WO2022145065A1 - Matériau d'acier - Google Patents

Matériau d'acier Download PDF

Info

Publication number
WO2022145065A1
WO2022145065A1 PCT/JP2021/014767 JP2021014767W WO2022145065A1 WO 2022145065 A1 WO2022145065 A1 WO 2022145065A1 JP 2021014767 W JP2021014767 W JP 2021014767W WO 2022145065 A1 WO2022145065 A1 WO 2022145065A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
content
steel material
phosphide
steel
Prior art date
Application number
PCT/JP2021/014767
Other languages
English (en)
Japanese (ja)
Inventor
恭平 石川
謙 木村
耕平 中田
美百合 梅原
真吾 山▲崎▼
Original Assignee
日本製鉄株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 日本製鉄株式会社 filed Critical 日本製鉄株式会社
Publication of WO2022145065A1 publication Critical patent/WO2022145065A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon

Definitions

  • the present invention relates to steel materials.
  • phosphorus (P) may be concentrated at specific points in the steel, for example, between dendrite trees and grain boundaries, and may reduce the toughness, ductility, corrosion resistance and weldability of the steel material. ing.
  • P phosphorus
  • Patent Document 1 describes a carbon steel slab containing REM and capable of improving toughness by refining the produced phosphide. Further, in Patent Document 1, the steel containing Te, which is a surface active element, has a fine solidified structure, a small amount of P supplied between the dendrite resins, a fine phosphide, and carbon steel slabs. It is taught that the deterioration of toughness of steel is suppressed.
  • Patent Document 2 high-purity ferritic stainless steel with improved secondary processing brittleness that is manifested by heat treatment after deep drawing without excessive reduction of P and alloying of trace elements, Si, Mo, etc. Steel plates are listed. Further, in Patent Document 2, in order to improve the secondary processing brittleness, it is effective to precipitate P as a compound in advance to reduce the solid melt P in the steel and delay the grain boundary segregation of P. It is taught that even when the fine phospholides are deposited at the grain boundaries, the effect of delaying the segregation of the grain boundaries of P is greater than the action as the starting point of cracking.
  • Patent Document 3 describes a stainless steel in which P remains, positively precipitates as a coarse Ti-based precipitate, detoxifies P, and has improved properties such as workability and yield strength. Further, in Patent Document 3, Ti-based carbides and Ti-based phosphates are coarsened to detoxify solid-dissolved C and solid-dissolved P, and the pinning effect of Ti-based precipitates is used to coarsen the crystal grains of the steel plate. It is taught to control and improve ductility, rigging, and anisotropy of mechanical properties.
  • the fine particles present in the steel may be used as pinning particles that suppress the grain growth of the metal structure.
  • pinning particles for refining the metal structure of the weld heat-affected zone, but a carbon steel slab utilizing REM phosphate as pinning particles is proposed. (See, for example, Patent Document 4,).
  • Patent Document 4 describes a carbon steel slab containing REM, which can improve the toughness of the weld heat-affected zone by utilizing inclusions as pinning particles. Further, in order to utilize inclusions as pinning particles, it is necessary to generate a large amount of particles on the order of submicrons, and ZrS is generated in molten steel to generate slabs after solidification. It is taught that REM phosphide is deposited with ZrS as a precipitation nucleus by reducing the pressure using the temperature difference between the surface layer portion and the central portion.
  • the present inventors have secured a certain amount or more of a specific element, and the phosphide obtained by reacting the specific element with phosphorus is used as a pinning particle. We have found that it is possible to suppress the grain growth of a metal structure by using it, and completed the present invention.
  • the steel materials that have achieved the above objectives are as follows. (1) By mass%, C: 0.001 to 1.000%, Si: 0.01-3.00%, Mn: 0.10 to 4.50%, P: 0.0005 to 0.300%, S: 0.0300% or less, Al: 0.001-5.000%, N: 0.2000% or less, O: 0.0100% or less, At least one Z element selected from the group consisting of Zr: 0 to 0.8000% and Hf: 0 to 0.8000%.
