WO2021065738A1 - フェライト系ステンレス鋼板およびその製造方法ならびにフェライト系ステンレス部材 - Google Patents

フェライト系ステンレス鋼板およびその製造方法ならびにフェライト系ステンレス部材 Download PDF

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WO2021065738A1
WO2021065738A1 PCT/JP2020/036379 JP2020036379W WO2021065738A1 WO 2021065738 A1 WO2021065738 A1 WO 2021065738A1 JP 2020036379 W JP2020036379 W JP 2020036379W WO 2021065738 A1 WO2021065738 A1 WO 2021065738A1
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Prior art keywords
steel sheet
stainless steel
content
crystal orientation
rolling
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PCT/JP2020/036379
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English (en)
French (fr)
Japanese (ja)
Inventor
航 西村
井上　宜治
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Nippon Steel Stainless Steel Corp
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Nippon Steel Stainless Steel Corp
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Priority to EP20871144.0A priority Critical patent/EP4043597A4/en
Priority to CN202080069794.0A priority patent/CN114502760B/zh
Priority to KR1020227014596A priority patent/KR102748718B1/ko
Priority to US17/641,186 priority patent/US12270096B2/en
Priority to JP2021551196A priority patent/JP7268182B2/ja
Priority to MX2022003956A priority patent/MX2022003956A/es
Publication of WO2021065738A1 publication Critical patent/WO2021065738A1/ja
Anticipated expiration legal-status Critical
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Definitions

  • the present invention relates to a ferritic stainless steel sheet, a method for manufacturing the same, and a ferritic stainless member.
  • Ferritic stainless steel sheets are used in a wide range of fields such as home appliances, kitchen equipment, and electronic equipment. In recent years, the application of stainless steel sheets has been studied as a material used for exhaust pipes, fuel tanks, and pipes of automobiles and motorcycles.
  • the above-mentioned exhaust system parts are required to have corrosion resistance and heat resistance in the exhaust environment and the fuel environment. Further, the above-mentioned parts are manufactured by press working from a steel plate or by forming a steel plate into a steel pipe having a predetermined size (diameter) and then forming the steel plate into a desired shape. Therefore, the material steel sheet used for the parts is required to have high workability.
  • the component configuration has become complicated, and along with this, the shape of the component itself has also become complicated.
  • the exhaust system member not only the above-mentioned material properties such as corrosion resistance and heat resistance are required, but also cost is emphasized.
  • various efforts to reduce the number of steps in the molding process and the welding process at the time of forming the part are being studied.
  • One example is the integral molding of parts. In the conventional construction method, a method of forming a steel plate or a steel pipe and then welding and joining with other parts has been used.
  • the integral molding process is to integrally mold a steel plate or a steel pipe by combining various processes (deep drawing, overhanging, bending, pipe expansion, etc.) with respect to a portion previously joined by welding. ..
  • the welding process can be omitted and the cost can be reduced, but the stainless steel sheet used for the above member is required to have higher workability.
  • the stainless steel plate used for the exhaust system parts is required to have various workability.
  • workability such as deep drawing property and hole expansion property is important characteristics.
  • bendability, overhangability, and tube expandability may also be required.
  • ferritic stainless steel sheets are cheaper than austenitic stainless steel sheets. Therefore, from the viewpoint of cost, it can be said that it is suitable as a steel sheet used for the above members.
  • ferritic stainless steel sheets are inferior in formability, their uses and shapes may be limited. For this reason, when a ferritic stainless steel sheet is used as the above member, the parts used thereof may be limited.
  • Patent Document 1 discloses a steel sheet having improved workability by controlling conditions such as annealing temperature and time after hot rolling, and a method for manufacturing the same.
  • Patent Document 1 specifically discloses a steel sheet having an average r value of 1.2 or more.
  • the crystal orientation of the steel sheet is controlled by controlling the structure of the steel sheet in the annealing process of the hot-rolled steel sheet. As a result, a steel sheet having high workability can be obtained.
  • Patent Document 2 discloses a steel sheet in which annealing of a hot-rolled steel sheet is omitted and workability is improved, and a method for manufacturing the same. Specifically, Patent Document 2 discloses a steel sheet having an average r value of about 1.3 and a plate thickness of 0.7 mm. In the method for manufacturing a steel sheet, the rolling reduction, the friction coefficient between the roll and the steel sheet, and the temperature on the exit side of the finish rolling mill are controlled during the finish rolling in the hot rolling process. Furthermore, the annealing of the hot-rolled plate is omitted. As a result, in Patent Document 2, the number of steps can be reduced and a steel sheet having higher workability can be obtained.
  • Patent Document 3 discloses a steel sheet having improved workability by controlling hot spreading conditions and performing two-step cold spreading and annealing, and a method for manufacturing the same. Specifically, Patent Document 3 discloses a steel sheet having an average r value of about 2.3 at the maximum and a plate thickness of 0.8 mm.
  • the above-mentioned method for manufacturing a steel sheet controls the temperature and reduction rate during rough rolling and finish rolling of hot rolling, and combines intermediate cold rolling and intermediate annealing at 650 to 900 ° C. As a result, the structure before the finish cold rolling is controlled to obtain a highly workable steel sheet.
