WO2022107757A1 - Stainless steel bar material and electromagnetic component - Google Patents

Stainless steel bar material and electromagnetic component Download PDF

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Publication number
WO2022107757A1
WO2022107757A1 PCT/JP2021/042062 JP2021042062W WO2022107757A1 WO 2022107757 A1 WO2022107757 A1 WO 2022107757A1 JP 2021042062 W JP2021042062 W JP 2021042062W WO 2022107757 A1 WO2022107757 A1 WO 2022107757A1
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less
content
amount
steel
rod
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PCT/JP2021/042062
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French (fr)
Japanese (ja)
Inventor
祥太 山先
光司 高野
幸寛 西田
規介 田中
雅之 東城
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日鉄ステンレス株式会社
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Priority to US18/037,694 priority Critical patent/US20240011137A1/en
Priority to CN202180077648.7A priority patent/CN116438321A/en
Priority to MX2023005833A priority patent/MX2023005833A/en
Priority to EP21894631.7A priority patent/EP4249612A1/en
Priority to KR1020237016897A priority patent/KR20230088905A/en
Priority to JP2022563763A priority patent/JPWO2022107757A1/ja
Publication of WO2022107757A1 publication Critical patent/WO2022107757A1/en

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Definitions

  • the present invention relates to electromagnetic stainless steel, particularly stainless steel rod-shaped steel having excellent high-speed cold forging property, machinability, and soft magnetic properties, and electromagnetic parts using the same.
  • Japanese Unexamined Patent Publication No. 6-49606 Japanese Unexamined Patent Publication No. 6-49605 Japanese Unexamined Patent Publication No. 3-44448
  • the present invention has been made to solve the above problems, and the gist of the present invention is the following stainless steel rod-shaped steel materials and electromagnetic parts.
  • the chemical composition is 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: 8.0 to Contains 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.030%, Al: 7,000% or less. moreover, Ti: 0 to 2.00%, Nb: 0 to 2.00%, B: 0 to 0.1000%, and so on.
  • a stainless rod-shaped steel material having an average particle size of a nitride of 10 ⁇ m or less and a solid solution N content in steel of 0.020% by mass or less.
  • the chemical composition is 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: 8.0 to Contains 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.030%, Al: 7,000% or less.
  • Ti 0 to 2.00%, Nb: 0 to 2.00%, B: 0 to 0.1000%, and so on. It contains one or more selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more.
  • Group 3 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
  • the present inventors conducted various studies in order to obtain stainless steel rod-shaped steel materials and electromagnetic parts having excellent high-speed cold forging properties, machinability, and soft magnetic properties. As a result, the following findings (a) to (c) were obtained.
  • a combination of ferritic stainless steel whose composition is adjusted with one or more of B, Ti, and Nb and a hot rolling process (finish rolling inlet temperature, finish rolling roll diameter, heat treatment temperature) to obtain the average grain size of nitrides.
  • the amount of solid melt N and the amount of solid melt B in steel can be reduced.
  • the high-speed cold forging property has a compression rate of 70%, the unbreakable strain rate is 0.1 / s or more, the machinability has a cutting resistance of 50 mm or more, and the soft magnetic property is maintained.
  • the present invention was made based on the above findings. In addition, a preferred embodiment of the present invention will be described in detail. In the following description, a preferred embodiment of the present invention will be described as the present invention. Hereinafter, each requirement of the present invention will be described in detail.
  • the "bar-shaped steel material” includes “bar steel”, “wire rod”, “steel wire”, “deformed wire”, “deformed bar steel” and the like.
  • the average particle size of the nitride is controlled. Specifically, the average particle size of the nitride is 10 ⁇ m or less. This is because when the average particle size of the nitride exceeds 10 ⁇ m, the high-speed cold forging property is deteriorated by the coarse nitride.
  • the average particle size of the nitride is more preferably 7 ⁇ m or less, and even more preferably 5 ⁇ m or less.
  • the average particle size of the nitride is preferably 0.01 ⁇ m or more.
  • the nitride includes carbonitride.
  • the average particle diameter of the nitride is the surface layer portion, the central portion, and the 1/4 depth position portion existing between the surface layer portion and the central portion in the L cross section of the rod-shaped steel material (cross section including the center line of the rod-shaped steel material).
  • the amount of solid solution N in steel is 0.020% by mass or less, or the amount of solid solution B is 0.015% by mass or less.
  • the soft magnetic properties and high-speed cold forging property are improved.
  • an invention having a suitable component composition described later and an average particle size of the above-mentioned nitride and defining the amount of solid-dissolved N in steel to be 0.020% by mass or less will be referred to as "Invention 1".
  • an invention having a suitable component composition of the present invention and the average particle size of the above-mentioned nitride and defining the amount of solid solution B in steel to be 0.015% by mass or less is referred to as "the present invention 2".
  • Amount of solid solution N in steel In the rod-shaped steel material according to the present invention 1, the amount of solid solution N in steel is controlled. Specifically, the amount of solid solution N in the steel is 0.020% by mass or less. This is because when the amount of solid solution N in the steel exceeds 0.020% by mass, the soft magnetic properties and high-speed cold forging property are deteriorated due to the lattice strain due to the solid solution N.
  • the amount of solid solution N in the steel is more preferably 0.015% by mass or less, and further preferably 0.01% by mass or less.
  • the amount of solid solution N in the steel is preferably 0.00001% by mass or more. Since the crystal structure of the steel of the present invention is ferritic steel, the amount of solid solution N in the steel corresponds to the amount of solid solution N in the ferrite phase.
  • the problem of the present invention can be solved by controlling the amount of solid solution B in the steel.
  • the amount of solid solution B in the steel is 0.015% by mass or less. This is because when the amount of the solid solution B in the steel exceeds 0.015% by mass, the soft magnetic properties and the high-speed cold forging property are deteriorated due to the lattice strain due to the solid solution B.
  • the amount of solid solution B in the steel is more preferably 0.010% by mass or less, and further preferably 0.005% by mass or less.
  • the amount of solid solution B in the steel is preferably 0.00001% by mass or more. Since the crystal structure of the steel of the present invention is ferritic steel, the amount of solid solution B in the steel corresponds to the amount of solid solution B in the ferrite phase.
  • C 0.001 to 0.030% C enhances the strength and machinability of the steel material. Therefore, the C content is set to 0.001% or more. However, if C is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability deteriorate. Therefore, the C content is set to 0.030% or less.
  • the C content is preferably 0.020% or less, more preferably 0.015% or less.
  • Si 0.01-4.00% Si is contained as a deoxidizing element to improve soft magnetic properties and machinability. Therefore, the Si content is preferably 0.01% or more, preferably 0.10% or more. However, if Si is excessively contained, high-speed cold forging property, soft magnetic property, and machinability are deteriorated. Therefore, the Si content is set to 4.00% or less. The Si content is preferably 3.00% or less, more preferably 1.50% or less.
  • Mn 0.01-2.00% Mn improves the strength, soft magnetic properties, and machinability of steel materials. Therefore, the Mn content is preferably 0.01% or more, preferably 0.05% or more. However, if Mn is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, corrosion resistance may decrease. Therefore, the Mn content is set to 2.00% or less. The Mn content is preferably 1.00% or less, and more preferably 0.50% or less.
  • Ni 0.01-4.00% Ni improves the toughness and soft magnetic properties of steel materials, high-speed cold forging, and machinability. Therefore, the Ni content is preferably 0.01% or more, preferably 0.05% or more. However, if Ni is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Ni content is set to 4.00% or less. The Ni content is preferably 3.00% or less, more preferably 1.00% or less, and even more preferably 0.50% or less.
  • Cr 8.0 to 35.0% Cr improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Cr content is set to 8.0% or more. The Cr content is preferably 10.0% or more. However, if Cr is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. The Cr content should be 35.0% or less. The Cr content is preferably 21.0% or less, more preferably 20.0% or less.
  • Mo 0.01-5.00% Mo improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Mo content is 0.01% or more. However, if Mo is excessively contained, high-speed cold forging property, soft magnetic property, and machinability are deteriorated. Therefore, the Mo content is set to 5.00% or less.
  • the Mo content is preferably 3.00% or less, more preferably 2.00% or less, and even more preferably 1.50% or less.
  • Cu 0.01-2.00%
  • the Cu content is preferably 0.01% or more, preferably 0.05% or more.
  • the Cu content is set to 2.00% or less.
  • the Cu content is preferably 1.00% or less, more preferably 0.80% or less, still more preferably 0.40% or less.
  • N 0.001 to 0.030% N improves the strength and machinability of the steel material. It is also an element that forms a nitride. Therefore, the N content is preferably 0.001% or more, preferably 0.002% or more. However, if N is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large, and the amount of solid solution N increases. Therefore, the N content is set to 0.030% or less. The N content is preferably 0.025% or less, more preferably 0.020% or less.
  • Al 7,000% or less
  • Al has the effect of promoting deoxidation and improving the cleanliness level of inclusions.
  • the addition of Al enhances soft magnetic properties, high-speed cold forging, and machinability.
  • the Al content is set to 7,000% or less.
  • the Al content is preferably 3.000% or less, more preferably 0.100% or less, and even more preferably 0.020% or less.
  • the Al content is preferably 0.001% or more.
  • the rod-shaped steel material according to the present invention contains one or more elements selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more within the following component range. Incorporate in. These elements are the main elements constituting the nitride and need to be controlled because they are related to the average particle size of the nitride and the amount of solid solution N. Of Ti, Nb, and B, the element not selected above may not be contained or may be contained within the following component range.
  • Ti 0 to 2.00% Ti has the effects of enhancing the strength, soft magnetic properties, high-speed cold forging property, and machinability of steel materials. Further, Ti forms a nitride and is related to the amount of solid solution N. Further, since carbonitride is formed, the formation of Cr carbide is suppressed and the formation of a Cr-deficient layer is suppressed. As a result, it has the effect of preventing intergranular corrosion. Therefore, the Ti content is set to 0.001% or more. However, if Ti is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the Ti content is set to 2.00% or less.
  • the Ti content is preferably 1.00% or less, more preferably 0.50% or less, further preferably 0.50% or less, and even more preferably 0.25% or less. In addition, it is preferably contained in an amount of 0.01% or more in order to exhibit the effect. More preferably, 0.05% or more. It may be 0.10% or more.
  • Nb 0 to 2.00%
  • Nb has the effect of enhancing the strength, soft magnetic properties, high-speed cold forging property, and machinability of the steel material. Further, Nb forms a nitride and is related to the amount of solid solution N. Further, since carbonitride is formed, the formation of Cr carbide is suppressed and the formation of a Cr-deficient layer is suppressed. As a result, it has the effect of preventing intergranular corrosion. Therefore, the Nb content is set to 0.001% or more. However, if Nb is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large.
  • the Nb content is set to 2.00% or less.
  • the Nb content is preferably 1.00% or less, more preferably 0.80% or less, and even more preferably 0.60% or less.
  • it is preferably contained in an amount of 0.02% or more in order to exhibit the effect. More preferably, 0.05% or more. It may be 0.10% or more.
  • B 0 to 0.1000%
  • B has the effect of enhancing the soft magnetic properties, high-speed cold forging property, and machinability of the steel material. Further, B forms a boron nitride such as BN, and is related to the amount of solid solution N and the amount of solid solution B. In particular, BN contributes to the improvement of machinability. Therefore, the B content is set to 0.0001% or more. However, if B is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the B content is set to 0.1000% or less. The B content is preferably 0.0200% or less, more preferably 0.0100% or less. Further, in order to exhibit the effect, it is preferably contained in an amount of 0.0005% or more. 0.0010% or more is more preferable. It may be 0.0020% or more.
  • the rod-shaped steel material according to the present invention contains, if necessary, one or more elements selected from Sn, V, W, Ga, Co, Sb and Ta as the elements of the first group. May be good.
  • Sn 0 to 2.50% Sn may be contained as necessary because it has the effects of improving corrosion resistance, soft magnetic properties, high-speed cold forging property, and machinability. However, if Sn is contained in an excessive amount, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness decreases due to the grain boundary segregation of Sn. Therefore, the Sn content is set to 2.50% or less.
  • the Sn content is more preferably 1.00% or less, and further preferably 0.20% or less.
  • the Sn content is preferably 0.0001% or more, and more preferably 0.05% or more.
  • V 0-2.0% Since V has an effect of improving soft magnetic properties, high-speed cold forging property, and machinability, it may be contained as necessary. However, if V is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse carbonitride. Therefore, the V content is set to 2.0% or less. The V content is preferably 1.0% or less, more preferably 0.5% or less, and even more preferably 0.1% or less. On the other hand, in order to obtain the above effect, the V content is preferably 0.001% or more.
  • W 0 to 3.00% Since W has an effect of improving corrosion resistance, it may be contained if necessary. However, if W is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse carbonitride. Therefore, the W content is set to 3.00% or less.
  • the W content is preferably 2.00% or less, more preferably 1.50% or less.
  • the W content is preferably 0.05% or more, and more preferably 0.10% or more.
  • Ga 0-0.05% Since Ga has an effect of improving corrosion resistance, it may be contained if necessary. However, if Ga is excessively contained, the hot workability is deteriorated. Therefore, the Ga content is set to 0.05% or less. On the other hand, in order to obtain the above effect, the Ga content is preferably 0.0004% or more.
  • Co 0-2.50% Since Co has the effects of improving the strength, soft magnetic properties, high-speed cold forging property, and machinability of the steel material, it may be contained as necessary. In addition, the addition of an appropriate amount of Co increases the saturation magnetic flux density, and thus enhances the soft magnetic characteristics. However, if Co is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Co content is 2.50% or less.
  • the Co content is preferably 1.00% or less, and more preferably 0.80% or less.
  • the Co content is preferably 0.05% or more, more preferably 0.10% or more.
  • Sb 0 to 2.50% Since Sb has an effect of improving corrosion resistance, it may be contained if necessary. However, if Sb is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Sb content is set to 2.50% or less.
