates and internal cracks occur. Also, soft magnetic properties deteriorate. Therefore, the upper limit is limited to 3.0%. Preferably, it is 0.05 to 3.0%.

Ga has an effect of improving corrosion resistance, so it may be contained as necessary. However, if Ga is contained excessively, the hot workability deteriorates. The upper limit is 0.05%. It is preferably 0.0004% or more.

Co may be added as necessary in order to improve the soft magnetic properties and toughness of the matrix. However, if the Co content exceeds 2.5%, a martensitic structure or an austenitic structure is generated in repeated welding, heating, and cooling steps, resulting in a ferrite single-phase structure. Corrosion cracking resistance is lowered. Also, soft magnetic properties deteriorate. Therefore, the upper limit of Co is set to 2.5%. Preferably, it is 0.05% or more.

Sn and Sb may be added as necessary in order to improve the corrosion resistance of the matrix. However, when each of these elements is added in excess of 2.5%, internal cracks tend to occur. Also, soft magnetic properties deteriorate. Therefore, the upper limit is set to 2.5%. Preferably, it is 0.01% or more.

Ta forms fine precipitates in the matrix in repeated welding, heating, and cooling steps to improve heat resistance (heat deformation resistance), so it may be added as necessary. However, when added in excess of 2.5%, coarse precipitates are formed, promoting internal cracking. Also, soft magnetic properties deteriorate. Therefore, the upper limit is set to 2.5%. Preferably, it is 0.01% or more.

Ca, Mg, and REM are effective in deoxidizing during welding, and may be added as necessary. However, if it is added excessively, coarse oxides are formed in repeated welding processes, and internal cracks are likely to occur. Also, soft magnetic properties deteriorate. Therefore, Ca and REM are each limited to 0.05% or less, and Mg is limited to 0.012% or less. Preferably, each is 0.0002% or more.

Zr forms fine precipitates in the matrix in repeated welding, heating, and cooling steps to improve heat resistance (heat deformation resistance), so that it may be added as necessary. However, if added in excess of 0.012%, it forms coarse precipitates and promotes internal cracking. Also, soft magnetic properties deteriorate. Therefore, the upper limit is set to 0.012%. Preferably, it is 0.0002% or more.

Pb, Se, Te, and Bi may be added as necessary in order to impart machinability after 3D modeling. However, when the Pb content exceeds 0.30%, the Se content exceeds 0.80%, the Te content exceeds 0.30%, and the Bi content exceeds 0.50%, internal cracks are promoted. Also, soft magnetic properties deteriorate. Therefore, the upper limits of Pb are 0.30%, Se is 0.80%, Te is 0.30%, and Bi is 0.50%. Preferably, each is 0.0001% or more.

S may be added as necessary in order to impart machinability after 3D modeling. However, if the content exceeds 0.50%, internal cracks tend to occur. Also, soft magnetic properties deteriorate. Therefore, the upper limit is set to 0.50%. S is preferably as low as possible, and there is no lower limit.

P is limited to 0.30% or less in order to suppress internal cracking and stress corrosion cracking during welding and deterioration of soft magnetic properties. Preferably, it is 0.05% or less. P is preferably as low as possible, and there is no lower limit.

The chemical composition of the metal wire of the present invention is composed of chemical components consisting of Fe and impurities other than the elements described above.

Typical unavoidable impurities include Ge, Na, Be, F, Ga, and the like, and are usually mixed in the range of 0.01% or less as unavoidable impurities in the steel manufacturing process.

(Example 1)
Steels having the chemical compositions shown in Tables 1 and 2 were melted in a 45 kg vacuum melting furnace and processed into steel bars with a diameter of 11 mm by hot forging and hot extrusion. After that, wire drawing and annealing were repeated to make a trial metal wire with a diameter of 1.0 mm. In Tables 1 and 2, blanks mean that they were not intentionally added. In addition, numerical values outside the scope of the present invention are underlined.

A thick stainless steel plate (10 mm thick) (strongly cooled substrate) is used as the substrate 2 for lamination molding, and the prototype metal wire is spirally formed on the substrate 2 using an MIG arc welding robot. Continuous lamination and repeated welding, lamination in the lamination direction 12 shown in FIG. : 100 mm, height 80 mm, thickness: 8 mm). The arc welding conditions were a welding current of 229 A, an arc voltage of 17.1 V, and a welding speed of 1.1 m/min, using a shielding gas of Ar+3% oxygen.

A sample of 10 mm in the circumferential direction, total height (80 mm) in the height direction, and total thickness (8 mm) in the thickness direction was cut out from the cylinder formed by molding. Crystal orientation measurement, soft magnetic properties and pitting potential were evaluated using the cut samples.

Regarding the crystal orientation, EBSD (Electron Back-Scattering Deflection Pattern) evaluation was performed on an inspection surface parallel to the cylindrical surface at the center position in the height direction and the center position in the thickness direction of the sample. The evaluation conditions were the same as those described above. When the lamination direction//<100> fraction was 0.90 or more, it was evaluated as particularly good.