  • Japanese Unexamined Patent Publication No. 2005-105347 Japanese Unexamined Patent Publication No. 2000-265215 Japanese Unexamined Patent Publication No. 2003-138349
  • the deep drawing property is improved by controlling the crystal orientation using the Rankford value (hereinafter referred to as "r value”) as an index.
  • r value the Rankford value
  • the rolling reduction is increased during rolling and the annealing temperature is raised so that the rolled surface and the ⁇ 111 ⁇ surface become parallel to each other (hereinafter, also referred to as “ ⁇ 111 ⁇ crystal grains”). It is effective to develop.) In the entire thickness of the steel sheet.
  • the plate thickness may be 1.0 mm or more.
  • the reduction rate is inevitably small. Therefore, it is conceivable that the ⁇ 111 ⁇ crystal grains, which are effective for improving the deep drawing property, may not be sufficiently formed and the texture may not be developed only by increasing the rolling reduction rate.
  • Patent Documents 1 to 3 when the hot-rolled plate is annealed in the manufacturing process, the processing strain at the time of hot-rolling disappears. Therefore, it is considered that the total amount of dislocations that is the driving force for recrystallization is reduced and the ⁇ 111 ⁇ crystal grains are not sufficiently developed. In addition, an increase in the number of steps greatly reduces productivity.
  • the steel sheet disclosed in Patent Document 2 is assumed to be a thin steel sheet having a thickness of 1.0 mm or less. Further, even if the manufacturing method described in Patent Document 2 is used, it is considered that the r value is insufficient for a steel plate having a plate thickness of 1.0 mm or more. Further, in Patent Document 3, in the steel sheet having a plate thickness of 1.0 mm or more assumed in the present application, the total rolling ratio is insufficient even after two-step cold rolling and annealing, and ⁇ 111 ⁇ crystal grains are not sufficiently developed. Can be considered. In addition, an increase in the number of steps greatly reduces productivity.
  • recrystallizing the steel sheet structure in the process of being manufactured by performing hot-rolled sheet annealing, intermediate annealing, and / or heat treatment may promote randomization of crystal orientation.
  • the in-plane anisotropy ( ⁇ r) of the steel sheets is increased, which may lead to defects such as cracks during steel sheet forming such as deep drawing or hole expansion.
  • An object of the present invention is to solve the above-mentioned problems, to solve the above-mentioned problems, to have excellent workability, particularly deep drawing property, a ferritic stainless steel plate for exhaust parts having a plate thickness of 1.0 mm or more, a manufacturing method thereof, and a ferrite for exhaust parts.
  • the purpose is to provide ferritic stainless steel members.
  • the present invention has been made to solve the above problems, and the gist of the present invention is the following ferritic stainless steel sheet, its manufacturing method, and a ferritic stainless member for exhaust system parts.
  • the chemical composition is mass%.
  • each element symbol in the above formula (i) represents the content (mass%) of each element contained in the steel, and if it is not contained, it is set to zero, and each symbol in the above formulas (ii) and (iii).
  • the chemical composition is mass%.
  • W 0.0005-2.0%
  • Sn 0.01 to 0.50%
  • Mg 0.0002 to 0.0100%
  • B 0.0002 to 0.005%
  • V 0.05 to 1.0%
  • Mo 0.2 to 3.0%
  • the chemical composition is mass%. Al: 0.003 to 0.5%, Cu: 0.1-2.0%, Zr: 0.05-0.30%, Co: 0.05-0.50%, Sb: 0.01 to 0.50%, and REM: 0.001 to 0.05%,
  • the chemical composition is mass%. Ni: 0.1-2.0%, Ca: 0.0001 to 0.0030%, Ta: 0.01-0.10%, and Ga: 0.0002-0.1%,
  • a ferrite-based stainless steel member for exhaust system parts of automobiles or motorcycles which is made of the ferrite-based stainless steel sheet according to any one of (1) to (5) above.
  • the average heating rate from the heating start temperature to the recrystallization start temperature Ts (° C.) calculated by the following formula (viii) is set to 15 ° C./s or more, and the recrystallization start temperature Ts (° C.)
  • the average heating rate from to the annealing temperature Tf (° C.) is set to 10 ° C./s or less.
  • FIG. 1 is a diagram showing the relationship between the sum of ⁇ 111 ⁇ ⁇ 112> crystal orientation intensities of a steel sheet and the average r value.
  • Figure 2 is a diagram showing the relationship between the ⁇ 322 ⁇ ⁇ 236> sum and r 45 of the crystal orientation strength of the steel sheet.
  • the present inventors have added alloying elements such as Nb, which are highly effective in suppressing recrystallization, within the scope of the present invention, thereby suppressing recovery and recrystallization during hot spreading and causing heat spreading strain.
  • alloying elements such as Nb
  • C 0.001 to 0.020%
  • C deteriorates toughness, corrosion resistance and oxidation resistance, and C dissolved in the matrix inhibits the development of aggregates in the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation. Therefore, the smaller the C content, the better.
  • the C content shall be 0.020% or less.
  • the C content is set to 0.001% or more.
  • the C content is preferably 0.002% or more, and preferably 0.010% or less.