  • Nb 0-3.000%, Ti: 0 to 0.500%, Ta: 0 to 0.500%, V: 0 to 1.00%, Cu: 0 to 3.00%, Ni: 0-60.00%, Cr: 0 to 30.00%, Mo: 0 to 5.00%, W: 0 to 2.00%, B: 0-0.0200%, Co: 0 to 3.00%, Be: 0 to 0.050%, Ag: 0 to 0.500%, Ca: 0-0.0500%, Mg: 0-0.0500%, At least one of La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and Sc: 0 to 0.5000% in total.
  • Nb 0.003 to 3.000%, Ti: 0.005 to 0.500%, Ta: 0.001 to 0.500%, V: 0.001 to 1.00%, Cu: 0.001 to 3.00%, Ni: 0.001 to 60.00%, Cr: 0.001 to 30.00%, Mo: 0.001 to 5.00%, W: 0.001 to 2.00%, B: 0.0001-0.0200%, Co: 0.001 to 3.00%, Be: 0.0003 to 0.050%, Ag: 0.001 to 0.500%, Ca: 0.0001-0.0500%, Mg: 0.0001-0.0500%, At least one of La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and Sc: 0.0001 to 0.5000% in total.
  • the steel material according to the embodiment of the present invention is based on mass%.
  • Nb 0-3.000%, Ti: 0 to 0.500%, Ta: 0 to 0.500%, V: 0 to 1.00%, Cu: 0 to 3.00%, Ni: 0-60.00%, Cr: 0 to 30.00%, Mo: 0 to 5.00%, W: 0 to 2.00%, B: 0-0.0200%, Co: 0 to 3.00%, Be: 0 to 0.050%, Ag: 0 to 0.500%, Ca: 0-0.0500%, Mg: 0-0.0500%, At least one of La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and Sc: 0 to 0.5000% in total.
  • the metallographic structure it is generally important to miniaturize the metallographic structure in order to improve the material properties required for steel materials, for example, low temperature toughness and / or to achieve both high strength and low temperature toughness.
  • the recrystallization of austenite crystal grains is suppressed by controlling the end temperature at the time of hot rolling, more specifically, finish rolling of the steel material to a low temperature. Due to the suppression of recrystallization, the driving force of ferrite transformation is increased to generate more new crystals.
  • the texture tends to develop in a specific direction by rolling, so that a metal structure showing high anisotropy can be obtained. Therefore, it may not be suitable for applications that require an isotropic metal structure, for example, applications that require high hole expandability such as undercarriage parts of automobiles.
  • Recrystallization means that after plastic working by hot rolling or the like, the strain energy accumulated by the plastic working when held at a high temperature is released by diffusion accompanied by rearrangement of atomic positions, and new crystal grains are generated. It is a phenomenon that occurs. Therefore, the metal structure refined by recrystallization generally has less anisotropy and becomes an isotropic structure. Therefore, in applications where an isotropic metallographic structure is preferred, miniaturization by recrystallization is very advantageous.
  • the use and control of pinned particles may be effective in suppressing the formation of coarse tissue.
  • the present inventors have investigated the elements in steel that can be used as pinning particles for suppressing the grain growth of the metal structure.
  • the present inventors have determined the amounts of the elements Zr and Hf (hereinafter, also referred to as “Z element”) as inclusions formed in the steel by those elements, more specifically, oxides of these elements. , Secure a certain amount or more while considering the relationship with nitrides and sulfides (that is, the effective amount of the Z element corresponding to the left side of Equation 1 is 0.0003% or more), and further, the specific element is contained in steel.
  • the amount of P in the phosphonic acid measured by the extraction residue method is 0.0003 atomic% or more with respect to the steel material.
  • the phosphite can effectively function as pinning particles, resulting in grain growth of the metal structure. It was found that it can be remarkably suppressed.
  • the above-mentioned Z element has a property of easily forming inclusions composed of oxides, nitrides and sulfides in combination with O (oxygen), N (nitrogen) and S (sulfur) existing in steel.
  • O oxygen
  • N nitrogen
  • S sulfur
  • the amount of the Z element that can contribute to the reaction with P in the steel decreases, and a phosphide as a pinning particle is sufficiently formed. You will not be able to.