  • the Sb content is more preferably 1.00% or less, and further preferably 0.20% or less.
  • the Sb content is preferably 0.01% or more, and more preferably 0.05% or more.
  • Ta 0-2.50% Since Ta has an effect of improving corrosion resistance, it may be contained if necessary. However, if Ta is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Ta content is 2.50% or less. The Ta content is preferably 1.50% or less, more preferably 0.90% or less. On the other hand, in order to obtain the above effect, the Ta content is preferably 0.01% or more, more preferably 0.04% or more, and further preferably 0.08% or more.
  • the rod-shaped steel material according to the present invention may contain one or more elements selected from Ca, Mg, Zr, and REM as the second group element, if necessary.
  • Ca, Mg, Zr, and REM may be contained, if necessary, for deoxidation.
  • the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated.
  • the toughness is reduced by the coarse inclusions. Therefore, Ca: 0.05% or less, Mg: 0.012% or less, Zr: 0.012% or less, REM: 0.05% or less.
  • the Ca content is preferably 0.010% or less, more preferably 0.005% or less.
  • the Mg content is preferably 0.010% or less, more preferably 0.005% or less.
  • Zr is preferably 0.010% or less, and more preferably 0.005% or less.
  • the REM is preferably 0.010% or less.
  • the Ca content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • the Mg content is preferably 0.0004% or more, and more preferably 0.001% or more.
  • the Zr content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • the REM content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • REM is a general term for 17 elements including 15 elements of lanthanoids, Y and Sc. One or more of these 17 elements can be contained in steel, and the REM content means the total content of these elements.
  • the rod-shaped steel material according to the present invention may contain one or more elements selected from Pb, Se, Te, Bi, S and P as the elements of the third group, if necessary. .. 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%, Pb, Se, Te, Bi, S and P may be contained if necessary because of machinability. However, if each of these elements is excessively contained, the soft magnetic properties and the high-speed cold forging property are deteriorated. It also reduces toughness.
  • Pb 0.30% or less
  • Se 0.80% or less
  • Te 0.30% or less
  • Bi 0.50% or less
  • S 0.50 or less
  • the Pb content is preferably 0.1% or less, more preferably 0.05% or less.
  • the Se content is preferably 0.1% or less, and more preferably 0.05% or less.
  • the Te content is preferably 0.1% or less, more preferably 0.05% or less.
  • the Bi content is preferably 0.1% or less, and more preferably 0.05% or less.
  • the S content is preferably 0.1% or less, and more preferably 0.05% or less.
  • the P content is preferably 0.1% or less, and more preferably 0.05% or less.
  • Pb 0.0001% or more
  • Se 0.0001% or more
  • Te 0.0001% or more
  • Bi 0.0001% or more
  • S 0.0001% or more
  • the Pb content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the Se content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the Te content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • the Bi content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the S content is more preferably 0.0001% or more, and further preferably 0.0002% or more.
  • the P content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the balance is Fe and impurities.
  • impurity is a component mixed with raw materials such as ore and scrap, and various factors in the manufacturing process when the steel sheet is industrially manufactured, and is allowed as long as it does not adversely affect the present invention. Means something.
  • impurities examples include O, Zn, H and the like. Impurities are preferably reduced, but when they are contained, O, Zn and H are preferably 0.01% or less.
  • the stainless steel rod-shaped steel material according to the present invention can obtain the effect as long as it has the above-mentioned configuration regardless of the manufacturing method.
  • the stainless steel rod-shaped steel material according to the present invention can be obtained by the following manufacturing method. It can be obtained stably.
  • a steel having the above chemical composition is melted, a slab having a predetermined diameter is cast, and then hot or hot rod wire rolling is rough-rolled, intermediate-rolled, and finish-rolled. And heat-treat the rod-shaped steel material. It is preferable to perform inclined rolling before rough rolling. Then, if necessary, pickling or the like is performed as appropriate.
  • Finish rolling inlet temperature In hot rolling of rod-shaped steel, it is preferable to control the inlet temperature of finish rolling.
  • the temperature at the finish rolling inlet side of the bar-shaped steel material changes the average particle size of the nitride and also changes the solid solution fraction of N and B contained in the steel. Therefore, the finish rolling inlet temperature affects the soft magnetic properties, high-speed cold forging property, and machinability.
  • the temperature on the finish rolling inlet side of the bar-shaped steel material exceeds 1200 ° C., the nitride is easily melted, and the amount of solid solution N and the amount of solid solution B increase. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated.
  • the finish rolling inlet temperature is preferably 1200 ° C. or lower, preferably 1100 ° C. or lower, and even more preferably 1050 ° C. or lower.
  • the temperature on the finishing rolling inlet side is less than 600 ° C.
  • the amount of solid solution N becomes too small, so that the machinability deteriorates.
  • the presence of the unsolid solution nitride increases the average particle size of the nitride, which reduces the high-speed cold forging property. Therefore, the temperature on the entry side of the finish rolling is set to 600 ° C. or higher.
  • the finish rolling inlet temperature is preferably 700 ° C. or higher, more preferably 800 ° C.
  • the roll diameter of finish rolling affects the strain distribution and amount of bar-shaped steel, and is related to the average particle size of nitrides and the amount of solid melt N in steel. , It affects machinability and needs to be controlled.
  • the diameter of the finished rolled roll is less than 50 mm, strain is not introduced into the center of the rod-shaped steel material, formation of fine nitrides on the dislocations is not promoted, and the average particle diameter of the nitrides becomes large.
  • the amount of solid solution N increases. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated.
  • the diameter of the finished rolled roll is preferably 50 mm or more, preferably 80 mm or more, and more preferably 100 mm or more.
  • the diameter of the finished rolled roll exceeds 500 mm, the nitride becomes too fine and the amount of solid solution N and the amount of solid solution B also increase, resulting in deterioration of machinability and magnetic properties. It is preferable, and 300 mm or less is more preferable.
  • Heat treatment temperature of rod-shaped steel material It is preferable that the hot-rolled rod-shaped steel material is heat-treated.
  • the heat treatment temperature of the bar steel changes the average particle size of the nitride and the solid solution fraction in the steel. Therefore, the heat treatment temperature of the rod-shaped steel material affects the soft magnetic properties, high-speed cold forging property, and machinability.
  • the heat treatment temperature of the rod-shaped steel material exceeds 1300 ° C., the nitride is easily melted, and the amount of solid solution N and the amount of solid solution B increase. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated.
  • the average particle size of the nitride becomes too small, which reduces machinability.
  • the heat treatment temperature is set to 1300 ° C. or lower, preferably 1200 ° C. or lower, and more preferably 1100 ° C. or lower.
  • the heat treatment temperature of the rod-shaped steel material is less than 500 ° C., the amount of solid solution N becomes too small, and the machinability deteriorates.
  • the presence of the unsolid solution nitride increases the average particle size of the nitride, which reduces the high-speed cold forging property. Therefore, the heat treatment temperature is set to 500 ° C. or higher.
  • the heat treatment temperature is preferably 600 ° C. or higher, more preferably 700 ° C. or higher.
  • the stainless steel rod of the present invention has a compressibility of 70% and a strain rate without cracks of 0.1 / s or more, and can realize excellent high-speed cold forging property.
  • the stainless steel rod-shaped steel material of the present invention has a hole depth (tool life) of 50 mm or more due to drilling, and can realize excellent machinability.
  • the stainless steel rod-shaped steel material of the present invention has a coercive force of 5.0 A / m or less, and can realize excellent soft magnetic properties.
  • Electromagnetic parts are, for example, cores and connectors such as injectors and solenoid valves, and since the rod-shaped steel material used as the material has excellent soft magnetic properties, "magnetic attraction” It can produce effects such as “improvement”, “reducing the diameter of parts”, and “improvement of responsiveness”. In addition, since the rod-shaped steel used as the material has excellent high-speed cold forging and machinability, it is possible to manufacture the part at high production and low cost, and it is also possible to make a near net shape by cold forging. To.
  • the conditions are described below. Specifically, the cast slab is heated, and after inclined rolling, rough rolling, and intermediate rolling, No. Finish rolling was performed at a finish rolling temperature of 1180 ° C. and a finish rolling roll diameter of 480 mm under the conditions of 123, and then No. 1 in Table 6 was performed. Heat treatment was performed at a temperature of 1290 ° C. under the condition of 123 to prepare a bar wire (bar-shaped steel material) having a diameter of 20.0 mm.
  • the obtained bar wire (bar-shaped steel material) was evaluated for the average particle size of the nitride, the amount of solid melt N in the steel, the amount of solid melt B, high-speed cold forging property, soft magnetic properties, and machinability.
  • Table 3 and 4 are examples of the present invention and comparative examples corresponding to the present invention 1, and the amount of solid solution N in the steel is shown in the table.
  • Table 5 shows an example of the present invention and a comparative example corresponding to the present invention 2, and the actual results of the amount of solid solution B in the steel are shown in the table.
  • the average particle size of the nitride is the surface layer portion, the central portion, and the 1/4 depth position portion existing between the surface layer portion and the central portion in the L cross section of the rod-shaped steel material (cross section including the center line of the rod-shaped steel material).
  • one or more visual fields were measured with a visual field of 400 times. Then, the nitride in the observation field of view was identified using FE-SEM / ESD, and the average value of the equivalent circle diameters of the nitride in the same field of view was calculated.
  • the average particle size of the nitride is 0.01 to 5 ⁇ m, it is “A”, if it is 5 to 7 ⁇ m, it is “B”, if it is 7 to 10 ⁇ m, it is “C”, and if it exceeds 10 ⁇ m, it is “D”.
  • the steel bar of the present invention was used, it was "A”, “B”, and “C”, and the average particle size of the nitride was excellent.
  • the nitride includes carbonitride.
  • the high-speed cold forging property was judged from the presence or absence of cracks in the end face by a compression test.
  • a test piece of ⁇ 10 ⁇ 15 mm is prepared, the strain rate is changed under the condition of a compression rate of 70% at room temperature, the test piece is compressed, the side surface of the test piece after the test is observed, the presence or absence of cracks is judged, and high-speed cooling is performed.
  • the forgeability was evaluated. "A” if the compression rate is 70% and the strain rate without cracking is 10 / s or more, "B” if it is 1 / s or more, "C” if it is 0.1 / s or more, and less than 0.1 / s. If so, it was set as "D". When the steel bar of the present invention was used, it was "A”, “B”, and “C”, and was excellent in high-speed cold forging property.
  • the coercive force (A / m) was measured.
  • a ring-shaped test piece having a thickness of 3 mm, an outer diameter of 10 mm, and an inner diameter of 8 mm was prepared, and after being heat-treated at 950 ° C. ⁇ 2 hr, the coercive force was measured. If the coercive force is 2.0 A / m or less, it is "A”, if it is 3.5 A / m or less, it is "B”, if it is 5.0 A / m or less, it is "C”, and if it is over 5.0 A / m. For example, “D” was used. When the steel bar of the present invention was used, it was “A”, “B", and “C”, and had excellent soft magnetic properties.
  • the machinability was evaluated by the tool life.
  • a hole of ⁇ 15 ⁇ 30 mm is prepared and drilled in the longitudinal direction (dry type, drill diameter: ⁇ 4 mm, cutting speed: 25 m / min, feed: 0.1 mm / rev, tool: SKH9) to make the hole uncut.
  • the depth was measured and the machinability was evaluated. If the hole depth (tool life) is 130 mm or more, it is set as "A”, if it is 100 mm or more, it is set as "B”, if it is 50 mm or more, it is set as "C”, and if it is less than 50 mm, it is set as "D”. When the steel bar of the present invention was used, it was "A”, “B", and “C”, and the machinability was excellent.
  • Table 6 shows an example of the present invention and a comparative example corresponding to the present invention 1, and the amount of solid solution N in the steel is shown in the table.
  • Table 7 shows an example of the present invention and a comparative example corresponding to the present invention 2, and the actual results of the amount of solid solution B in the steel are shown in the table.
  • a rod-shaped steel material having excellent soft magnetic properties can be obtained, which is extremely useful in industry.

Abstract

A stainless steel bar material which has a chemical composition that contains, in mass%, from 0.001% to 0.030% of C, from 0.01% to 4.00% of Si, from 0.01% to 2.00% of Mn, from 0.01% to 4.00% of Ni, from 8.0% to 35.0% of Cr, from 0.01% to 5.00% of Mo, from 0.01% to 2.00% of Cu, from 0.001% to 0.030% of N, 7.000% or less of Al, from 0% to 2.00% of Ti, from 0% to 2.00% of Nb and from 0% to 0.1% of B, with the balance being made up of Fe and impurities. With respect to this stainless steel bar material, the chemical composition additionally contains, in mass%, one or more elements selected from among 0.001% or more of Ti, 0.001% or more of Nb and 0.0001% or more of B; the average particle diameter of nitrides is 10 μm or less; and the amount of N solid-solved in the steel is 0.020% by mass or less.

Description

ステンレス棒状鋼材及び電磁部品Stainless steel rods and electromagnetic parts
　本発明は、電磁ステンレス鋼、特に高速冷間鍛造性と切削性、軟磁気特性に優れるステンレス棒状鋼材及びそれを用いた電磁部品に関する。 The present invention relates to electromagnetic stainless steel, particularly stainless steel rod-shaped steel having excellent high-speed cold forging property, machinability, and soft magnetic properties, and electromagnetic parts using the same.