  • the C content is more preferably 0.003% or more, and more preferably 0.008% or less.
  • Si 0.02 to 1.5%
  • Si is an element that improves oxidation resistance and high-temperature strength in addition to being a deoxidizing element. Further, by containing Si, the amount of oxygen in the steel is reduced, and the textures of the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation are easily developed. Therefore, the Si content is set to 0.02% or more. However, if Si is contained in an amount of more than 1.5%, the steel sheet becomes remarkably hard and the bendability deteriorates during steel pipe processing.
  • the Si content should be 1.5% or less.
  • the Si content is preferably more than 0.30%, more preferably 0.80% or more.
  • the Si content is preferably 1.2% or less in consideration of toughness and pickling property during steel sheet production. Further, the Si content is more preferably 1.0% or less.
  • Mn 0.02 to 1.5% Mn forms MnCr 2 O 4 or Mn O at high temperatures to improve scale adhesion. Therefore, the Mn content is set to 0.02% or more.
  • the Mn content is preferably 0.10% or more, and more preferably 0.20% or more. However, if Mn is contained in an amount of more than 1.5%, the amount of oxide increases and abnormal oxidation is likely to occur. In addition, Mn produces a compound with S and inhibits the development of aggregates in the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation. Therefore, the Mn content is set to 1.5% or less.
  • the Mn content is preferably 1.0% or less, and the Mn content is more preferably 0.8% or less. Further, considering the flat cracks caused by the oxide of the welded portion of the steel pipe, the Mn content is more preferably 0.3% or less.
  • P 0.01-0.05% Since P is a solid solution strengthening element like Si, it is preferable to reduce its content from the viewpoint of material and toughness. Since P dissolved in the matrix inhibits the development of aggregates in the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation, the P content is set to 0.05% or less.
  • the P content is set to 0.01% or more. Further, in consideration of production cost and oxidation resistance, the P content is preferably 0.015% or more, and preferably 0.03% or less.
  • S 0.0001-0.01%
  • S is preferably reduced as much as possible from the viewpoint of material, corrosion resistance and oxidation resistance.
  • an excessive content of S produces a compound with Ti or Mn, which makes it easy for cracks originating from inclusions to occur when bending the steel pipe.
  • the presence of these compounds inhibits the development of aggregates in the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation.
  • the S content should be 0.01% or less.
  • the S content is set to 0.0001% or more.
  • the S content is preferably 0.0005% or more, and preferably 0.005% or less.
  • Cr 13.0 to 20.0% Cr is an element necessary for ensuring high temperature strength and oxidation resistance, which are the most important characteristics of exhaust components. Therefore, the Cr content is set to 13.0% or more. However, if the Cr content exceeds 20.0%, the toughness is lowered and the manufacturability is deteriorated, and in particular, brittle cracks or poor bendability of the welded portion of the steel pipe occur.
  • the Cr content is set to 20.0% or less.
  • the Cr content is preferably 14.0% or more.
  • the Cr content is preferably 15.0% or more, and preferably 18.0% or less.
  • N 0.001 to 0.030% N, like C, reduces low temperature toughness, workability, and oxidation resistance.
  • N dissolved in the matrix inhibits the development of aggregates in the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation, it is preferable to reduce the content as much as possible. Therefore, the N content is set to 0.030% or less.
  • the N content is set to 0.001% or more.
  • the N content is preferably 0.005% or more, and preferably 0.020% or less.
  • Nb 0.005% or more and less than 0.10% Nb has an effect of suppressing recovery and recrystallization and increasing the amount of accumulated hot-rolled strain in the hot rolling step.
  • This hot rolling strain together with the cold rolling strain introduced in the cold rolling process, strongly contributes to the development of ⁇ 111 ⁇ .
  • Nb binds to C, N, and S to improve corrosion resistance, intergranular corrosion resistance, and deep drawing resistance. Further, in a high temperature region, the solid solution strengthening ability and the precipitation strengthening ability are high, and the high temperature strength and the thermal fatigue characteristics are improved.
  • the Nb content is set to 0.005% or more.
  • the Nb content is preferably 0.010% or more, and more preferably 0.015% or more.
  • excessive Nb content significantly delays the progress of recrystallization in the final annealing after cold rolling and inhibits the development of ⁇ 111 ⁇ . Therefore, the Nb content is set to less than 0.10%. Further, considering the influence on recrystallization, the Nb content is preferably 0.08% or less, and more preferably 0.05% or less.
  • each element symbol in the above formula (i) represents the content (mass%) of each element contained in the steel, and if it is not contained, it is set to zero.
  • Ti has the effect of combining with C, N, and S to improve corrosion resistance, intergranular corrosion resistance, and deep drawing property. Further, Ti nitride becomes a nucleus during slab casting, thereby increasing the equiaxed crystal ratio, developing the texture of the product plate in the ⁇ 111 ⁇ direction, and improving the r value.
  • the ferrite-based stainless steel sheet according to the present invention needs to satisfy the above equation (i). However, if Ti is contained in an amount of more than 0.30%, the solid solution Ti hardens the steel sheet and lowers the toughness. Therefore, the Ti content is set to 0.30% or less. Further, in consideration of manufacturing cost and the like, the Ti content is preferably 0.05% or more, and preferably 0.25% or less.