  • the amount of the Z element in consideration of such inclusions is calculated as the effective amount of the Z element by the above formula 1 which will be described in detail later, and the effective amount is a certain amount or more, that is, 0.0003.
  • the Z element can be reacted with P in the steel to form a sufficient amount of phosphide to effectively function as pinning particles.
  • the amount and size of such a phosphide are as described in detail later, and the amount of P in the phosphide measured by the extraction residue method is 0. It has been found that a higher pinning effect can be achieved by keeping the average particle size in the range of 0003 atomic% or more and the average particle size measured by the TEM replica method within the range of less than 100 nm. According to the present invention, such a pinning effect can be effectively applied regardless of whether or not the miniaturization of the metal structure is due to recrystallization.
  • the Z element present in the recrystallized austenite during hot rolling reacts with P to become fine.
  • the phosphite is precipitated, and the pinning effect of the phosphite suppresses the growth of recrystallized austenite grains.
  • a steel material having an austenite metal structure has fine crystal grains, and a steel material having a martensite metal structure has fine so-called old austenite grains.
  • the fine recrystallized austenite grains transform into a fine ferrite structure in the process of lowering the temperature after the completion of hot rolling, the metal structure containing an isotropic and fine ferrite structure is stably maintained. It becomes possible.
  • the Z element in the present invention easily combines with O, N and S to form inclusions as described above, and therefore it is generally difficult to secure a predetermined effective amount in steel. Under these circumstances, the pinning effect of the phosphide containing the Z element has not been known so far. However, recent advances in refining technology have made it possible to reduce the content of elements such as O, N, and S, which are generally present in steel as impurities, to extremely low levels. It was possible to realize an effective amount of the Z element within a predetermined range. Therefore, the pinning effect of the phosphide containing the Z element has been clarified for the first time by the present inventors, and is extremely surprising and surprising.
  • Carbon (C) is an element necessary for stabilizing hardness and / or ensuring strength. In order to sufficiently obtain these effects, the C content is 0.001% or more. The C content may be 0.005% or more, 0.010% or more, or 0.020% or more. On the other hand, if C is excessively contained, toughness, bendability and / or weldability may decrease. Therefore, the C content is 1.000% or less. The C content may be 0.800% or less, 0.600% or less, or 0.500% or less.
  • Si is a deoxidizing element and is an element that also contributes to the improvement of strength. In order to sufficiently obtain these effects, the Si content is 0.01% or more. The Si content may be 0.05% or more, 0.10% or more, or 0.30% or more. On the other hand, if Si is excessively contained, the toughness may be lowered or surface quality defects called scale defects may occur. Therefore, the Si content is 3.00% or less. The Si content may be 2.00% or less, 1.00% or less, or 0.60% or less.
  • Manganese (Mn) is an element effective for improving hardenability and / or strength, and is also an effective austenite stabilizing element. In order to sufficiently obtain these effects, the Mn content is 0.10% or more. The Mn content may be 0.50% or more, 0.70% or more, or 1.00% or more. On the other hand, if Mn is excessively contained, MnS harmful to toughness may be generated or the oxidation resistance may be lowered. Therefore, the Mn content is 4.50% or less. The Mn content may be 4.00% or less, 3.50% or less, or 3.00% or less.
  • Phosphorus (P) is an element that is generally mixed in the manufacturing process, but in the embodiment of the present invention, it effectively functions as an element constituting a phosphide, which is a pinning particle, in suppressing grain growth.
  • the P content is 0.0005% or more.
  • the P content may be 0.001% or more, 0.002% or more, 0.003% or more, 0.005% or more, or 0.007% or more.
  • the P content is 0.300% or less.
  • the P content may be 0.100% or less, 0.050% or less, or 0.030% or less.
  • S 0.0300% or less
  • Sulfur (S) is an element mixed in the manufacturing process, and is preferable from the viewpoint of reducing inclusions formed with the Z element according to the embodiment of the present invention, so that the S content is 0%. There may be. However, in order to reduce the S content to less than 0.0001%, it takes time for refining, which leads to a decrease in productivity. Therefore, the S content may be 0.0001% or more, 0.0005% or more, or 0.0010% or more. On the other hand, if S is excessively contained, the effective amount of the Z element may decrease and the toughness may decrease. Therefore, the S content is 0.0300% or less.