　従来、インジェクタや電磁弁などに代表されるような、電磁ステンレス製品は、ＳＵＳ４３０、ＳＵＳ４１０Ｌなどを代表とするフェライト系ステンレス鋼線材、鋼線を素材として加工・成型・熱処理され製造されてきた。しかしながら、上記のようなフェライト系ステンレス鋼線材から加工、製造されたステンレス製品の軟磁気特性は、高精度・高出力な部品に十分対応できていない。また、それら製品は、冷間鍛造性や切削性が部品製造の高生産へ対応できず、用途の制限を受ける欠点があった。上記課題に対して、軟磁気特性や冷間鍛造性、切削性の向上として、合金元素の最適化による技術が検討されている（例えば、特許文献１～３）。しかし、成分とプロセスの組合せによる組織制御を活用することにより、フェライト系ステンレス棒線の軟磁気特性、高速冷間鍛造性、切削性の向上を実現できることに着目した発明はない。 Conventionally, electromagnetic stainless steel products such as injectors and solenoid valves have been manufactured by processing, molding, and heat-treating using ferrite-based stainless steel wires and steel wires such as SUS430 and SUS410L as materials. However, the soft magnetic properties of stainless steel products processed and manufactured from the above-mentioned ferritic stainless steel wire rods are not sufficiently compatible with high-precision and high-output parts. In addition, these products have the drawback that their cold forgeability and machinability cannot cope with the high production of parts manufacturing, and their applications are limited. To solve the above problems, techniques for optimizing alloying elements have been studied for improving soft magnetic properties, cold forging properties, and machinability (for example, Patent Documents 1 to 3). However, there is no invention focusing on the fact that the soft magnetic characteristics, high-speed cold forging property, and machinability of ferritic stainless steel rods can be improved by utilizing the structure control by the combination of components and processes.
特開平６－４９６０６号公報Japanese Unexamined Patent Publication No. 6-49606 特開平６－４９６０５号公報Japanese Unexamined Patent Publication No. 6-49605 特開平３－４４４４８号公報Japanese Unexamined Patent Publication No. 3-44448
　以上を踏まえ、本発明は、上記課題を解決し、高速冷間鍛造性と切削性、軟磁気特性に優れる電磁ステンレス鋼、特にステンレス棒状鋼材及びそれを用いた電磁部品を提供することを目的とする。 Based on the above, it is an object of the present invention to solve the above problems and to provide electromagnetic stainless steel having excellent high-speed cold forging property, machinability, and soft magnetic property, particularly stainless rod-shaped steel material and electromagnetic parts using the same. do.
　本発明は、上記の課題を解決するためになされたものであり、下記のステンレス棒状鋼材及び電磁部品を要旨とする。
［１］化学組成が、質量％で、
　Ｃ：０．００１～０．０３０％、Ｓｉ：０．０１～４．００％、Ｍｎ：０．０１～２．００％、Ｎｉ：０．０１～４．００％、Ｃｒ：８．０～３５．０％、Ｍｏ：０．０１～５．００％、Ｃｕ：０．０１～２．００％、Ｎ：０．００１～０．０３０％、Ａｌ：７．０００％以下を含有し、
　さらに、
　Ｔｉ：０～２．００％、Ｎｂ：０～２．００％、Ｂ：０～０．１０００％であり、
　Ｔｉ：０．００１％以上、Ｎｂ：０．００１％以上、Ｂ：０．０００１％以上から選択される一種以上を含有し、
　Ｓｎ：０～２．５０％、Ｖ：０～２．０％、Ｗ：０～３．００％、Ｇａ：０～０．０５％、Ｃｏ：０～２．５０％、Ｓｂ：０～２．５０％、Ｔａ：０～２．５０％、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％であり、
　残部：Ｆｅおよび不純物であり、
窒化物の平均粒子径が１０μｍ以下であり、鋼中の固溶Ｎ量が０．０２０質量％以下であるステンレス棒状鋼材。 The present invention has been made to solve the above problems, and the gist of the present invention is the following stainless steel rod-shaped steel materials and electromagnetic parts.
[1] The chemical composition is 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: 8.0 to Contains 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.030%, Al: 7,000% or less.
moreover,
Ti: 0 to 2.00%, Nb: 0 to 2.00%, B: 0 to 0.1000%, and so on.
It contains one or more selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more.
Sn: 0 to 2.50%, V: 0 to 2.0%, W: 0 to 3.00%, Ga: 0 to 0.05%, Co: 0 to 2.50%, Sb: 0 to 2 .50%, Ta: 0 to 2.50%, 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%
Remaining: Fe and impurities,
A stainless rod-shaped steel material having an average particle size of a nitride of 10 μm or less and a solid solution N content in steel of 0.020% by mass or less.
［２］化学組成が、質量％で、
　Ｃ：０．００１～０．０３０％、Ｓｉ：０．０１～４．００％、Ｍｎ：０．０１～２．００％、Ｎｉ：０．０１～４．００％、Ｃｒ：８．０～３５．０％、Ｍｏ：０．０１～５．００％、Ｃｕ：０．０１～２．００％、Ｎ：０．００１～０．０３０％、Ａｌ：７．０００％以下を含有し、
　さらに、
　Ｔｉ：０～２．００％、Ｎｂ：０～２．００％、Ｂ：０～０．１０００％であり、
　Ｔｉ：０．００１％以上、Ｎｂ：０．００１％以上、Ｂ：０．０００１％以上から選択される一種以上を含有し、
　Ｓｎ：０～２．５０％、Ｖ：０～２．０％、Ｗ：０～３．００％、Ｇａ：０～０．０５％、Ｃｏ：０～２．５０％、Ｓｂ：０～２．５０％、Ｔａ：０～２．５０％、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％であり、
　残部：Ｆｅおよび不純物であり、
窒化物の平均粒子径が１０μｍ以下であり、鋼中の固溶Ｂ量が０．０１５質量％以下であるステンレス棒状鋼材。 [2] The chemical composition is 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: 8.0 to Contains 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.030%, Al: 7,000% or less.
moreover,
Ti: 0 to 2.00%, Nb: 0 to 2.00%, B: 0 to 0.1000%, and so on.
It contains one or more selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more.
Sn: 0 to 2.50%, V: 0 to 2.0%, W: 0 to 3.00%, Ga: 0 to 0.05%, Co: 0 to 2.50%, Sb: 0 to 2 .50%, Ta: 0 to 2.50%, 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%
Remaining: Fe and impurities,
A stainless rod-shaped steel material having an average particle size of a nitride of 10 μm or less and a solid solution B amount in steel of 0.015% by mass or less.
［３］前記化学組成が、質量％でさらに、下記第１群～第３群から選択される１群以上を含有する、［１］または［２］に記載のステンレス棒状鋼材。
第１群　
　Ｓｎ：０．０００１～２．５％、Ｖ：０．００１～２．０％Ｗ：０．０５～３．０％、Ｇａ：０．０００４～０．０５％、Ｃｏ：０．０５～２．５％、Ｓｂ：０．０１～２．５％、およびＴａ：０．０１～２．５％から選択される一種以上。
第２群
　Ｃａ：０．０００２～０．０５％、Ｍｇ：０．０００２～０．０１２％、Ｚｒ：０．０００２～０．０１２％、およびＲＥＭ：０．０００２～０．０５％から選択される一種以上。
第３群
　Ｐｂ：０．０００１～０．３０％、Ｓｅ：０．０００１～０．８０％、Ｔｅ：０．０００１～０．３０％、Ｂｉ：０．０００１～０．５０％、Ｓ：０．０００１～０．５０％、Ｐ：０．０００１～０．３０％から選択される一種以上。 [3] The stainless steel rod-shaped steel material according to [1] or [2], wherein the chemical composition further contains one or more groups selected from the following groups 1 to 3 in mass%.
Group 1
Sn: 0.0001 to 2.5%, V: 0.001 to 2.0% W: 0.05 to 3.0%, Ga: 0.0004 to 0.05%, Co: 0.05 to 2 One or more selected from .5%, Sb: 0.01 to 2.5%, and Ta: 0.01 to 2.5%.
Group 2 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% More than one kind.
Group 3 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 One or more selected from .0001 to 0.50% and P: 0.0001 to 0.30%.
［４］圧縮率７０％で割れなきひずみ速度が０．１／ｓ以上である、［１］～［３］のいずれか１つに記載のステンレス棒状鋼材。
［５］ドリル加工による穴深さ（工具寿命）が５０ｍｍ以上である、［１］～［４］のいずれか１つに記載のステンレス棒状鋼材。
［６］保磁力が５．０Ａ／ｍ以下である、［１］～［５］のいずれか１つに記載のステンレス棒状鋼材。 [4] The stainless steel rod-shaped steel material according to any one of [1] to [3], which has a compressibility of 70% and a strain rate without cracking of 0.1 / s or more.
[5] The stainless steel rod-shaped steel material according to any one of [1] to [4], wherein the hole depth (tool life) by drilling is 50 mm or more.
[6] The stainless steel rod-shaped steel material according to any one of [1] to [5], which has a coercive force of 5.0 A / m or less.
［７］［１］～［６］のいずれか１つに記載のステンレス棒状鋼材を用いた電磁部品。 [7] An electromagnetic component using the stainless rod-shaped steel material according to any one of [1] to [6].
　本発明によれば、高速冷間鍛造性と切削性、軟磁気特性に優れるステンレス棒状鋼材及び電磁部品を得ることができる。 According to the present invention, it is possible to obtain stainless steel rod-shaped steel materials and electromagnetic parts having excellent high-speed cold forging properties, machinability, and soft magnetic properties.
　本発明者らは高速冷間鍛造性と切削性、軟磁気特性に優れるステンレス棒状鋼材及び電磁部品を得るために、種々の検討を行なった。その結果、以下の（ａ）～（ｃ）の知見を得た。 The present inventors conducted various studies in order to obtain stainless steel rod-shaped steel materials and electromagnetic parts having excellent high-speed cold forging properties, machinability, and soft magnetic properties. As a result, the following findings (a) to (c) were obtained.
　（ａ）Ｂ，Ｔｉ，Ｎｂの一種以上で成分調整されたフェライト系ステンレス鋼と熱延プロセス（仕上圧延入側温度、仕上げ圧延のロール径、熱処理温度）の組み合わせで、窒化物平均粒子径と鋼中の固溶Ｎ量、固溶Ｂ量を小さくすることができる。 (A) A combination of ferritic stainless steel whose composition is adjusted with one or more of B, Ti, and Nb and a hot rolling process (finish rolling inlet temperature, finish rolling roll diameter, heat treatment temperature) to obtain the average grain size of nitrides. The amount of solid melt N and the amount of solid melt B in steel can be reduced.
　（ｂ）その結果、高速冷間鍛造性については圧縮率７０％で割れなきひずみ速度が０．１／ｓ以上であり、切削性については切削抵抗が５０ｍｍ以上であり、軟磁気特性については保磁力が５．０Ａ／ｍ以下となり、高速冷間鍛造性と切削性、軟磁気特性の特性をいずれも向上することのできる新しい手法を見出した。 (B) As a result, the high-speed cold forging property has a compression rate of 70%, the unbreakable strain rate is 0.1 / s or more, the machinability has a cutting resistance of 50 mm or more, and the soft magnetic property is maintained. We have found a new method that can improve the characteristics of high-speed cold forging, machinability, and soft magnetic properties by reducing the magnetic force to 5.0 A / m or less.
　本発明は上記の知見に基づいてなされたものである。また、本発明の好ましい一実施形態を詳細に説明する。以降の説明では、本発明の好ましい一実施形態を本発明として記載する。以下、本発明の各要件について詳しく説明する。本発明の棒状の鋼材において、「棒状鋼材」は「棒鋼」、「線材」、「鋼線」、「異形線」、「異形棒鋼」などを含む。 The present invention was made based on the above findings. In addition, a preferred embodiment of the present invention will be described in detail. In the following description, a preferred embodiment of the present invention will be described as the present invention. Hereinafter, each requirement of the present invention will be described in detail. In the bar-shaped steel material of the present invention, the "bar-shaped steel material" includes "bar steel", "wire rod", "steel wire", "deformed wire", "deformed bar steel" and the like.
　１．窒化物の平均粒子径
　本発明に係る棒状鋼材では、窒化物の平均粒子径を制御する。具体的には、窒化物の平均粒子径を１０μｍ以下とする。窒化物の平均粒子径が１０μｍ超となると、粗大窒化物によって高速冷間鍛造性が低下するためである。窒化物の平均粒子径は７μｍ以下とするのがより好ましく、５μｍ以下とするのがさらに好ましくい。一方、窒化物の平均粒子径が小さくなりすぎると、軟磁気特性や切削性が劣化するため、窒化物の平均粒子径は０．０１μｍ以上が好ましい。なお、窒化物には炭窒化物を含む。 1. 1. Average particle size of nitride In the rod-shaped steel material according to the present invention, the average particle size of the nitride is controlled. Specifically, the average particle size of the nitride is 10 μm or less. This is because when the average particle size of the nitride exceeds 10 μm, the high-speed cold forging property is deteriorated by the coarse nitride. The average particle size of the nitride is more preferably 7 μm or less, and even more preferably 5 μm or less. On the other hand, if the average particle size of the nitride becomes too small, the soft magnetic properties and machinability deteriorate. Therefore, the average particle size of the nitride is preferably 0.01 μm or more. The nitride includes carbonitride.
　窒化物の平均粒子径は、棒状鋼材のＬ断面（棒状鋼材の中心線を含む断面）において、表層部、中心部、および表層部と中心部との間に存在する１／４深さ位置部において、４００倍の視野で、１視野以上測定を行い、観察視野における窒化物を、ＦＥ－ＳＥＭ／ＥＳＤを用いて同定し、同視野の窒化物の円相当径の平均値を算出することによって求めることができる。 The average particle diameter of the nitride is the surface layer portion, the central portion, and the 1/4 depth position portion existing between the surface layer portion and the central portion in the L cross section of the rod-shaped steel material (cross section including the center line of the rod-shaped steel material). By measuring one or more fields in a 400-fold field, identifying the nitrides in the observation field using FE-SEM / ESD, and calculating the average value of the equivalent circle diameters of the nitrides in the same field. You can ask.