  • W 0-2.0% W, like Nb, suppresses recovery and recrystallization in the hot rolling process and increases the accumulation of hot rolling strain. Furthermore, the effect of increasing high temperature strength is also high. Therefore, it may be contained as needed. However, excessive content of W results in deterioration of toughness and reduced elongation. In addition, the amount of the Laves phase, which is an intermetallic compound phase, is increased, which inhibits the development of the texture of the ⁇ 111 ⁇ orientation and lowers the r value. Therefore, the W content is set to 2.0% or less. Further, in consideration of manufacturing cost and manufacturability, the W content is preferably 1.5% or less.
  • the W content is preferably 0.0005% or more.
  • the W content is more preferably 0.1% or more.
  • Sn 0 to 0.50% Sn causes compositional supercooling during slab casting and increases equiaxed crystal ratio. As a result, the texture of the product plate in the ⁇ 111 ⁇ direction is developed, and the r value and the expandability of the steel pipe are improved.
  • the Sn content is set to 0.50% or less. Further, in consideration of high temperature characteristics, manufacturing cost and toughness, the Sn content is preferably 0.30% or less. On the other hand, in order to obtain the above effect, the Sn content is preferably 0.01% or more.
  • Mg 0 to 0.0100% Like Al, Mg forms Mg oxide in molten steel and has a deoxidizing effect. In addition, in Mg, finely crystallized Mg oxide becomes a nucleus, which increases the equiaxed crystal ratio of the slab, and promotes the precipitation of Nb and Ti-based fine precipitates in the subsequent steps. Specifically, when the above-mentioned precipitates are finely precipitated in the hot-rolling step, they become recrystallized nuclei in the hot-rolling step and the subsequent annealing step of the hot-rolled plate. As a result, a very fine recrystallized structure can be obtained. This recrystallized structure contributes to the development of the texture of the ⁇ 111 ⁇ orientation and also to the improvement of toughness. Therefore, it may be contained as needed.
  • the Mg content is set to 0.0100% or less.
  • the Mg content is preferably 0.0002% or more. Further, in consideration of the refining cost, the Mg content is more preferably 0.0003% or more, and preferably 0.0020% or less.
  • B 0 to 0.005% B has the effect of improving the grain boundary strength, secondary processability, low temperature toughness, and high temperature strength in the medium temperature range by segregating at the grain boundaries. Therefore, it may be contained as needed.
  • the B by making content exceeds 0.005%, B compounds such as Cr 2 B is produced, intergranular corrosion, and reduce the fatigue properties. In addition, it inhibits the development of aggregates in the ⁇ 111 ⁇ orientation, resulting in a decrease in r-value. Therefore, the B content is set to 0.005% or less.
  • the B content is preferably 0.0002% or more. Further, in consideration of weldability and manufacturability, the B content is preferably 0.0003% or more, and preferably 0.0010% or less.
  • V 0 to 1.0%
  • V has the effect of combining with C or N to improve corrosion resistance and heat resistance. Therefore, it may be contained as needed. However, when V is contained in excess of 1.0%, coarse carbonitride is produced and the toughness is lowered. Furthermore, the development of aggregates in the ⁇ 111 ⁇ orientation is inhibited. Therefore, the V content is set to 1.0% or less. In addition, in consideration of manufacturing cost and manufacturability, the V content is preferably 0.2% or less. On the other hand, in order to obtain the above effect, the V content is preferably 0.05% or more.
  • Mo 0-3.0% Mo, like Nb and W, suppresses recovery and recrystallization in the hot rolling process and increases the accumulation of hot rolling strain.
  • Mo is an element that improves corrosion resistance, and is an element that suppresses crevice corrosion, especially in pipe materials having a crevice structure.
  • Mo has a high effect of improving high temperature strength. Therefore, it may be contained as needed.
  • the Mo content is set to 3.0% or less. Further, in consideration of manufacturing cost and manufacturability, the Mo content is preferably 1.5% or less. On the other hand, the above effect is exhibited when the Mo content is 0.2% or more. Therefore, the Mo content is preferably 0.2% or more.
  • Al 0 to 0.5%
  • Al may be used as a deoxidizing element, and may be contained as necessary in order to improve high temperature strength and oxidation resistance. In addition, it becomes a precipitation site of TiN and Laves phase, and the precipitate is made finer to improve low temperature toughness.
  • content of Al in excess of 0.5% results in elongation, poor weldability and surface quality. It also forms coarse Al oxides and reduces low temperature toughness. Therefore, the Al content is set to 0.5% or less.
  • the Al content is preferably 0.003% or more. Further, in consideration of the refining cost, the Al content is preferably 0.01% or more, and preferably 0.1% or less.
  • Cu 0-2.0%
  • Cu has the effect of improving the corrosion resistance and improving the high-temperature strength in the medium temperature range by precipitating Cu that is solid-solved in the matrix, so-called ⁇ -Cu. Therefore, it may be contained as needed.
  • the Cu content is set to 2.0% or less. Further, in consideration of oxidation resistance and manufacturability, the Cu content is preferably less than 1.5%. On the other hand, in order to obtain the above effect, the Cu content is preferably 0.1% or more.