  • the S content is preferably 0.0100% or less, more preferably 0.0050% or less, and most preferably 0.0030% or less.
  • Aluminum (Al) is a deoxidizing element and is also an effective element for improving corrosion resistance and / or heat resistance.
  • the Al content is 0.001% or more.
  • the Al content may be 0.010% or more, 0.100% or more, or 0.200% or more.
  • the Al content may be 1.000% or more, 2.000% or more, or 3.000% or more.
  • the Al content is 5.000% or less.
  • the Al content may be 4.500% or less, 4000% or less, or 3.500% or less.
  • the Al content may be 1.500% or less, 1.000% or less, or 0.300% or less.
  • N Nitrogen (N) is an element mixed in the manufacturing process, and is preferable from the viewpoint of reducing inclusions formed with the Z element according to the embodiment of the present invention, so that the N content is 0%. There may be. However, in order to reduce the N content to less than 0.0001%, it takes time for refining, which leads to a decrease in productivity. Therefore, the N content may be 0.0001% or more, 0.0005% or more, or 0.0010% or more. On the other hand, N is also an element effective for stabilizing austenite, and may be intentionally contained if necessary. In this case, the N content is preferably 0.0100% or more, and may be 0.0200% or more and 0.0500% or more. However, if N is excessively contained, the effective amount of the Z element may decrease and the toughness may decrease. Therefore, the N content is 0.2000% or less. The N content may be 0.1500% or less, 0.1000% or less, or 0.0800% or less.
  • Oxygen (O) is an element mixed in the manufacturing process, and is preferable from the viewpoint of reducing inclusions formed with the Z element according to the embodiment of the present invention, so that the O content is 0%. There may be. However, in order to reduce the O content to less than 0.0001%, it takes time for refining, which leads to a decrease in productivity. Therefore, the O content may be 0.0001% or more, 0.0005% or more, or 0.0010% or more. On the other hand, if O is excessively contained, coarse inclusions may be formed, the effective amount of the Z element may be lowered, and the formability and / or toughness of the steel material may be lowered. Therefore, the O content is 0.0100% or less. The O content may be 0.0080% or less, 0.0060% or less, or 0.0040% or less.
  • the Z element according to the embodiment of the present invention is Zr: 0 to 0.8000% and Hf: 0 to 0.8000%, and zirconium (Zr) and hafnium (Hf) are pinned based on the formation of a phosphide. The effect can be exhibited. By exhibiting the pinning effect, it becomes possible to remarkably suppress the grain growth of the metal structure.
  • any one element may be used alone, or both may be used. Further, the Z element may be present in an amount satisfying Equation 1, which will be described in detail later, and the lower limit thereof is not particularly limited. However, for example, the content of each Z element or the total content may be 0.0010% or more, preferably 0.0050% or more, more preferably 0.0150% or more, and even more. It is preferably 0.0300% or more, and most preferably 0.0500% or more. On the other hand, even if the Z element is excessively contained, the effect is saturated, and therefore, if the Z element is contained in the steel material more than necessary, the manufacturing cost may increase.
  • the content of each Z element is 0.8000% or less, for example, 0.7000% or less, 0.6000% or less, 0.5000% or less, 0.4000% or less, or 0.3000% or less. May be good.
  • the total content of the Z element is 1.6000% or less, for example, 1.2000% or less, 1.000% or less, 0.8000% or less, 0.6000% or less, or 0.5000% or less. You may.
  • the steel material may contain one or more of the following optional elements, if necessary.
  • the steel material has Nb: 0 to 3.000%, Ti: 0 to 0.500%, Ta: 0 to 0.500%, V: 0 to 1.00%, Cu: 0 to 3.00%, Ni: 0 to 60.00%, Cr: 0 to 30.00%, Mo: 0 to 5.00%, W: 0 to 2.00%, B: 0 to 0.0200%, Co: 0 to 3 It may contain one or more of .00%, Be: 0 to 0.050%, and Ag: 0 to 0.500%.