　２．鋼中の固溶Ｎ量と固溶Ｂ量
　本発明に係る棒状鋼材では、鋼中の固溶Ｎ量を０．０２０質量％以下とする、あるいは固溶Ｂ量を０．０１５質量％以下とすることにより、軟磁気特性と高速冷間鍛造性を改善する。以下、本発明の後述する好適な成分組成と上記窒化物の平均粒子径を具備するとともに鋼中の固溶Ｎ量を０．０２０質量％以下と規定する発明を「本発明１」と称する。また、本発明の好適な成分組成と上記窒化物の平均粒子径を具備するとともに鋼中の固溶Ｂ量を０．０１５質量％以下と規定する発明を「本発明２」と称する。 2. 2. Amount of solid solution N and amount of solid solution B in steel In the rod-shaped steel material according to the present invention, the amount of solid solution N in steel is 0.020% by mass or less, or the amount of solid solution B is 0.015% by mass or less. By doing so, the soft magnetic properties and high-speed cold forging property are improved. Hereinafter, an invention having a suitable component composition described later and an average particle size of the above-mentioned nitride and defining the amount of solid-dissolved N in steel to be 0.020% by mass or less will be referred to as "Invention 1". Further, an invention having a suitable component composition of the present invention and the average particle size of the above-mentioned nitride and defining the amount of solid solution B in steel to be 0.015% by mass or less is referred to as "the present invention 2".
　２－１．鋼中の固溶Ｎ量
　本発明１に係る棒状鋼材では、鋼中の固溶Ｎ量を制御する。具体的には、鋼中の固溶Ｎ量を０．０２０質量％以下とする。鋼中の固溶Ｎ量が０．０２０質量％超となると、固溶Ｎによる格子ひずみによって軟磁気特性と高速冷間鍛造性が低下するためである。鋼中の固溶Ｎ量は０．０１５質量％以下とするのがより好ましく、０．０１質量％以下とするのがさらに好ましい。一方、鋼中の固溶Ｎ量が小さくなりすぎると、切削性が劣化するため、好ましくは鋼中の固溶Ｎ量を０．００００１質量％以上とする。なお、本発明鋼において、結晶組織はフェライト鋼であるため、鋼中の固溶Ｎ量はフェライト相中の固溶Ｎ量に相当する。 2-1. Amount of solid solution N in steel In the rod-shaped steel material according to the present invention 1, the amount of solid solution N in steel is controlled. Specifically, the amount of solid solution N in the steel is 0.020% by mass or less. This is because when the amount of solid solution N in the steel exceeds 0.020% by mass, the soft magnetic properties and high-speed cold forging property are deteriorated due to the lattice strain due to the solid solution N. The amount of solid solution N in the steel is more preferably 0.015% by mass or less, and further preferably 0.01% by mass or less. On the other hand, if the amount of solid solution N in the steel becomes too small, the machinability deteriorates, so the amount of solid solution N in the steel is preferably 0.00001% by mass or more. Since the crystal structure of the steel of the present invention is ferritic steel, the amount of solid solution N in the steel corresponds to the amount of solid solution N in the ferrite phase.
　鋼中の固溶Ｎ量は、棒状鋼材に対し電解抽出残渣を行い、窒化物を抽出させ、窒化物のＮ量（Ｎｐｒｅ）を測定し、鋼中全Ｎ量（Ｎ０）との差分から、鋼中の固溶Ｎ量（＝Ｎ０－Ｎｐｒｅ）を測定することができる。 The amount of solid-melted N in the steel is the difference from the total amount of N in the steel (N 0 ) by measuring the N amount (N pre ) of the nitride by performing electrolytic extraction residue on the rod-shaped steel material and extracting the nitride. Therefore, the amount of solid melt N (= N 0 −N pre ) in the steel can be measured.
　２－２．鋼中の固溶Ｂ量
　本発明２に係る棒状鋼材では、鋼中の固溶Ｂ量を制御することで本発明の課題を解決することもできる。具体的には、鋼中の固溶Ｂ量を０．０１５質量％以下とする。鋼中の固溶Ｂ量が０．０１５質量％超となると、固溶Ｂによる格子ひずみによって軟磁気特性と高速冷間鍛造性が低下するためである。鋼中の固溶Ｂ量は０．０１０質量％以下とするのがより好ましく、０．００５質量％以下とするのがさらに好ましい。一方、鋼中の固溶Ｂ量が小さくなりすぎると、切削性が劣化するため、好ましくは鋼中の固溶Ｂ量を０．００００１質量％以上とする。なお、本発明鋼において、結晶組織はフェライト鋼であるため、鋼中の固溶Ｂ量はフェライト相中の固溶Ｂ量に相当する。 2-2. Amount of solid solution B in steel In the rod-shaped steel material according to the present invention 2, the problem of the present invention can be solved by controlling the amount of solid solution B in the steel. Specifically, the amount of solid solution B in the steel is 0.015% by mass or less. This is because when the amount of the solid solution B in the steel exceeds 0.015% by mass, the soft magnetic properties and the high-speed cold forging property are deteriorated due to the lattice strain due to the solid solution B. The amount of solid solution B in the steel is more preferably 0.010% by mass or less, and further preferably 0.005% by mass or less. On the other hand, if the amount of solid solution B in the steel becomes too small, the machinability deteriorates, so the amount of solid solution B in the steel is preferably 0.00001% by mass or more. Since the crystal structure of the steel of the present invention is ferritic steel, the amount of solid solution B in the steel corresponds to the amount of solid solution B in the ferrite phase.
　鋼中の固溶Ｂ量は、棒状鋼材に対し電解抽出残渣を行い、窒化物を抽出させ、窒化物のＢ量（Ｂｐｒｅ）を測定し、鋼中全Ｂ量（Ｂ０）との差分から、鋼中の固溶Ｂ量（＝Ｂ０－Ｂｐｒｅ）を測定することができる。 The amount of solid B in the steel is the difference from the total amount of B in the steel (B 0 ) after electrolytic extraction residue is applied to the rod-shaped steel to extract the nitride and the amount of B of the nitride (B pre ) is measured. Therefore, the amount of solid melt B (= B 0 −B pre ) in the steel can be measured.
　３．化学組成
　各元素の限定理由は下記のとおりである。なお、以下の説明において含有量についての「％」は、「質量％」を意味する。 3. 3. The reasons for limiting the chemical composition of each element are as follows. In the following description, "%" for the content means "mass%".
　Ｃ：０．００１～０．０３０％
　Ｃは、鋼材の強度、切削性を高める。このため、Ｃ含有量は、０．００１％以上とする。しかしながら、Ｃを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が劣化する。このため、Ｃ含有量は０．０３０％以下とする。Ｃ含有量は０．０２０％以下とするのが好ましく、０．０１５％以下とするのがより好ましい。 C: 0.001 to 0.030%
C enhances the strength and machinability of the steel material. Therefore, the C content is set to 0.001% or more. However, if C is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability deteriorate. Therefore, the C content is set to 0.030% or less. The C content is preferably 0.020% or less, more preferably 0.015% or less.
　Ｓｉ：０．０１～４．００％
　Ｓｉは、脱酸元素として含有させ、軟磁気特性、切削性を向上させる。このため、Ｓｉ含有量は０．０１％以上とし、０．１０％以上とするのが好ましい。しかしながら、Ｓｉを過剰に含有させると、高速冷間鍛造性と軟磁気特性、切削性が劣化する。このため、Ｓｉ含有量は４．００％以下とする。Ｓｉ含有量は３．００％以下とするのが好ましく、１．５０％以下とするのがより好ましい。 Si: 0.01-4.00%
Si is contained as a deoxidizing element to improve soft magnetic properties and machinability. Therefore, the Si content is preferably 0.01% or more, preferably 0.10% or more. However, if Si is excessively contained, high-speed cold forging property, soft magnetic property, and machinability are deteriorated. Therefore, the Si content is set to 4.00% or less. The Si content is preferably 3.00% or less, more preferably 1.50% or less.
　Ｍｎ：０．０１～２．００％
　Ｍｎは、鋼材の強度と軟磁気特性、切削性を向上させる。このため、Ｍｎ含有量は、０．０１％以上とし、０．０５％以上とするのが好ましい。しかしながら、Ｍｎを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。また、耐食性が低下する場合もある。このため、Ｍｎ含有量は２．００％以下とする。Ｍｎ含有量は１．００％以下とするのが好ましく、０．５０％以下とするのがより好ましい。 Mn: 0.01-2.00%
Mn improves the strength, soft magnetic properties, and machinability of steel materials. Therefore, the Mn content is preferably 0.01% or more, preferably 0.05% or more. However, if Mn is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, corrosion resistance may decrease. Therefore, the Mn content is set to 2.00% or less. The Mn content is preferably 1.00% or less, and more preferably 0.50% or less.
　Ｎｉ：０．０１～４．００％
　Ｎｉは、鋼材の靭性と軟磁気特性、高速冷間鍛造性、切削性を向上させる。このため、Ｎｉ含有量は０．０１％以上とし、０．０５％以上とするのが好ましい。しかしながら、Ｎｉを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。このため、Ｎｉ含有量は４．００％以下とする。Ｎｉ含有量は３．００％以下とするのが好ましく、１．００％以下とするのがより好ましく、０．５０％以下とするのがさらに好ましい。 Ni: 0.01-4.00%
Ni improves the toughness and soft magnetic properties of steel materials, high-speed cold forging, and machinability. Therefore, the Ni content is preferably 0.01% or more, preferably 0.05% or more. However, if Ni is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Ni content is set to 4.00% or less. The Ni content is preferably 3.00% or less, more preferably 1.00% or less, and even more preferably 0.50% or less.
　Ｃｒ：８．０～３５．０％
　Ｃｒは、耐食性と軟磁気特性、高速冷間鍛造性、切削性を向上させる。このため、Ｃｒ含有量は、８．０％以上とする。Ｃｒ含有量は１０．０％以上とするのが好ましい。しかしながら、Ｃｒを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。Ｃｒ含有量は３５．０％以下にする。Ｃｒ含有量は２１．０％以下とするのが好ましく、２０．０％以下とするのがより好ましい。 Cr: 8.0 to 35.0%
Cr improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Cr content is set to 8.0% or more. The Cr content is preferably 10.0% or more. However, if Cr is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. The Cr content should be 35.0% or less. The Cr content is preferably 21.0% or less, more preferably 20.0% or less.
　Ｍｏ：０．０１～５．００％
　Ｍｏは、耐食性と軟磁気特性、高速冷間鍛造性、切削性を向上させる。このため、Ｍｏ含有量は０．０１％以上とする。しかしながら、Ｍｏを過剰に含有させると、高速冷間鍛造性、軟磁気特性、切削性が低下する。このため、Ｍｏ含有量は５．００％以下とする。Ｍｏ含有量は３．００％以下とするのが好ましく、２．００％以下とするのがより好ましく、１．５０％以下とするのがさらに好ましい。 Mo: 0.01-5.00%
Mo improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Mo content is 0.01% or more. However, if Mo is excessively contained, high-speed cold forging property, soft magnetic property, and machinability are deteriorated. Therefore, the Mo content is set to 5.00% or less. The Mo content is preferably 3.00% or less, more preferably 2.00% or less, and even more preferably 1.50% or less.
　Ｃｕ：０．０１～２．００％
　Ｃｕは、耐食性と軟磁気特性、高速冷間鍛造性、切削性を向上させる。このため、Ｃｕ含有量は０．０１％以上とし、０．０５％以上とするのが好ましい。しかしながら、Ｃｕを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。このため、Ｃｕ含有量は２．００％以下とする。Ｃｕ含有量は１．００％以下とするのが好ましく、０．８０％以下とするのがより好ましく、０．４０％以下とするのがさらに好ましい。 Cu: 0.01-2.00%
Cu improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Cu content is preferably 0.01% or more, preferably 0.05% or more. However, if Cu is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Cu content is set to 2.00% or less. The Cu content is preferably 1.00% or less, more preferably 0.80% or less, still more preferably 0.40% or less.
　Ｎ：０．００１～０．０３０％
　Ｎは、鋼材の強度、切削性を向上させる。また、窒化物を形成させる元素である。このため、Ｎ含有量は０．００１％以上とし、０．００２％以上とするのが好ましい。しかしながら、Ｎを過剰に含有させると、軟磁気特性、切削性、高速冷間鍛造性が低下する。また、窒化物の平均粒子径が大きくなり、固溶Ｎ量が多くなる。このため、Ｎ含有量は０．０３０％以下とする。Ｎ含有量は０．０２５％以下とするのが好ましく、０．０２０％以下とするのがより好ましい。 N: 0.001 to 0.030%
N improves the strength and machinability of the steel material. It is also an element that forms a nitride. Therefore, the N content is preferably 0.001% or more, preferably 0.002% or more. However, if N is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large, and the amount of solid solution N increases. Therefore, the N content is set to 0.030% or less. The N content is preferably 0.025% or less, more preferably 0.020% or less.
　Ａｌ：７．０００％以下
　Ａｌは、脱酸を促進させ、介在物清浄度レベルを向上させる効果を有する。また、Ａｌの添加は軟磁気特性、高速冷間鍛造性、切削性を高める。しかしながら、Ａｌを過剰に含有させると、その効果は飽和し、軟磁気特性、高速冷間鍛造性、切削性が低下する。また、粗大介在物によって靭性が低下する。このため、Ａｌ含有量は７．０００％以下とする。Ａｌ含有量は３．０００％以下とするのが好ましく、０．１００％以下とするのがより好ましく、０．０２０％以下とするのがさらに好ましい。一方、前記効果を得るためには、Ａｌ含有量は０．００１％以上とするのが好ましい。 Al: 7,000% or less Al has the effect of promoting deoxidation and improving the cleanliness level of inclusions. In addition, the addition of Al enhances soft magnetic properties, high-speed cold forging, and machinability. However, if Al is excessively contained, the effect is saturated, and the soft magnetic property, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse inclusions. Therefore, the Al content is set to 7,000% or less. The Al content is preferably 3.000% or less, more preferably 0.100% or less, and even more preferably 0.020% or less. On the other hand, in order to obtain the above effect, the Al content is preferably 0.001% or more.