  • Zr 0 to 0.30%
  • Zr is an element that improves oxidation resistance, and may be contained if necessary. However, if Zr is contained in an amount of more than 0.30%, the manufacturability such as toughness and pickling property is significantly lowered. In addition, the compound of Zr, carbon and nitrogen is coarsened. As a result, the steel sheet structure at the time of thermal annealing is coarse-grained and the r value is lowered. Therefore, the Zr content is set to 0.30% or less. Further, considering the production cost, the Zr content is preferably 0.20% or less. On the other hand, in order to obtain the above effect, the Zr content is preferably 0.05% or more.
  • Co 0 to 0.50%
  • Co is an element that improves high-temperature strength and may be contained if necessary.
  • excessive content of Co reduces toughness and workability. Therefore, the Co content is set to 0.50% or less. Further, considering the production cost, the Co content is preferably 0.30% or less. On the other hand, in order to obtain the above effect, the Co content is preferably 0.05% or more.
  • Sb 0 to 0.50% Sb may be contained if necessary in order to segregate at the grain boundaries and increase the high temperature strength. However, if Sb is contained in an amount of more than 0.50%, excessive segregation occurs and the low temperature toughness of the welded portion is lowered. Therefore, the Sb content is set to 0.50% or less. Further, in consideration of high temperature characteristics, manufacturing cost and toughness, the Sb content is preferably 0.30% or less. On the other hand, in order to obtain the above effect, the Sb content is preferably 0.01% or more.
  • REM 0-0.05% REM (rare earth element) has the effect of refining various precipitates and improving toughness and oxidation resistance. Therefore, it may be contained as needed. However, if the REM content exceeds 0.05%, the castability is significantly reduced. Therefore, the REM content is set to 0.05% or less. On the other hand, in order to obtain the above effect, the REM content is preferably 0.001% or more. In consideration of refining cost and manufacturability, the REM content is more preferably 0.003% or more, and preferably 0.01% or less.
  • REM is a general term for 17 elements including 15 elements of lanthanoids and Y and Sc. One or more of these 17 elements can be contained in the steel material, and the REM content means the total content of these elements.
  • Ni 0-2.0% Since Ni is an element that improves toughness and corrosion resistance, it may be contained if necessary. However, when Ni is contained in an amount of more than 2.0%, an austenite phase is formed, which inhibits the development of the texture of the ⁇ 111 ⁇ orientation. As a result, the r value is lowered, and the bendability of the steel pipe is remarkably lowered. Therefore, the Ni content is set to 2.0% or less. Further, in consideration of the production cost, the Ni content is preferably 0.5% or less. On the other hand, in order to obtain the above effect, the Ni content is preferably 0.1% or more.
  • Ca 0 to 0.0030% Since Ca is an effective element as a desulfurization element, it may be contained if necessary. However, when the Ca content exceeds 0.0030%, coarse CaS is produced, which reduces toughness and corrosion resistance. Therefore, the Ca content is set to 0.0030% or less. On the other hand, in order to obtain the above effect, the Ca content is preferably 0.0001% or more. In consideration of refining cost and manufacturability, the Ca content is more preferably 0.0003% or more, and preferably 0.0020% or less.
  • Ta 0 to 0.10% Ta may be contained if necessary because it binds to C and N and contributes to the improvement of toughness. However, if the Ta content exceeds 0.10%, the manufacturing cost increases and the manufacturability is significantly lowered. Therefore, the Ta content is set to 0.10% or less. On the other hand, in order to obtain the above effect, the Ta content is preferably 0.01% or more. In consideration of refining cost and manufacturability, the Ta content is more preferably 0.02% or more, and preferably 0.08% or less.
  • Ga 0-0.1% Ga has the effects of improving corrosion resistance and suppressing hydrogen embrittlement. Therefore, it may be contained as needed.
  • the Ga content is 0.1% or less.
  • the Ga content is preferably 0.0002% or more in consideration of the formation of sulfides and hydrides. From the viewpoint of manufacturing cost and manufacturability, ductility and toughness, the Ga content is more preferably 0.0005% or more, and preferably 0.02% or less.
  • the balance is Fe and unavoidable impurities.
  • the "unavoidable impurity” is a component mixed by various factors in the raw material such as ore and scrap, and various factors in the manufacturing process when the steel material is industrially manufactured, and is within a range that does not adversely affect the present invention. Means what is acceptable.
  • the crystal grain size number is 6.0 or more, preferably 6.5 or more. This is because if the crystal grain size number of the steel sheet is less than 6.0, it causes rough skin such as orange peel. On the other hand, the crystal grain size of the steel sheet is preferably 9.0 or less because it is necessary to sufficiently grow the crystal grains in order to develop the ⁇ 111 ⁇ ⁇ 112> orientation.
  • the crystal particle size number is measured by observing with an optical microscope in accordance with JIS G0551.
  • the sum of the crystal orientation intensities of ⁇ 111 ⁇ ⁇ 112> is less than 9.0, the texture of the ⁇ 111 ⁇ ⁇ 112> orientation cannot be developed, and a steel sheet having good deep drawing property can be obtained. I can't. ⁇ 111 ⁇ ⁇ 112>
  • the sum of the crystal orientation intensities is 9.0 or more, preferably 10.0 or more, and more preferably 11.0 or more.