  • the steel materials include Ca: 0 to 0.0500%, Mg: 0 to 0.0500%, and La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er. At least one of Tm, Yb, Lu, and Sc: one or more of 0 to 0.5000% in total may be contained. Further, the steel material may contain one or two of Sn: 0 to 0.300% and Sb: 0 to 0.300%. The steel materials are Te: 0 to 0.100%, Se: 0 to 0.100%, As: 0 to 0.050%, Bi: 0 to 0.500%, and Pb: 0 to 0.500%. One or more of them may be contained. Hereinafter, these optional elements will be described in detail.
  • Niobium (Nb) is an element that contributes to strengthening precipitation and suppressing recrystallization.
  • the Nb content may be 0%, but in order to obtain these effects, the Nb content is preferably 0.003% or more.
  • the Nb content may be 0.005% or more or 0.010% or more.
  • the Nb content may be 1.000% or more or 1.500% or more from the viewpoint of sufficiently strengthening precipitation.
  • the Nb content is 3.000% or less.
  • the Nb content may be 2.800% or less, 2.500% or less, or 2.000% or less.
  • the Nb content is preferably 0.100% or less, 0.080% or less, 0.050% or less, or 0.030. It may be less than or equal to%.
  • Titanium (Ti) is an element that contributes to improving the strength of steel materials by strengthening precipitation.
  • the Ti content may be 0%, but in order to obtain such an effect, the Ti content is preferably 0.005% or more.
  • the Ti content may be 0.010% or more, 0.050% or more, or 0.080% or more.
  • the Ti content is 0.500% or less.
  • the Ti content may be 0.300% or less, 0.200% or less, or 0.100% or less.
  • Tantalum (Ta) is an element effective in controlling the morphology of carbides and increasing their strength.
  • the Ta content may be 0%, but in order to obtain these effects, the Ta content is preferably 0.001% or more.
  • the Ta content may be 0.005% or more, 0.010% or more, or 0.050% or more.
  • the Ta content is 0.500% or less.
  • the Ta content may be 0.300% or less, 0.100% or less, or 0.080% or less.
  • Vanadium (V) is an element that contributes to improving the strength of steel materials by strengthening precipitation.
  • the V content may be 0%, but in order to obtain such an effect, the V content is preferably 0.001% or more.
  • the V content may be 0.01% or more, 0.02% or more, 0.05% or more, or 0.10% or more.
  • the V content is 1.00% or less.
  • the V content may be 0.80% or less, 0.60% or less, or 0.50% or less.
  • Copper (Cu) is an element that contributes to the improvement of strength and / or corrosion resistance.
  • the Cu content may be 0%, but in order to obtain these effects, the Cu content is preferably 0.001% or more.
  • the Cu content may be 0.01% or more, 0.10% or more, 0.15% or more, 0.20% or more, or 0.30% or more.
  • the Cu content is 3.00% or less.
  • the Cu content may be 2.00% or less, 1.50% or less, 1.00% or less, or 0.50% or less.
  • Nickel (Ni) is an element that contributes to the improvement of strength and / or heat resistance, and is also an effective austenite stabilizing element.
  • the Ni content may be 0%, but in order to obtain these effects, the Ni content is preferably 0.001% or more.
  • the Ni content may be 0.01% or more, 0.10% or more, 0.50% or more, 0.70% or more, 1.00% or more, or 3.00% or more.
  • the Ni content may be 30.00% or more, 35.00% or more, or 40.00% or more.
  • the deformation resistance during hot working increases in addition to the increase in alloy cost, which may increase the equipment load.
  • the Ni content is 60.00% or less.
  • the Ni content may be 55.00% or less or 50.00% or less.
  • the Ni content is 15.00% or less, 10.00% or less, 6.00% or less, or 4.00% or less. You may.
  • Chromium (Cr) is an element that contributes to the improvement of strength and / or corrosion resistance.
  • the Cr content may be 0%, but in order to obtain these effects, the Cr content is preferably 0.001% or more.