　本発明に係る棒状鋼材は、上記元素に加え、Ｔｉ：０．００１％以上、Ｎｂ：０．００１％以上、Ｂ：０．０００１％以上から選択される一種以上の元素を、下記成分範囲内で含有させる。これらの元素は窒化物を構成する主要元素であり、窒化物の平均粒子径や固溶Ｎ量に関係するため制御する必要がある。Ｔｉ、Ｎｂ、Ｂのうち、上記選択されなかった元素については、含有しないか、下記成分範囲内で含有させることができる。 In addition to the above elements, the rod-shaped steel material according to the present invention contains one or more elements selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more within the following component range. Incorporate in. These elements are the main elements constituting the nitride and need to be controlled because they are related to the average particle size of the nitride and the amount of solid solution N. Of Ti, Nb, and B, the element not selected above may not be contained or may be contained within the following component range.
　Ｔｉ：０～２．００％
　Ｔｉは、鋼材の強度、軟磁気特性、高速冷間鍛造性、切削性を高める効果を有する。また、Ｔｉは窒化物を形成し、固溶Ｎ量に関係する。更に炭窒化物を形成するので、Ｃｒ炭化物の生成を抑制し、Ｃｒ欠乏層の生成を抑制する。この結果、粒界腐食を防止する効果を有する。このため、Ｔｉ含有量は０．００１％以上とする。しかしながら、Ｔｉを過剰に含有させると、軟磁気特性、切削性、高速冷間鍛造性が低下する。また、窒化物の平均粒子径が大きくなる。このため、Ｔｉ含有量は２．００％以下とする。Ｔｉ含有量は１．００％以下とするのが好ましく、０．５０％以下とするのがより好ましく、０．５０％以下とすることがさらに好ましく、０．２５％以下とすると一層好ましい。また、効果発現のために、０．０１％以上含有するのが好ましい。０．０５％以上がさらに好ましい。０．１０％以上であってもよい。 Ti: 0 to 2.00%
Ti has the effects of enhancing the strength, soft magnetic properties, high-speed cold forging property, and machinability of steel materials. Further, Ti forms a nitride and is related to the amount of solid solution N. Further, since carbonitride is formed, the formation of Cr carbide is suppressed and the formation of a Cr-deficient layer is suppressed. As a result, it has the effect of preventing intergranular corrosion. Therefore, the Ti content is set to 0.001% or more. However, if Ti is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the Ti content is set to 2.00% or less. The Ti content is preferably 1.00% or less, more preferably 0.50% or less, further preferably 0.50% or less, and even more preferably 0.25% or less. In addition, it is preferably contained in an amount of 0.01% or more in order to exhibit the effect. More preferably, 0.05% or more. It may be 0.10% or more.
　Ｎｂ：０～２．００％
　Ｎｂは、鋼材の強度、軟磁気特性、高速冷間鍛造性、切削性を高める効果を有する。また、Ｎｂは窒化物を形成し、固溶Ｎ量に関係する。更に炭窒化物を形成するので、Ｃｒ炭化物の生成を抑制し、Ｃｒ欠乏層の生成を抑制する。この結果、粒界腐食を防止する効果を有する。このため、Ｎｂ含有量は０．００１％以上とする。しかしながら、Ｎｂを過剰に含有させると、軟磁気特性、切削性、高速冷間鍛造性が低下する。また、窒化物の平均粒子径が大きくなる。このため、Ｎｂ含有量は２．００％以下とする。Ｎｂ含有量は１．００％以下とするのが好ましく、０．８０％以下とするのがより好ましく、０．６０％以下とすることがさらに好ましい。また、効果発現のために、０．０２％以上含有するのが好ましい。０．０５％以上がさらに好ましい。０．１０％以上であってもよい。 Nb: 0 to 2.00%
Nb has the effect of enhancing the strength, soft magnetic properties, high-speed cold forging property, and machinability of the steel material. Further, Nb forms a nitride and is related to the amount of solid solution N. Further, since carbonitride is formed, the formation of Cr carbide is suppressed and the formation of a Cr-deficient layer is suppressed. As a result, it has the effect of preventing intergranular corrosion. Therefore, the Nb content is set to 0.001% or more. However, if Nb is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the Nb content is set to 2.00% or less. The Nb content is preferably 1.00% or less, more preferably 0.80% or less, and even more preferably 0.60% or less. In addition, it is preferably contained in an amount of 0.02% or more in order to exhibit the effect. More preferably, 0.05% or more. It may be 0.10% or more.
　Ｂ：０～０．１０００％
　Ｂは、鋼材の軟磁気特性、高速冷間鍛造性、切削性を高める効果を有する。また、ＢはＢＮなどのボロン窒化物を形成し、固溶Ｎ量、固溶Ｂ量に関係する。特にＢＮは切削性の向上に寄与する。このため、Ｂ含有量は０．０００１％以上とする。しかしながら、Ｂを過剰に含有させると、軟磁気特性、切削性、高速冷間鍛造性が低下する。また、窒化物の平均粒子径が大きくなる。このため、Ｂ含有量は０．１０００％以下とする。Ｂ含有量は０．０２００％以下とするのが好ましく、０．０１００％以下とするのがより好ましい。また、効果発現のために、０．０００５％以上含有するのが好ましい。０．００１０％以上がさらに好ましい。０．００２０％以上であってもよい。 B: 0 to 0.1000%
B has the effect of enhancing the soft magnetic properties, high-speed cold forging property, and machinability of the steel material. Further, B forms a boron nitride such as BN, and is related to the amount of solid solution N and the amount of solid solution B. In particular, BN contributes to the improvement of machinability. Therefore, the B content is set to 0.0001% or more. However, if B is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the B content is set to 0.1000% or less. The B content is preferably 0.0200% or less, more preferably 0.0100% or less. Further, in order to exhibit the effect, it is preferably contained in an amount of 0.0005% or more. 0.0010% or more is more preferable. It may be 0.0020% or more.
　本発明に係る棒状鋼材は、上記元素に加え、必要に応じて、第１群の元素として、Ｓｎ、Ｖ、Ｗ、Ｇａ、Ｃｏ、ＳｂおよびＴａから選択される一種以上の元素を含有させてもよい。 In addition to the above elements, the rod-shaped steel material according to the present invention contains, if necessary, one or more elements selected from Sn, V, W, Ga, Co, Sb and Ta as the elements of the first group. May be good.
　Ｓｎ：０～２．５０％
　Ｓｎは、耐食性、軟磁気特性、高速冷間鍛造性、切削性を向上させる効果を有するため、必要に応じて含有させてもよい。しかしながら、Ｓｎを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。また、Ｓｎの粒界偏析によって靭性が低下する。このため、Ｓｎ含有量は２．５０％以下とする。Ｓｎ含有量は１．００％以下とするのがより好ましく、０．２０％以下とするのがさらに好ましい。一方、上記効果を得るためには、Ｓｎ含有量は０．０００１％以上とするのが好ましく、０．０５％以上とするのがより好ましい。 Sn: 0 to 2.50%
Sn may be contained as necessary because it has the effects of improving corrosion resistance, soft magnetic properties, high-speed cold forging property, and machinability. However, if Sn is contained in an excessive amount, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness decreases due to the grain boundary segregation of Sn. Therefore, the Sn content is set to 2.50% or less. The Sn content is more preferably 1.00% or less, and further preferably 0.20% or less. On the other hand, in order to obtain the above effect, the Sn content is preferably 0.0001% or more, and more preferably 0.05% or more.
　Ｖ：０～２．０％
　Ｖは、軟磁気特性、高速冷間鍛造性、切削性を向上させる効果を有するため、必要に応じて含有させてもよい。しかしながら、Ｖを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。また、粗大炭窒化物によって靭性が低下する。このため、Ｖ含有量は２．０％以下とする。Ｖ含有量は１．０％以下とするのが好ましく、０．５％以下とするのがより好ましく、０．１％以下とするのがさらに好ましい。一方、上記効果を得るためには、Ｖ含有量は０．００１％以上とするのが好ましい。 V: 0-2.0%
Since V has an effect of improving soft magnetic properties, high-speed cold forging property, and machinability, it may be contained as necessary. However, if V is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse carbonitride. Therefore, the V content is set to 2.0% or less. The V content is preferably 1.0% or less, more preferably 0.5% or less, and even more preferably 0.1% or less. On the other hand, in order to obtain the above effect, the V content is preferably 0.001% or more.
　Ｗ：０～３．００％
　Ｗは、耐食性を向上させる効果を有するため、必要に応じて含有させてもよい。しかしながら、Ｗを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。また、粗大炭窒化物によって靭性が低下する。このため、Ｗ含有量は３．００％以下とする。Ｗ含有量は２．００％以下とするのが好ましく、１．５０％以下とするのがより好ましい。一方、上記効果を得るためには、Ｗ含有量は０．０５％以上とするのが好ましく、０．１０％以上とするのがより好ましい。 W: 0 to 3.00%
Since W has an effect of improving corrosion resistance, it may be contained if necessary. However, if W is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse carbonitride. Therefore, the W content is set to 3.00% or less. The W content is preferably 2.00% or less, more preferably 1.50% or less. On the other hand, in order to obtain the above effect, the W content is preferably 0.05% or more, and more preferably 0.10% or more.
　Ｇａ：０～０．０５％
　Ｇａは、耐食性を向上させる効果を有するため、必要に応じて含有させてもよい。しかしながら、Ｇａを過剰に含有させると、熱間加工性が低下する。このため、Ｇａ含有量は０．０５％以下とする。一方、上記効果を得るためには、Ｇａ含有量は０．０００４％以上とするのが好ましい。 Ga: 0-0.05%
Since Ga has an effect of improving corrosion resistance, it may be contained if necessary. However, if Ga is excessively contained, the hot workability is deteriorated. Therefore, the Ga content is set to 0.05% or less. On the other hand, in order to obtain the above effect, the Ga content is preferably 0.0004% or more.
　Ｃｏ：０～２．５０％
　Ｃｏは、鋼材の強度、軟磁気特性、高速冷間鍛造性、切削性を向上させる効果を有するため、必要に応じて含有させてもよい。また、適量のＣｏ添加は飽和磁束密度を高めるため、軟磁気特性を高める。しかしながら、Ｃｏを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。このため、Ｃｏ含有量は２．５０％以下とする。Ｃｏ含有量は１．００％以下とするのが好ましく、０．８０％以下とするのがより好ましい。一方、上記効果を得るためには、Ｃｏ含有量は０．０５％以上とするのが好ましく、０．１０％以上とするのがより好ましい。 Co: 0-2.50%
Since Co has the effects of improving the strength, soft magnetic properties, high-speed cold forging property, and machinability of the steel material, it may be contained as necessary. In addition, the addition of an appropriate amount of Co increases the saturation magnetic flux density, and thus enhances the soft magnetic characteristics. However, if Co is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Co content is 2.50% or less. The Co content is preferably 1.00% or less, and more preferably 0.80% or less. On the other hand, in order to obtain the above effect, the Co content is preferably 0.05% or more, more preferably 0.10% or more.
　Ｓｂ：０～２．５０％
　Ｓｂは、耐食性を向上させる効果を有するため、必要に応じて含有させてもよい。しかしながら、Ｓｂを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。このため、Ｓｂ含有量は２．５０％以下とする。Ｓｂ含有量は１．００％以下とするのがより好ましく、０．２０％以下とするのがさらに好ましい。一方、上記効果を得るためには、Ｓｂ含有量は０．０１％以上とするのが好ましく、０．０５％以上とするのがより好ましい。 Sb: 0 to 2.50%
Since Sb has an effect of improving corrosion resistance, it may be contained if necessary. However, if Sb is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Sb content is set to 2.50% or less. The Sb content is more preferably 1.00% or less, and further preferably 0.20% or less. On the other hand, in order to obtain the above effect, the Sb content is preferably 0.01% or more, and more preferably 0.05% or more.
　Ｔａ：０～２．５０％
　Ｔａは、耐食性を向上させる効果を有するため、必要に応じて含有させてもよい。しかしながら、Ｔａを過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。このため、Ｔａ含有量は２．５０％以下とする。Ｔａ含有量は１．５０％以下とするのが好ましく、０．９０％以下とするのがより好ましい。一方、上記効果を得るためには、Ｔａ含有量は０．０１％以上とするのが好ましく、０．０４％以上とするのがより好ましく、０．０８％以上とするのがさらに好ましい。 Ta: 0-2.50%
Since Ta has an effect of improving corrosion resistance, it may be contained if necessary. However, if Ta is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Ta content is 2.50% or less. The Ta content is preferably 1.50% or less, more preferably 0.90% or less. On the other hand, in order to obtain the above effect, the Ta content is preferably 0.01% or more, more preferably 0.04% or more, and further preferably 0.08% or more.