  • the texture of ⁇ 236> orientation ⁇ 322 ⁇ is developed primarily to improve the value of r 45 is, workability is good, including the deep drawability. Therefore, in the steel sheet according to the present invention, the sum of the ⁇ 322 ⁇ ⁇ 236> crystal orientation strengths at the center of the plate thickness and the 1/8 part of the plate thickness (hereinafter, simply “ ⁇ 322 ⁇ ⁇ 236> sum of the crystal orientation strengths”. It is necessary to satisfy the above equation (iii).
  • the sum of the ⁇ 322 ⁇ ⁇ 236> crystal orientation intensities is 9.0 or more, preferably 10.0 or more, and more preferably 11.0 or more.
  • the crystal orientation strength at the center of the plate thickness which is generally measured, but also the crystal orientation strength at 1/8 part of the plate thickness is measured. Is going. This is because the measurement of 1/8 part of the plate thickness is most suitable for investigating the influence of the effect of suppressing recovery and recrystallization caused by the addition of Nb in the hot rolling process.
  • the shear deformation of cold rolling which affects the formation of the recrystallized structure during final annealing, is particularly likely to occur near the surface of the plate thickness, and in order to investigate the effect, it is necessary to use 1/8 part of the plate thickness. This is because the measurement of
  • the hot spreading strain is reduced due to remarkably recovery and recrystallization in the surface layer to 1/8 of the plate thickness where shear strain is likely to be introduced.
  • the crystal orientation strength of the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation is reduced.
  • an X-ray diffractometer manufactured by Rigaku Denki Kogyo Co., Ltd.
  • Mo-K ⁇ rays are used to reveal the central region of the plate thickness center region (the central region is revealed by a combination of mechanical polishing and electrolytic polishing).
  • (200), (110), and (211) positive electrode point diagrams were obtained, and an ODF (Orientation Distribution Function) was obtained from this using a spherical harmonic function.
  • the ⁇ 111 ⁇ ⁇ 112> crystal orientation intensity and the ⁇ 322 ⁇ ⁇ 236> crystal orientation intensity were calculated.
  • the crystal orientation strength of the ferrite phase which is the parent phase, is measured.
  • each r value The r value of the steel sheet according to the present invention is measured by the following method according to JIS Z 2254. Then, after obtaining the r values of the test piece in the directions parallel to the rolling direction, the 45 ° direction, and the 90 ° direction, the average r value is calculated.
  • the r value is calculated by the following method. Specifically, a JIS No. 13B tensile test piece was sampled from a cold-rolled annealed plate from parallel, 45 °, and 90 ° directions with respect to the rolling direction, and after applying a strain of 10 to 20%, the following (a) ) Is calculated by substituting each value into the formula. Further, using the following (iv) wherein the average r value (hereinafter referred to as "r m".) Is calculated.
  • r m (r 0 + 2r 45 + r 90) / 4 ⁇ (iv)
  • r 0 r value in the rolling direction
  • r 45 r value in the 45 ° direction with respect to the rolling direction
  • r 90 r value in the 90 ° direction with respect to the rolling direction
  • the crystal orientation intensities of the ⁇ 111 ⁇ ⁇ 112> orientation and the ⁇ 322 ⁇ ⁇ 236> orientation are set to values satisfying the above equations (ii) and (iii). Then, it is preferable that the equations (ii) and (iii) are satisfied and the following equations (v) and (vi) are satisfied. r m ⁇ 1.50 ⁇ (v) r 45 ⁇ 1.30 ⁇ ⁇ ⁇ (vi)
  • the plate thickness of the ferritic stainless steel plate according to the present invention is 1.0 mm or more.
  • the thickness of the ferritic stainless steel sheet is preferably 1.2 mm or more, and more preferably 1.5 mm or more.
  • the thickness of the steel sheet is preferably 3.0 mm or less, more preferably 2.5 mm or less.
  • the ferritic stainless steel sheet according to the present invention is preferably used for exhaust system parts such as automobiles and motorcycles. Further, it is preferable to use the ferritic stainless steel sheet according to the present invention as a material as a ferritic stainless steel member for exhaust parts of automobiles or motorcycles.
  • the method for producing a steel sheet of the present invention includes, for example, the steps of steelmaking-hot rolling-pickling-cold rolling-annealing.
  • steelmaking a method in which steel having the above chemical composition is melted in a converter and subsequently subjected to secondary refining is preferable.
  • the molten steel melted is made into a slab according to a known casting method (continuous casting).
  • Hot rolling step Subsequently, the slab is heated at the following temperature and hot-rolled to a predetermined plate thickness by continuous rolling.
  • the cast slab is preferably heated at 1100 to 1250 ° C. This is because if the heating temperature of the slab is less than 1100 ° C, the heating temperature is too low and scale generation is reduced, and the rolling roll and the steel material are seized, which deteriorates the surface quality and adversely affects the subsequent process. is there.