The soft magnetic properties were evaluated by magnetic flux density (T) (B50) when a magnetizing force of 50 Oe was applied with the magnetization direction directed to the lamination direction using the above-cut sample. When the B50 was 1.5 T or more, it was evaluated as particularly good, and when it was 1.4 T or more and less than 1.5 T, it was evaluated as good.
The pitting potential was measured according to JIS G0577. A pitting potential of 50 mV or more was evaluated as good, and the others were evaluated as x.

Tables 3 and 4 show the evaluation results.
Tables 1 and 3 are examples of the present invention, the component composition was within the range of the present invention, and good results were obtained in both the stacking direction//<100> fraction and B50. In Examples 14 to 20 of the present invention, both the laminate direction//<100> fraction and B50 were ⊚ and were particularly good.
On the other hand, Tables 2 and 4 are comparative examples, and the component composition is out of the range of the present invention, and both the stacking direction//<100> fraction and B50 are disqualified (x).

(Example 2)
When manufacturing the laminate structure 1 having the shape shown in FIG. Laminate molding was performed at the welding speed shown in Table 5 using a slowly cooled substrate (stainless thin plate (thickness 0.5 mm)).

Table 5 shows the results.
Invention No. Nos. 55 to 60 used strong example substrates, the welding speed was in the preferred range, and both the lamination direction//<100> fraction and B50 were good. Especially No. In 57 to 60, the welding speed was in a particularly suitable range, and both the stacking direction//<100> fraction and B50 were ⊚.
On the other hand, Comparative Example No. Nos. 61 and 62 have welding speeds outside the preferred range of the present invention. In 63 to 66, the cooling substrate was a slow-cooling substrate, so both the stacking direction//<100> fraction and B50 were x.

(Example 3)
Here, evaluation results of the crystal orientation characteristics and the soft magnetic characteristics (B50) of the shaped objects according to the manufacturing methods are compared. As materials, stainless steels having chemical compositions shown in steel type S in Table 1 are used. Regarding the laminate-molded product, when manufacturing the laminate structure 1 having the shape shown in FIG. ) (strongly cooled substrate) and stainless thin plate (0.5 mm) (slowly cooled substrate). The forged product was forged into a cylindrical shape with a diameter of 100 mm and a height of 80 mm, and was cut into a cylindrical shape with a thickness of 8 mm. As for the wire rod, a wire rod having a diameter of 10 mm was manufactured by wire rolling. Both the orientation evaluation direction of the crystal orientation (“<100> fraction” in Table 6) and the magnetization direction at the time of B50 evaluation are in the direction of the central axis of the cylinder for laminate-molded products and forged products (for laminate-molded products, direction 12), and the longitudinal direction of the wire.

Table 6 shows the results. As is clear from Table 6, when the layered structure 1 is layered and manufactured, a hard-cooled substrate is used as the substrate 2, and the welding speed is 20 m/min or less (conditions of the present invention), the direction of stacking //<100 > fraction was ◯ or ⊚, and at the same time, the soft magnetic characteristics (B50) were ◯ or ⊚, and good soft magnetic characteristics could be obtained. If the additive manufacturing conditions deviate from the above-described conditions of the present invention, in the case of forgings, and in the case of wire rods, both the <100> fraction and B50 are manufactured under the conditions of the present invention compared to the conditions of the present invention. The result was inferior to that of the laminate-molded product.

REFERENCE SIGNS LIST 1 Laminated structure 2 Substrate 3 Welding material 4 Lamination surface 5 Lamination interface 6 Layer 11 Welding direction 12 Lamination direction

Claims (5)

The chemical composition, 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: 0-0.05%,
Co: 0-2.5%,
Sn: 0-2.5%,
Sb: 0-2.5%,
Ta: 0-2.5%,
Ca: 0-0.05%,
Mg: 0-0.012%,
Zr: 0 to 0.012%,
REM: 0-0.05%,
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%,
balance: Fe and impurities,
Multiple layers are laminated,
A grain-oriented electromagnetic stainless steel having an area ratio of 0.70 or more for crystals having an angular difference of 20° or less between the stacking direction of the layers and the crystal <100> orientation. Further, the chemical composition is, in 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: 0.05-2.5%,
Sn: 0.01 to 2.5%,
Sb: 0.01-2.5%, and Ta: 0.01-2.5%,
containing one or more selected from
The grain-oriented electromagnetic stainless steel according to claim 1. Further, the chemical composition is, in mass %,
Ca: 0.0002-0.05%,
Mg: 0.0002-0.012%,
Zr: 0.0002-0.012%, and REM: 0.0002-0.05%,
containing one or more selected from
The grain-oriented electromagnetic stainless steel according to claim 1 or 2. Further, the chemical composition is, in 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 grain-oriented electromagnetic stainless steel according to any one of claims 1 to 3. An electromagnetic component using the grain-oriented electromagnetic stainless steel according to any one of claims 1 to 4.

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