　本発明に係る棒状鋼材は、上記元素に加え、必要に応じて、第２群の元素として、Ｃａ、Ｍｇ、Ｚｒ、およびＲＥＭから選択される一種以上の元素を含有させてもよい。
　Ｃａ：０～０．０５％
　Ｍｇ：０～０．０１２％
　Ｚｒ：０～０．０１２％
　ＲＥＭ：０～０．０５％
　Ｃａ、Ｍｇ、Ｚｒ、およびＲＥＭは、脱酸のため、必要に応じて、含有させてもよい。しかしながら、これら各元素を過剰に含有させると、軟磁気特性、高速冷間鍛造性、切削性が低下する。また、粗大介在物によって靭性が低下する。このため、Ｃａ：０．０５％以下、Ｍｇ：０．０１２％以下、Ｚｒ：０．０１２％以下、ＲＥＭ：０．０５％以下とする。Ｃａ含有量は、０．０１０％以下とするのが好ましく、０．００５％以下とするのがより好ましい。Ｍｇは、０．０１０％以下とするのが好ましく、０．００５％以下とするのがより好ましい。Ｚｒは、０．０１０％以下とするのが好ましく、０．００５％以下とするのがより好ましい。ＲＥＭは、０．０１０％以下とするのが好ましい。
　一方、上記効果を得るためには、Ｃａ：０．０００２％以上、Ｍｇ：０．０００２％以上、Ｚｒ：０．０００２％以上、ＲＥＭ：０．０００２％以上とするのが好ましい。Ｃａ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。Ｍｇ含有量は、０．０００４％以上とするのが好ましく、０．００１％以上とするのがさらに好ましい。Ｚｒ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。ＲＥＭ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。
　なお、ＲＥＭとは、ランタノイドの１５元素にＹおよびＳｃを合わせた１７元素の総称である。これらの１７元素のうちの１種以上を鋼に含有させることができ、ＲＥＭ含有量は、これらの元素の合計含有量を意味する。 In addition to the above elements, the rod-shaped steel material according to the present invention may contain one or more elements selected from Ca, Mg, Zr, and REM as the second group element, if necessary.
Ca: 0-0.05%
Mg: 0 to 0.012%
Zr: 0 to 0.012%
REM: 0-0.05%
Ca, Mg, Zr, and REM may be contained, if necessary, for deoxidation. However, if each of these elements is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse inclusions. Therefore, Ca: 0.05% or less, Mg: 0.012% or less, Zr: 0.012% or less, REM: 0.05% or less. The Ca content is preferably 0.010% or less, more preferably 0.005% or less. The Mg content is preferably 0.010% or less, more preferably 0.005% or less. Zr is preferably 0.010% or less, and more preferably 0.005% or less. The REM is preferably 0.010% or less.
On the other hand, in order to obtain the above effects, it is preferable that Ca: 0.0002% or more, Mg: 0.0002% or more, Zr: 0.0002% or more, and REM: 0.0002% or more. The Ca content is more preferably 0.0004% or more, and even more preferably 0.001% or more. The Mg content is preferably 0.0004% or more, and more preferably 0.001% or more. The Zr content is more preferably 0.0004% or more, and even more preferably 0.001% or more. The REM content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
REM is a general term for 17 elements including 15 elements of lanthanoids, Y and Sc. One or more of these 17 elements can be contained in steel, and the REM content means the total content of these elements.
　本発明に係る棒状鋼材は、上記元素に加え、必要に応じて、第３群の元素として、Ｐｂ、Ｓｅ、Ｔｅ、Ｂｉ、ＳおよびＰから選択される一種以上の元素を含有させてもよい。
　Ｐｂ：０～０．３０％、
　Ｓｅ：０～０．８０％、
　Ｔｅ：０～０．３０％、
　Ｂｉ：０～０．５０％、
　Ｓ：０～０．５０％、
　Ｐ：０～０．３０％、
　Ｐｂ、Ｓｅ、Ｔｅ、Ｂｉ、ＳおよびＰは、切削性のため、必要に応じて、含有させてもよい。しかしながら、これら各元素を過剰に含有させると、軟磁気特性、高速冷間鍛造性が低下する。また、靭性が低下する。このため、Ｐｂ：０．３０％以下、Ｓｅ：０．８０％以下、Ｔｅ：０．３０％以下、Ｂｉ：０．５０％以下、Ｓ：０．５０以下、Ｐ：０．３０以下とする。Ｐｂ含有量は、０．１％以下とするのが好ましく、０．０５％以下とするのがより好ましい。Ｓｅ含有量は、０．１％以下とするのが好ましく、０．０５％以下とするのがより好ましい。Ｔｅ含有量は、０．１％以下とするのが好ましく、０．０５％以下とするのがより好ましい。Ｂｉ含有量は、０．１％以下とするのが好ましく、０．０５％以下とするのがより好ましい。Ｓ含有量は、０．１％以下とするのが好ましく、０．０５％以下とするのがより好ましい。Ｐ含有量は、０．１％以下とするのが好ましく、０．０５％以下とするのがより好ましい。
　一方、上記効果を得るためには、Ｐｂ：０．０００１％以上、Ｓｅ：０．０００１％以上、Ｔｅ：０．０００１％以上、Ｂｉ：０．０００１％以上、Ｓ：０．０００１％以上、Ｐ：０．０００１％以上とするのが好ましい。Ｐｂ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。Ｓｅ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。Ｔｅ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。Ｂｉ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。Ｓ含有量は、０．０００１％以上とするのがより好ましく、０．０００２％以上とするのがさらに好ましい。Ｐ含有量は、０．０００４％以上とするのがより好ましく、０．００１％以上とするのがさらに好ましい。 In addition to the above elements, the rod-shaped steel material according to the present invention may contain one or more elements selected from Pb, Se, Te, Bi, S and P as the elements of the third group, if necessary. ..
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%,
Pb, Se, Te, Bi, S and P may be contained if necessary because of machinability. However, if each of these elements is excessively contained, the soft magnetic properties and the high-speed cold forging property are deteriorated. It also reduces toughness. Therefore, Pb: 0.30% or less, Se: 0.80% or less, Te: 0.30% or less, Bi: 0.50% or less, S: 0.50 or less, P: 0.30 or less. .. The Pb content is preferably 0.1% or less, more preferably 0.05% or less. The Se content is preferably 0.1% or less, and more preferably 0.05% or less. The Te content is preferably 0.1% or less, more preferably 0.05% or less. The Bi content is preferably 0.1% or less, and more preferably 0.05% or less. The S content is preferably 0.1% or less, and more preferably 0.05% or less. The P content is preferably 0.1% or less, and more preferably 0.05% or less.
On the other hand, in order to obtain the above effects, Pb: 0.0001% or more, Se: 0.0001% or more, Te: 0.0001% or more, Bi: 0.0001% or more, S: 0.0001% or more, P: It is preferably 0.0001% or more. The Pb content is more preferably 0.0004% or more, and further preferably 0.001% or more. The Se content is more preferably 0.0004% or more, and further preferably 0.001% or more. The Te content is more preferably 0.0004% or more, and even more preferably 0.001% or more. The Bi content is more preferably 0.0004% or more, and further preferably 0.001% or more. The S content is more preferably 0.0001% or more, and further preferably 0.0002% or more. The P content is more preferably 0.0004% or more, and further preferably 0.001% or more.
　本発明の鋼板の化学組成において、残部はＦｅおよび不純物である。ここで「不純物」とは、鋼板を工業的に製造する際に、鉱石、スクラップ等の原料、製造工程の種々の要因によって混入する成分であって、本発明に悪影響を与えない範囲で許容されるものを意味する。 In the chemical composition of the steel sheet of the present invention, the balance is Fe and impurities. Here, the "impurity" is a component mixed with raw materials such as ore and scrap, and various factors in the manufacturing process when the steel sheet is industrially manufactured, and is allowed as long as it does not adversely affect the present invention. Means something.
　なお、不純物としては、例えば、Ｏ、Ｚｎ、Ｈ等が例示される。不純物は低減されることが好ましいが、含有される場合は、Ｏ，ＺｎおよびＨは０．０１％以下とするのが望ましい。 Examples of impurities include O, Zn, H and the like. Impurities are preferably reduced, but when they are contained, O, Zn and H are preferably 0.01% or less.
　４．製造方法
　本発明に係る電磁ステンレス鋼（ステンレス棒状鋼材）の好ましい製造方法を説明する。本発明に係るステンレス棒状鋼材は、製造方法によらず、上述の構成を有していれば、その効果を得られるが、例えば、以下のような製造方法により、本発明に係るステンレス棒状鋼材を安定して得ることができる。 4. Manufacturing Method A preferred manufacturing method for the electromagnetic stainless steel (stainless steel rod-shaped steel material) according to the present invention will be described. The stainless steel rod-shaped steel material according to the present invention can obtain the effect as long as it has the above-mentioned configuration regardless of the manufacturing method. For example, the stainless steel rod-shaped steel material according to the present invention can be obtained by the following manufacturing method. It can be obtained stably.
　本発明に係るステンレス棒状鋼材では、上記化学組成を有する鋼を溶製し、所定の径を有する鋳片を鋳造した後、熱間または温間の棒線圧延を粗圧延、中間圧延、仕上圧延にて行い、棒状鋼材の熱処理を行う。粗圧延の前に傾斜圧延を行うと好ましい。その後、必要に応じて、適宜、酸洗などを行う。 In the stainless steel rod-shaped steel material according to the present invention, a steel having the above chemical composition is melted, a slab having a predetermined diameter is cast, and then hot or hot rod wire rolling is rough-rolled, intermediate-rolled, and finish-rolled. And heat-treat the rod-shaped steel material. It is preferable to perform inclined rolling before rough rolling. Then, if necessary, pickling or the like is performed as appropriate.
　４－１．仕上圧延入側温度
　棒状鋼材の熱間圧延は仕上圧延の入側温度を制御するのが好ましい。棒状鋼材の仕上圧延入側温度は、窒化物の平均粒子径を変化させるとともに、鋼中に含まれるＮ、Ｂの固溶量分率を変化させる。このため、仕上圧延入側温度は軟磁気特性、高速冷間鍛造性、切削性に影響を与える。棒状鋼材の仕上圧延入側温度を１２００℃超とすると、窒化物が溶解しやすくなり、固溶Ｎ量、固溶Ｂ量が増加する。この結果、軟磁気特性、高速冷間鍛造性が低下する。また、窒化物の平均粒子径が小さくなりすぎるため、切削性が低下する。そのため、仕上圧延入側温度は１２００℃以下とし、１１００℃以下が好ましく、１０５０℃以下が更に好ましい。一方で仕上圧延入側温度が６００℃未満となると、固溶Ｎ量が少なりなりすぎるため、切削性が低下する。また、未固溶窒化物の存在によって窒化物の平均粒子径が大きくなるため、高速冷間鍛造性が低下する。そのため、仕上圧延入側温度は６００℃以上とする。仕上圧延入側温度は７００℃以上で好ましく、８００℃で更に好ましい。 4-1. Finish rolling inlet temperature In hot rolling of rod-shaped steel, it is preferable to control the inlet temperature of finish rolling. The temperature at the finish rolling inlet side of the bar-shaped steel material changes the average particle size of the nitride and also changes the solid solution fraction of N and B contained in the steel. Therefore, the finish rolling inlet temperature affects the soft magnetic properties, high-speed cold forging property, and machinability. When the temperature on the finish rolling inlet side of the bar-shaped steel material exceeds 1200 ° C., the nitride is easily melted, and the amount of solid solution N and the amount of solid solution B increase. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes too small, which reduces machinability. Therefore, the finish rolling inlet temperature is preferably 1200 ° C. or lower, preferably 1100 ° C. or lower, and even more preferably 1050 ° C. or lower. On the other hand, when the temperature on the finishing rolling inlet side is less than 600 ° C., the amount of solid solution N becomes too small, so that the machinability deteriorates. In addition, the presence of the unsolid solution nitride increases the average particle size of the nitride, which reduces the high-speed cold forging property. Therefore, the temperature on the entry side of the finish rolling is set to 600 ° C. or higher. The finish rolling inlet temperature is preferably 700 ° C. or higher, more preferably 800 ° C.
　４－２．仕上圧延のロール径
　仕上圧延のロール径は棒状鋼材のひずみ分布と量に影響を与え、窒化物の平均粒子径と鋼中の固溶Ｎ量に関係し、軟磁気特性、高速冷間鍛造性、切削性に影響を与えるため、制御する必要がある。仕上圧延ロール径が５０ｍｍ未満となると、棒状鋼材中心部へひずみが導入されず、転位上への微細窒化物の形成が促進されず、窒化物の平均粒子径が大きくなる。また、固溶Ｎ量は多くなる。この結果、軟磁気特性、高速冷間鍛造性が低下する。なお、前記の仕上圧延ロール径の鋼中の固溶Ｎ量に及ぼす作用は、固溶Ｂの場合も同様であり、仕上圧延ロール径が５０ｍｍ未満となると固溶Ｂ量が多くなる。このため、仕上圧延ロール径は５０ｍｍ以上とし、８０ｍｍ以上が好ましく、１００ｍｍ以上が更に好ましい。一方で仕上圧延ロール径が５００ｍｍ超となると、窒化物が微細になりすぎ、固溶Ｎ量、固溶Ｂ量も多くなるため、切削性と磁気特性が低下するため、５００ｍｍ以下とし、４００ｍｍ以下で好ましく、３００ｍｍ以下で更に好ましい。 4-2. Roll diameter of finish rolling The roll diameter of finish rolling affects the strain distribution and amount of bar-shaped steel, and is related to the average particle size of nitrides and the amount of solid melt N in steel. , It affects machinability and needs to be controlled. When the diameter of the finished rolled roll is less than 50 mm, strain is not introduced into the center of the rod-shaped steel material, formation of fine nitrides on the dislocations is not promoted, and the average particle diameter of the nitrides becomes large. In addition, the amount of solid solution N increases. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated. The effect of the finished rolling roll diameter on the solid solution N amount in the steel is the same in the case of the solid solution B, and when the finished rolling roll diameter is less than 50 mm, the solid solution B amount increases. Therefore, the diameter of the finished rolled roll is preferably 50 mm or more, preferably 80 mm or more, and more preferably 100 mm or more. On the other hand, if the diameter of the finished rolled roll exceeds 500 mm, the nitride becomes too fine and the amount of solid solution N and the amount of solid solution B also increase, resulting in deterioration of machinability and magnetic properties. It is preferable, and 300 mm or less is more preferable.