  • the heating temperature of the slab exceeds 1250 ° C., the slab deforms at a high temperature due to its own weight, which is not preferable. Further, in consideration of productivity and surface defects, the heating temperature of the slab is preferably 1150 to 1200 ° C. In the present invention, the heating temperature of the slab and the hot rolling start temperature are synonymous.
  • the finishing temperature is 900 ° C. or lower
  • the slab is a hot-rolled steel sheet.
  • the effect of suppressing recovery and recrystallization due to the low temperature of finish rolling during hot rolling is particularly large at 1/8 part of the plate thickness from the surface layer where shear strain is strongly introduced during hot rolling. This is because the recrystallization generated by the shear strain as a driving force can suppress the disappearance of the thermal spread strain.
  • ⁇ 111 ⁇ ⁇ 112> can be mentioned as a typical one.
  • Hot-rolled sheet pickling step it is preferable that the hot-rolled steel sheet is pickled without annealing to obtain a pickled steel sheet. This is different from a general manufacturing method in which a hot-rolled steel sheet is usually annealed by hot-rolling sheet to obtain a sized recrystallized structure. In general, performing a microstructure control the hot-rolled sheet annealing is facilitated, Netsunobeibitsu disappeared, ⁇ 111 ⁇ ⁇ 112> other to prevent the development of the crystal orientation, to improve the r 45 ⁇ 322 ⁇ ⁇ 236 > Crystal orientation does not develop in the annealing process after cold rolling.
  • the ⁇ 322 ⁇ ⁇ 236> crystal orientation develops more strongly when a steel sheet with a developed texture called ⁇ -fiber ( ⁇ 011 ⁇ // RD ( ⁇ 100 ⁇ to ⁇ 111 ⁇ ⁇ 011>)) is annealed.
  • ⁇ -fiber ⁇ 011 ⁇ // RD ( ⁇ 100 ⁇ to ⁇ 111 ⁇ ⁇ 011>)
  • This ⁇ -fiber is developed by hot rolling and cold rolling in a ferritic stainless steel sheet.
  • the ⁇ -fiber developed during hot rolling disappears once before cold rolling, and the crystal orientation is randomized. For this reason, hot-rolled sheet annealing is not performed on the steel sheet related to this production.
  • the pickled steel sheet is cold-rolled at a reduction rate of 60% or more using a rolling mill having a roll diameter of 400 mm or more to obtain a cold-rolled steel sheet.
  • a rolling mill having a roll diameter of 400 mm or more to obtain a cold-rolled steel sheet.
  • the roll diameter it is possible to suppress the introduction of shear strain near the surface of the steel sheet during cold rolling.
  • Shear deformation introduced by shear strain becomes a nucleation site of random orientation grains and must be suppressed.
  • the rolling reduction ratio for cold rolling is preferably 60% or more, and more preferably 70% or more.
  • Annealing temperature The final annealing after cold rolling needs to be annealed at a sufficiently high temperature for the development of ⁇ 111 ⁇ ⁇ 112> recrystallized grains. At the same time, annealing at an excessively high temperature causes coarsening of crystal grains and causes rough skin such as orange peel. Further, the metal structure of the steel sheet according to the present invention needs to have a fine structure having a crystal grain size number of 6.0 or more. Therefore, it is preferable that the cold-rolled steel sheet is annealed at an annealing temperature Tf (° C.) that satisfies the following equation (vii). 800 ⁇ Tf (° C) ⁇ 950 ... (vii)
  • the annealing temperature Tf (° C.) is preferably 800 ° C. or higher.
  • the annealing temperature Tf (° C.) is preferably 950 ° C. or lower.
  • Heating rate it is preferable to control the time from the heating start temperature (heating start temperature) to the time when the average heating rate reaches the target temperature.
  • the crystal grains in the ⁇ 111 ⁇ ⁇ 112> orientation are more likely to occur in the early stage of recrystallization than the crystal grains in other orientations. Further, the crystal grains in the ⁇ 111 ⁇ ⁇ 112> orientation grow by grain during annealing and develop by eclipsing the crystal grains in other orientations.
  • the steel sheet temperature is first brought to the recrystallization start temperature Ts (° C.) by rapid heating, and then slowly raised to the annealing temperature Tf (° C.) in order to grow the crystal grains in the ⁇ 111 ⁇ ⁇ 112> orientation. , It is preferable to proceed with recrystallization.
  • Ts (° C.) is calculated by the following equation (viii), but more preferably, Ts (° C.) satisfies the following equation (xi). This is because, in the steel sheet, the texture of the ⁇ 111 ⁇ ⁇ 112> orientation is particularly strongly developed. 700 ⁇ Ts (° C) ⁇ Tf (° C) -100 ... (viii)
  • Ts (° C.) 700+ (1-X / 100) x 130 ... (ix)
  • X Cold rolling reduction rate
  • the average heating rate from the heating start temperature to the recrystallization start temperature Ts (° C.) is preferably 15 ° C./s or more, and more preferably 20 ° C./s or more. Further, the average heating rate from the recrystallization start temperature Ts (° C.) to the annealing temperature Tf (° C.) is preferably 10 ° C./s or less, and more preferably 5 ° C./s or less.
  • the texture of the ⁇ 322 ⁇ ⁇ 236> orientation and the texture of the ⁇ 111 ⁇ ⁇ 112> orientation develop at the same time. From these, the ferritic stainless steel sheet according to the present invention can be obtained.