　４－３．棒状鋼材の熱処理温度
　熱間圧延された棒状鋼材は熱処理されるのが好ましい。棒状鋼材の熱処理温度は、窒化物の平均粒子径と鋼中の固溶量分率を変化させる。このため、棒状鋼材の熱処理温度は軟磁気特性、高速冷間鍛造性、切削性に影響を与える。棒状鋼材の熱処理温度を１３００℃超とすると、窒化物が溶解しやすくなり、固溶Ｎ量、固溶Ｂ量が増加する。この結果、軟磁気特性、高速冷間鍛造性が低下する。また、窒化物の平均粒子径が小さくなりすぎるため、切削性が低下する。そのため、熱処理温度は１３００℃以下とし、１２００℃以下が好ましく、１１００℃以下が更に好ましい。一方で棒状鋼材の熱処理温度が５００℃未満となると、固溶Ｎ量が少なくなりすぎるため、切削性が低下する。また、未固溶窒化物の存在によって窒化物の平均粒子径が大きくなるため、高速冷間鍛造性が低下する。そのため、熱処理温度は５００℃以上とする。熱処理温度は６００℃以上で好ましく、７００℃で更に好ましい。 4-3. Heat treatment temperature of rod-shaped steel material It is preferable that the hot-rolled rod-shaped steel material is heat-treated. The heat treatment temperature of the bar steel changes the average particle size of the nitride and the solid solution fraction in the steel. Therefore, the heat treatment temperature of the rod-shaped steel material affects the soft magnetic properties, high-speed cold forging property, and machinability. When the heat treatment temperature of the rod-shaped steel material exceeds 1300 ° C., the nitride is easily melted, and the amount of solid solution N and the amount of solid solution B increase. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes too small, which reduces machinability. Therefore, the heat treatment temperature is set to 1300 ° C. or lower, preferably 1200 ° C. or lower, and more preferably 1100 ° C. or lower. On the other hand, when the heat treatment temperature of the rod-shaped steel material is less than 500 ° C., the amount of solid solution N becomes too small, and the machinability deteriorates. In addition, the presence of the unsolid solution nitride increases the average particle size of the nitride, which reduces the high-speed cold forging property. Therefore, the heat treatment temperature is set to 500 ° C. or higher. The heat treatment temperature is preferably 600 ° C. or higher, more preferably 700 ° C. or higher.
　５．ステンレス棒状鋼材の品質
　本発明のステンレス棒状鋼材は、圧縮率７０％で割れなきひずみ速度が０．１／ｓ以上となり、優れた高速冷間鍛造性を実現することができる。
　本発明のステンレス棒状鋼材は、ドリル加工による穴深さ（工具寿命）が５０ｍｍ以上となり、優れた切削性を実現することができる。
　本発明のステンレス棒状鋼材は、保磁力が５．０Ａ／ｍ以下となり、優れた軟磁気特性を実現することができる。 5. Quality of Stainless Steel Rod The stainless steel rod of the present invention has a compressibility of 70% and a strain rate without cracks of 0.1 / s or more, and can realize excellent high-speed cold forging property.
The stainless steel rod-shaped steel material of the present invention has a hole depth (tool life) of 50 mm or more due to drilling, and can realize excellent machinability.
The stainless steel rod-shaped steel material of the present invention has a coercive force of 5.0 A / m or less, and can realize excellent soft magnetic properties.
　６．電磁部品
　本発明のステンレス棒状鋼材を用いた電磁部品は、例えばインジェクタや電磁弁などのコアやコネクタなどであり、素材とする棒状鋼材が優れた軟磁気特性を有することから、“磁気吸引力の向上”や“部品の細径化”、“応答性の向上”などという効果を奏することができる。また、素材とする棒状鋼材が優れた高速冷間鍛造性と切削性を有することから、当該部品を高生産・低コストで製造することが可能となり、冷間鍛造でのニアネットシェイプ化も可能にする。 6. Electromagnetic parts The electromagnetic parts using the stainless steel rod-shaped steel material of the present invention are, for example, cores and connectors such as injectors and solenoid valves, and since the rod-shaped steel material used as the material has excellent soft magnetic properties, "magnetic attraction" It can produce effects such as "improvement", "reducing the diameter of parts", and "improvement of responsiveness". In addition, since the rod-shaped steel used as the material has excellent high-speed cold forging and machinability, it is possible to manufacture the part at high production and low cost, and it is also possible to make a near net shape by cold forging. To.
　以下、実施例によって本発明をより具体的に説明するが、本発明は例示でありこれらの実施例に限定されるものではない。 Hereinafter, the present invention will be described in more detail by way of examples, but the present invention is an example and is not limited to these examples.
　表１、２に記載の化学組成を有する鋼を溶製した。鋼の溶製の際には、ステンレス鋼の安価な溶製プロセスであるＡＯＤ溶製を想定し、１００ｋｇの真空溶解炉にて溶解し、直径１８０ｍｍの鋳片に鋳造した。その後、下記の製造条件により直径２０．０ｍｍのステンレス棒線とした。 Steels having the chemical compositions shown in Tables 1 and 2 were melted. At the time of melting the steel, AOD melting, which is an inexpensive melting process of stainless steel, was assumed, and the steel was melted in a 100 kg vacuum melting furnace and cast into a slab having a diameter of 180 mm. Then, according to the following manufacturing conditions, a stainless steel rod having a diameter of 20.0 mm was obtained.
　以下に条件を記載する。具体的には、鋳造した鋳片を加熱し、傾斜圧延、粗圧延、中間圧延の後、表６のＮｏ．１２３の条件の仕上圧延温度１１８０℃、仕上圧延ロール径４８０ｍｍで仕上圧延を行い、その後表６のＮｏ．１２３の条件の温度１２９０℃で熱処理を施し、直径２０．０ｍｍの棒線（棒状鋼材）を作製した。 The conditions are described below. Specifically, the cast slab is heated, and after inclined rolling, rough rolling, and intermediate rolling, No. Finish rolling was performed at a finish rolling temperature of 1180 ° C. and a finish rolling roll diameter of 480 mm under the conditions of 123, and then No. 1 in Table 6 was performed. Heat treatment was performed at a temperature of 1290 ° C. under the condition of 123 to prepare a bar wire (bar-shaped steel material) having a diameter of 20.0 mm.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
　得られた棒線（棒状鋼材）について、窒化物の平均粒子径および鋼中の固溶Ｎ量、固溶Ｂ量、高速冷間鍛造性、軟磁気特性、切削性を評価した。以下、表３、表４および表５にまとめて結果を示す。表３、表４は本発明１に対応する本発明例及び比較例であり、表中に鋼中の固溶Ｎ量を記載している。表５は本発明２に対応する本発明例及び比較例であり、表中には鋼中の固溶Ｂ量の実績を記載している。なお、これらの測定は以下の手順に従い、測定を行った。 The obtained bar wire (bar-shaped steel material) was evaluated for the average particle size of the nitride, the amount of solid melt N in the steel, the amount of solid melt B, high-speed cold forging property, soft magnetic properties, and machinability. Below, the results are summarized in Table 3, Table 4 and Table 5. Tables 3 and 4 are examples of the present invention and comparative examples corresponding to the present invention 1, and the amount of solid solution N in the steel is shown in the table. Table 5 shows an example of the present invention and a comparative example corresponding to the present invention 2, and the actual results of the amount of solid solution B in the steel are shown in the table. These measurements were performed according to the following procedure.
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000004
Figure JPOXMLDOC01-appb-T000004
Figure JPOXMLDOC01-appb-T000005
Figure JPOXMLDOC01-appb-T000005
　窒化物の平均粒子径は、棒状鋼材のＬ断面（棒状鋼材の中心線を含む断面）において、表層部、中心部、および表層部と中心部との間に存在する１／４深さ位置部において、４００倍の視野で、１視野以上測定を行った。そして、観察視野における窒化物を、ＦＥ－ＳＥＭ／ＥＳＤを用いて同定し、同視野の窒化物の円相当径の平均値を算出した。窒化物の平均粒子径が０．０１～５μｍであれば「Ａ」、５～７μｍであれば「Ｂ」、７～１０μｍであれば「Ｃ」、１０μｍ超であれば「Ｄ」とした。本発明の棒鋼鋼材を使用した場合、「Ａ」および「Ｂ」、「Ｃ」であり、窒化物の平均粒子径に優れていた。なお、窒化物には炭窒化物を含む。 The average particle size of the nitride is the surface layer portion, the central portion, and the 1/4 depth position portion existing between the surface layer portion and the central portion in the L cross section of the rod-shaped steel material (cross section including the center line of the rod-shaped steel material). In, one or more visual fields were measured with a visual field of 400 times. Then, the nitride in the observation field of view was identified using FE-SEM / ESD, and the average value of the equivalent circle diameters of the nitride in the same field of view was calculated. If the average particle size of the nitride is 0.01 to 5 μm, it is “A”, if it is 5 to 7 μm, it is “B”, if it is 7 to 10 μm, it is “C”, and if it exceeds 10 μm, it is “D”. When the steel bar of the present invention was used, it was "A", "B", and "C", and the average particle size of the nitride was excellent. The nitride includes carbonitride.
　鋼中の固溶Ｎ量は、棒状鋼材に対し電解抽出残渣を行い、窒化物を抽出させ、窒化物のＮ量（Ｎｐｒｅ）を測定し、鋼中全Ｎ量（Ｎ０）との差分から、鋼中の固溶Ｎ量（＝Ｎ０－Ｎｐｒｅ）を測定した。鋼中の固溶Ｎ量が０．００００１～０．０１質量％であれば「Ａ」、０．０１～０．０１５質量％であれば「Ｂ」、０．０１５～０．０２０質量％であれば「Ｃ」、０．０２０質量％超であれば「Ｄ」とした。本発明の棒鋼鋼材を使用した場合、表３に示すとおり、「Ａ」および「Ｂ」、「Ｃ」であり、鋼中の固溶Ｎ量に優れていた。 The amount of solid-melted N in the steel is the difference from the total amount of N in the steel (N 0 ) after electrolytic extraction residue is applied to the rod-shaped steel to extract the nitride and the amount of N of the nitride (N pre ) is measured. From the above, the amount of solid melt N (= N 0 −N pre ) in the steel was measured. If the amount of solid melt N in the steel is 0.00001 to 0.01% by mass, it is "A", if it is 0.01 to 0.015% by mass, it is "B", and if it is 0.015 to 0.020% by mass. If there is, it is given as "C", and if it exceeds 0.020% by mass, it is given as "D". When the steel bar of the present invention was used, it was "A", "B", and "C" as shown in Table 3, and the amount of solid solution N in the steel was excellent.
　鋼中の固溶Ｂ量は、棒状鋼材に対し電解抽出残渣を行い、窒化物を抽出させ、窒化物のＢ量（Ｂｐｒｅ）を測定し、鋼中全Ｂ量（Ｂ０）との差分から、鋼中の固溶Ｂ量（＝Ｂ０－Ｂｐｒｅ）を測定した。鋼中の固溶Ｂ量が０．０１質量％以下であれば「Ｂ」、０．０１～０．０１５質量％であれば「Ｃ」、０．０１５質量％超であれば「Ｄ」とした。本発明の棒鋼鋼材を使用した場合、表５に示すとおり、「Ｂ」および「Ｃ」であり、鋼中の固溶Ｂ量に優れていた。 The amount of solid B in the steel is the difference from the total amount of B in the steel (B 0 ) after electrolytic extraction residue is applied to the rod-shaped steel to extract the nitride and the amount of B of the nitride (B pre ) is measured. From the above, the amount of solid melt B (= B 0 −B pre ) in the steel was measured. If the amount of solid solution B in the steel is 0.01% by mass or less, it is "B", if it is 0.01 to 0.015% by mass, it is "C", and if it is more than 0.015% by mass, it is "D". did. When the steel bar of the present invention was used, it was "B" and "C" as shown in Table 5, and the amount of solid solution B in the steel was excellent.
　高速冷間鍛造性は圧縮試験によって端面の割れ有無から判定した。φ１０×１５ｍｍの試験片を作製し、常温で圧縮率７０％の条件でひずみ速度を変化させ、試験片を圧縮させ、試験後の試験片側面を観察し、割れの有無を判定し、高速冷間鍛造性を評価した。圧縮率７０％で割れなきひずみ速度１０／ｓ以上であれば「Ａ」、１／ｓ以上であれば「Ｂ」、０．１／ｓ以上であれば「Ｃ」、０．１／ｓ未満であれば「Ｄ」とした。本発明の棒鋼鋼材を使用した場合、「Ａ」および、「Ｂ」、「Ｃ」であり、高速冷間鍛造性に優れていた。 The high-speed cold forging property was judged from the presence or absence of cracks in the end face by a compression test. A test piece of φ10 × 15 mm is prepared, the strain rate is changed under the condition of a compression rate of 70% at room temperature, the test piece is compressed, the side surface of the test piece after the test is observed, the presence or absence of cracks is judged, and high-speed cooling is performed. The forgeability was evaluated. "A" if the compression rate is 70% and the strain rate without cracking is 10 / s or more, "B" if it is 1 / s or more, "C" if it is 0.1 / s or more, and less than 0.1 / s. If so, it was set as "D". When the steel bar of the present invention was used, it was "A", "B", and "C", and was excellent in high-speed cold forging property.
　軟磁気特性は、保磁力（Ａ／ｍ）を測定した。厚さ３ｍｍ×外径１０ｍｍ×内径８ｍｍのリング状試験片を作製し、９５０℃×２ｈｒの熱処理を施した後に保磁力を測定した。保磁力が２．０Ａ／ｍ以下であれば「Ａ」、３．５Ａ／ｍ以下であれば「Ｂ」、５．０Ａ／ｍ以下であれば「Ｃ」、５．０Ａ／ｍ超であれば「Ｄ」とした。本発明の棒鋼鋼材を使用した場合、「Ａ」および「Ｂ」、「Ｃ」であり、軟磁気特性に優れていた。 For the soft magnetic property, the coercive force (A / m) was measured. A ring-shaped test piece having a thickness of 3 mm, an outer diameter of 10 mm, and an inner diameter of 8 mm was prepared, and after being heat-treated at 950 ° C. × 2 hr, the coercive force was measured. If the coercive force is 2.0 A / m or less, it is "A", if it is 3.5 A / m or less, it is "B", if it is 5.0 A / m or less, it is "C", and if it is over 5.0 A / m. For example, "D" was used. When the steel bar of the present invention was used, it was "A", "B", and "C", and had excellent soft magnetic properties.