  • the slab thickness, hot-rolled plate thickness, etc. may be appropriately designed. Further, in cold rolling, roll roughness, rolling oil, number of rolling passes, rolling speed, rolling temperature and the like may be appropriately selected. If necessary, the annealing may be carried out by bright annealing in which the annealing is performed in a non-oxidizing atmosphere such as hydrogen gas or nitrogen gas. Further, annealing may be carried out in the air. Further, after annealing, a tension leveler step for temper rolling or shape correction may be carried out, or a plate may be passed through.
  • the steel plate manufactured by the above method is, for example, a member for exhaust parts. These members are press-processed from a steel plate or formed into a desired shape after the steel plate is formed into a steel pipe of a predetermined size (diameter).
  • the pickled hot-rolled steel sheet is cold-rolled to the thickness shown in Table 2 at a reduction rate of 60% or more using a roll having a diameter of 400 to 500 mm, and continuously annealed-pickled to obtain the steel sheet. Obtained.
  • the annealing conditions at this time are from the annealing temperature Tf (° C.), the recrystallization start temperature Ts (° C.), the heating rate from the heating start temperature to the recrystallization start temperature Ts (° C.), and the recrystallization start temperature Ts (° C.).
  • the manufacturing method in a suitable range of the present invention is used for both the heating rate up to the annealing temperature Tf (° C.).
  • the obtained steel sheet was measured for grain size number, crystal orientation strength, and r value.
  • the crystal grain size number was measured by observing with an optical microscope in accordance with JIS G0551.
  • crystal orientation intensity measurement an X-ray diffractometer (manufactured by Rigaku Denki Kogyo Co., Ltd.) is used, and Mo-K ⁇ rays are used to reveal the central region of the plate thickness (the central region is revealed by a combination of mechanical polishing and electrolytic polishing). (200), (110), and (211) positive electrode point diagrams of (200), (110), and (211) were obtained, and ODF (Orientation Distribution Function) was obtained from this using a spherical harmonic function. Based on this measurement result, the ⁇ 111 ⁇ ⁇ 011> crystal orientation intensity and the ⁇ 322 ⁇ ⁇ 236> crystal orientation intensity were calculated. In the present invention, the crystal orientation strength of the ferrite phase, which is the parent phase, was measured.
  • r value it is carried out by the above-mentioned method according to JIS Z 2254, test pieces are collected from parallel, 45 ° and 90 ° directions with respect to the rolling direction, and the average r value is calculated after obtaining the r value. did. Specifically, JIS No. 13B tensile test piece was sampled, and after applying a strain of 10 to 20% in the direction of parallel to the rolling direction, the direction of 45 °, and the direction of 90 °, the above value was calculated by a predetermined method. .. The workability (deep drawing property) was evaluated based on the measured r value. Specifically, and a r m ⁇ 1.50, was assessed in the case of r 45 ⁇ 1.30 and a good processability (deep drawability).
  • Inventive Examples B1 to B20 using steels having the chemical composition specified in the present invention have the crystal orientation strength (organization) of the ferrite phase required in the present invention. In addition to being realized, the crystal grain size number was satisfied, and the result was excellent in processability (deep drawing property).
  • Comparative Examples b1 to b10 using steels whose chemical composition deviates from the present invention (steel Nos. A1 to a10 in Table 1), the crystal orientation strength (organization) of the ferrite phase required in the present invention is shown. The result was that the workability (deep drawing property) was inferior.
  • the steel types listed in Table 1 were hot-rolled, pickled, and annealed as needed under the conditions shown in Table 3, and then cold-rolled and cold-rolled and annealed. Each manufacturing condition is as shown in Table 3. Further, as in Example 1, the workability (deep drawing property) was evaluated by the r value.

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PCT/JP2020/036379 2019-10-02 2020-09-25 フェライト系ステンレス鋼板およびその製造方法ならびにフェライト系ステンレス部材 Ceased WO2021065738A1 (ja)

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EP20871144.0A EP4043597A4 (en) 2019-10-02 2020-09-25 FERRITIC STAINLESS STEEL SHEET, METHOD OF MANUFACTURE THEREOF AND FERRITIC STAINLESS STEEL PART
CN202080069794.0A CN114502760B (zh) 2019-10-02 2020-09-25 铁素体系不锈钢钢板及其制造方法、以及铁素体系不锈钢构件
KR1020227014596A KR102748718B1 (ko) 2019-10-02 2020-09-25 페라이트계 스테인리스 강판 및 그 제조 방법 그리고 페라이트계 스테인리스 부재
US17/641,186 US12270096B2 (en) 2019-10-02 2020-09-25 Ferritic stainless steel sheet, production method thereof, and ferritic stainless member
JP2021551196A JP7268182B2 (ja) 2019-10-02 2020-09-25 フェライト系ステンレス鋼板およびその製造方法ならびにフェライト系ステンレス部材
MX2022003956A MX2022003956A (es) 2019-10-02 2020-09-25 Hoja de acero inoxidable ferritico, metodo de produccion de la misma y miembro de acero inoxidable ferritico.

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