　切削性は、工具寿命によって評価した。φ１５×３０ｍｍの試験片を作製し、長手方向へドリル加工（乾式、ドリル径：φ４ｍｍ、切削速度：２５ｍ／ｍｉｎ、送り：０．１ｍｍ／ｒｅｖ、工具：ＳＫＨ９）を行い、切削不能となる穴深さを測定し、切削性を評価した。穴深さ（工具寿命）が１３０ｍｍ以上であれば「Ａ」、１００ｍｍ以上であれば「Ｂ」、５０ｍｍ以上であれば「Ｃ」、５０ｍｍ未満であれば「Ｄ」とした。本発明の棒鋼鋼材を使用した場合、「Ａ」および「Ｂ」、「Ｃ」であり、切削性に優れていた。 The machinability was evaluated by the tool life. A hole of φ15 × 30 mm is prepared and drilled in the longitudinal direction (dry type, drill diameter: φ4 mm, cutting speed: 25 m / min, feed: 0.1 mm / rev, tool: SKH9) to make the hole uncut. The depth was measured and the machinability was evaluated. If the hole depth (tool life) is 130 mm or more, it is set as "A", if it is 100 mm or more, it is set as "B", if it is 50 mm or more, it is set as "C", and if it is less than 50 mm, it is set as "D". When the steel bar of the present invention was used, it was "A", "B", and "C", and the machinability was excellent.
　続いて表１に示す鋼種Ｐを用いて、表６、表７に記載の条件により、直径１５ｍｍの棒状鋼材を作製した。なお、仕上圧延入側温度、仕上圧延ロール径、熱処理温度以外の履歴は前記実施例１と同様とした。作製した棒線（棒状鋼材）について、窒化物の平均粒子径および鋼中の固溶Ｎ量、固溶Ｂ量、高速冷間鍛造性、軟磁気特性、切削性を、上述の方法で測定した。以下、結果をまとめて、表６、表７に示す。表６は本発明１に対応する本発明例及び比較例であり、表中に鋼中の固溶Ｎ量を記載している。表７は本発明２に対応する本発明例及び比較例であり、表中には鋼中の固溶Ｂ量の実績を記載している。 Subsequently, using the steel grade P shown in Table 1, a rod-shaped steel material having a diameter of 15 mm was produced under the conditions shown in Tables 6 and 7. The history other than the finish rolling inlet temperature, the finish rolling roll diameter, and the heat treatment temperature was the same as in Example 1. The average particle size of the nitride, the amount of solid melt N in the steel, the amount of solid melt B, the high-speed cold forging property, the soft magnetic property, and the machinability were measured for the produced bar wire (bar-shaped steel material) by the above-mentioned method. .. The results are summarized below and are shown in Tables 6 and 7. Table 6 shows an example of the present invention and a comparative example corresponding to the present invention 1, and the amount of solid solution N in the steel is shown in the table. Table 7 shows an example of the present invention and a comparative example corresponding to the present invention 2, and the actual results of the amount of solid solution B in the steel are shown in the table.
Figure JPOXMLDOC01-appb-T000006
Figure JPOXMLDOC01-appb-T000006
Figure JPOXMLDOC01-appb-T000007
Figure JPOXMLDOC01-appb-T000007
　本発明によれば、軟磁気特性に優れる棒状鋼材を得ることができ、産業上極めて有用である。 According to the present invention, a rod-shaped steel material having excellent soft magnetic properties can be obtained, which is extremely useful in industry.

Claims (7)

  1. 　化学組成が、質量％で、
    　Ｃ：０．００１～０．０３０％、
    　Ｓｉ：０．０１～４．００％、
    　Ｍｎ：０．０１～２．００％、
    　Ｎｉ：０．０１～４．００％、
    　Ｃｒ：８．０～３５．０％、
    　Ｍｏ：０．０１～５．００％、
    　Ｃｕ：０．０１～２．００％、
    　Ｎ：０．００１～０．０３０％、
    　Ａｌ：７．０００％以下を含有し、
    　さらに、
    　Ｔｉ：０～２．００％、
    　Ｎｂ：０～２．００％、
    　Ｂ：０～０．１０００％であり、
    　Ｔｉ：０．００１％以上、Ｎｂ：０．００１％以上、Ｂ：０．０００１％以上から選択される一種以上を含有し、
    　Ｓｎ：０～２．５０％、
    　Ｖ：０～２．０％、
    　Ｗ：０～３．００％、
    　Ｇａ：０～０．０５％、
    　Ｃｏ：０～２．５０％、
    　Ｓｂ：０～２．５０％、
    　Ｔａ：０～２．５０％、
    　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％であり、
    　残部：Ｆｅおよび不純物であり、
    窒化物の平均粒子径が１０μｍ以下であり、鋼中の固溶Ｎ量が０．０２０質量％以下であるステンレス棒状鋼材。     The chemical composition is by mass%,
    C: 0.001 to 0.030%,
    Si: 0.01-4.00%,
    Mn: 0.01-2.00%,
    Ni: 0.01-4.00%,
    Cr: 8.0 to 35.0%,
    Mo: 0.01-5.00%,
    Cu: 0.01-2.00%,
    N: 0.001 to 0.030%,
    Al: Contains 7,000% or less,
    moreover,
    Ti: 0 to 2.00%,
    Nb: 0 to 2.00%,
    B: 0 to 0.1000%,
    It contains one or more selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more.
    Sn: 0 to 2.50%,
    V: 0-2.0%,
    W: 0 to 3.00%,
    Ga: 0-0.05%,
    Co: 0-2.50%,
    Sb: 0 to 2.50%,
    Ta: 0-2.50%,
    Ca: 0-0.05%,
    Mg: 0 to 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%,
    Remaining: Fe and impurities,
    A stainless rod-shaped steel material having an average particle size of a nitride of 10 μm or less and a solid solution N content in steel of 0.020% by mass or less.
  2. 　化学組成が、質量％で、
    　Ｃ：０．００１～０．０３０％、
    　Ｓｉ：０．０１～４．００％、
    　Ｍｎ：０．０１～２．００％、
    　Ｎｉ：０．０１～４．００％、
    　Ｃｒ：８．０～３５．０％、
    　Ｍｏ：０．０１～５．００％、
    　Ｃｕ：０．０１～２．００％、
    　Ｎ：０．００１～０．０３０％、
    　Ａｌ：７．０００％以下を含有し、
    　さらに、
    　Ｔｉ：０～２．００％、
    　Ｎｂ：０～２．００％、
    　Ｂ：０～０．１０００％であり、
    　Ｔｉ：０．００１％以上、Ｎｂ：０．００１％以上、Ｂ：０．０００１％以上から選択される一種以上を含有し、
    　Ｓｎ：０～２．５０％、
    　Ｖ：０～２．０％、
    　Ｗ：０～３．００％、
    　Ｇａ：０～０．０５％、
    　Ｃｏ：０～２．５０％、
    　Ｓｂ：０～２．５０％、
    　Ｔａ：０～２．５０％、
    　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％であり、
    　残部：Ｆｅおよび不純物であり、
    窒化物の平均粒子径が１０μｍ以下であり、鋼中の固溶Ｂ量が０．０１５質量％以下であるステンレス棒状鋼材。     The chemical composition is by mass%,
    C: 0.001 to 0.030%,
    Si: 0.01-4.00%,
    Mn: 0.01-2.00%,
    Ni: 0.01-4.00%,
    Cr: 8.0 to 35.0%,
    Mo: 0.01-5.00%,
    Cu: 0.01-2.00%,
    N: 0.001 to 0.030%,
    Al: Contains 7,000% or less,
    moreover,
    Ti: 0 to 2.00%,
    Nb: 0 to 2.00%,
    B: 0 to 0.1000%,
    It contains one or more selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more.
    Sn: 0 to 2.50%,
    V: 0-2.0%,
    W: 0 to 3.00%,
    Ga: 0-0.05%,
    Co: 0-2.50%,
    Sb: 0 to 2.50%,
    Ta: 0-2.50%,
    Ca: 0-0.05%,
    Mg: 0 to 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%,
    Remaining: Fe and impurities,
    A stainless rod-shaped steel material having an average particle size of a nitride of 10 μm or less and a solid solution B amount in steel of 0.015% by mass or less.
  3. 　前記化学組成が、質量％でさらに、下記第１群～第３群から選択される１群以上を含有する、請求項１または請求項２に記載のステンレス棒状鋼材。
    第１群　
    　Ｓｎ：０．０００１～２．５％、
    　Ｖ：０．００１～２．０％
    　Ｗ：０．０５～３．０％、
    　Ｇａ：０．０００４～０．０５％、
    　Ｃｏ：０．０５～２．５％、
    　Ｓｂ：０．０１～２．５％、および
    　Ｔａ：０．０１～２．５％、
    　から選択される一種以上。
    第２群
    　Ｃａ：０．０００２～０．０５％、
    　Ｍｇ：０．０００２～０．０１２％、
    　Ｚｒ：０．０００２～０．０１２％、および
    　ＲＥＭ：０．０００２～０．０５％、
    　から選択される一種以上。
    第３群
    　Ｐｂ：０．０００１～０．３０％、
    　Ｓｅ：０．０００１～０．８０％、
    　Ｔｅ：０．０００１～０．３０％、
    　Ｂｉ：０．０００１～０．５０％、
    　Ｓ：０．０００１～０．５０％、
    　Ｐ：０．０００１～０．３０％、
    　から選択される一種以上。     The stainless steel rod-shaped steel material according to claim 1 or 2, wherein the chemical composition further contains one or more groups selected from the following groups 1 to 3 in mass%.
    Group 1
    Sn: 0.0001 to 2.5%,
    V: 0.001 to 2.0%
    W: 0.05-3.0%,
    Ga: 0.0004-0.05%,
    Co: 0.05-2.5%,
    Sb: 0.01-2.5%, and Ta: 0.01-2.5%,
    One or more selected from.
    Group 2 Ca: 0.0002-0.05%,
    Mg: 0.0002 to 0.012%,
    Zr: 0.0002 to 0.012%, and REM: 0.0002 to 0.05%,
    One or more selected from.
    Group 3 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%,
    One or more selected from.
  4. 　圧縮率７０％で割れなきひずみ速度が０．１／ｓ以上である、請求項１～請求項３のいずれか１項に記載のステンレス棒状鋼材。 The stainless steel rod-shaped steel material according to any one of claims 1 to 3, wherein the compression rate is 70% and the strain rate without cracking is 0.1 / s or more.
  5. 　ドリル加工による穴深さ（工具寿命）が５０ｍｍ以上である、請求項１～請求項４のいずれか１項に記載のステンレス棒状鋼材。 The stainless steel rod-shaped steel material according to any one of claims 1 to 4, wherein the hole depth (tool life) by drilling is 50 mm or more.
  6. 　保磁力が５．０Ａ／ｍ以下である、請求項１～請求項５のいずれか１項に記載のステンレス棒状鋼材。 The stainless steel rod-shaped steel material according to any one of claims 1 to 5, wherein the coercive force is 5.0 A / m or less.
  7. 　請求項１～請求項６のいずれか一項に記載のステンレス棒状鋼材を用いた電磁部品。 An electromagnetic component using the stainless rod-shaped steel material according to any one of claims 1 to 6.
PCT/JP2021/042062 2020-11-19 2021-11-16 Stainless steel bar material and electromagnetic component WO2022107757A1 (en)

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JPH0344448A (en) 1989-07-11 1991-02-26 Daido Steel Co Ltd Stainless steel excellent in corrosion resistance
JPH0649606A (en) 1992-08-04 1994-02-22 Daido Steel Co Ltd Magnetic stainless steel
JPH0649605A (en) 1992-08-04 1994-02-22 Daido Steel Co Ltd Magnetic stainless steel
JP2000160302A (en) * 1998-11-19 2000-06-13 Sanyo Special Steel Co Ltd Electromagnetic stainless steel excellent in cold forgeability
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JP2006016665A (en) * 2004-07-01 2006-01-19 Nippon Steel & Sumikin Stainless Steel Corp Inexpensive stainless steel wire rod or steel wire having excellent corrosion resistance, cold workability and toughness and having magnetism
US20070166183A1 (en) * 2006-01-18 2007-07-19 Crs Holdings Inc. Corrosion-Resistant, Free-Machining, Magnetic Stainless Steel
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JPS59232258A (en) * 1983-06-14 1984-12-27 Sanyo Tokushu Seikou Kk Free-cutting, corrosion resistant and soft magnetic steel for bar or pipe with superior toughness
JPH0344448A (en) 1989-07-11 1991-02-26 Daido Steel Co Ltd Stainless steel excellent in corrosion resistance
JPH0649606A (en) 1992-08-04 1994-02-22 Daido Steel Co Ltd Magnetic stainless steel
JPH0649605A (en) 1992-08-04 1994-02-22 Daido Steel Co Ltd Magnetic stainless steel
JP2000160302A (en) * 1998-11-19 2000-06-13 Sanyo Special Steel Co Ltd Electromagnetic stainless steel excellent in cold forgeability
US20030086810A1 (en) * 2001-09-04 2003-05-08 Gunter Schnabel Cold-workable corrosion-resistant chromium steel
JP2006016665A (en) * 2004-07-01 2006-01-19 Nippon Steel & Sumikin Stainless Steel Corp Inexpensive stainless steel wire rod or steel wire having excellent corrosion resistance, cold workability and toughness and having magnetism
US20070166183A1 (en) * 2006-01-18 2007-07-19 Crs Holdings Inc. Corrosion-Resistant, Free-Machining, Magnetic Stainless Steel
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