  • the Cr content may be 0.01% or more, 0.05% or more, 0.10% or more, or 0.50% or more.
  • the Cr content may be 10.00% or more, 12.00% or more, or 15.00% or more.
  • the Cr content is 30.00% or less.
  • the Cr content may be 28.00% or less, 25.00% or less, or 20.00% or less.
  • the Cr content may be 10.00% or less, 9.00% or less, or 7.50% or less.
  • Molybdenum is an element that enhances the hardenability of steel and contributes to the improvement of strength, and is also an element that contributes to the improvement of corrosion resistance.
  • the Mo content may be 0%, but in order to obtain these effects, the Mo content is preferably 0.001% or more.
  • the Mo content may be 0.01% or more, 0.02% or more, 0.50% or more, or 1.00% or more.
  • Mo content is 5.00% or less.
  • the Mo content may be 4.50% or less, 4.00% or less, 3.00 or less, or 1.50% or less.
  • Tungsten is an element that enhances the hardenability of steel and contributes to the improvement of strength.
  • the W content may be 0%, but in order to obtain such an effect, the W content is preferably 0.001% or more.
  • the W content may be 0.01% or more, 0.02% or more, 0.05% or more, 0.10% or more, or 0.50% or more.
  • the W content is 2.00% or less.
  • the W content may be 1.80% or less, 1.50% or less, or 1.00% or less.
  • B is an element that contributes to the improvement of strength.
  • the B content may be 0%, but in order to obtain such an effect, the B content is preferably 0.0001% or more.
  • the B content may be 0.0003% or more, 0.0005% or more, or 0.0007% or more.
  • the B content is 0.0200% or less.
  • the B content may be 0.0100% or less, 0.0050% or less, 0.0030% or less, or 0.0020% or less.
  • Co is an element that contributes to the improvement of hardenability and / or heat resistance.
  • the Co content may be 0%, but in order to obtain these effects, the Co content is preferably 0.001% or more.
  • the Co content may be 0.01% or more, 0.02% or more, 0.05% or more, 0.10% or more, or 0.50% or more.
  • the Co content is 3.00% or less.
  • the Co content may be 2.50% or less, 2.00% or less, 1.50% or less, or 0.80% or less.
  • Beryllium (Be) is an element effective for increasing the strength of the base metal and refining the structure.
  • the Be content may be 0%, but in order to obtain such an effect, the Be content is preferably 0.0003% or more.
  • the Be content may be 0.0005% or more, 0.001% or more, or 0.010% or more.
  • the Be content is 0.050% or less.
  • the Be content may be 0.040% or less, 0.030% or less, or 0.020% or less.
  • Silver (Ag) is an element effective for increasing the strength of the base material and refining the structure.
  • the Ag content may be 0%, but in order to obtain such an effect, the Ag content is preferably 0.001% or more.
  • the Ag content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.050% or more.
  • the Ag content is 0.500% or less.
  • the Ag content may be 0.400% or less, 0.300% or less, or 0.200% or less.
  • Ca 0-0.0500%
  • Ca is an element that can control the morphology of sulfides.
  • the Ca content may be 0%, but in order to obtain such an effect, the Ca content is preferably 0.0001% or more.
  • the Ca content is 0.0500% or less.
  • Magnesium (Mg) is an element that can control the morphology of sulfides.
  • the Mg content may be 0%, but in order to obtain such an effect, the Mg content is preferably 0.0001% or more.
  • the Mg content may be greater than 0.0015%, greater than 0.0016%, greater than or equal to 0.0018% or greater than or equal to 0.0020%.
  • the Mg content is 0.0500% or less.
  • the Mg content may be 0.0400% or less, 0.0300% or less, or 0.0200% or less.
  • the total content of at least one of La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and Sc is 0%. However, in order to obtain such an effect, it is preferably 0.0001% or more.
  • the total content of at least one of La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and Sc is 0.0002% or more. It may be 0.0003% or more or 0.0004% or more.
  • the total content of at least one of La, Ce, Nd, Y, Pm, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and Sc is 0.5000%. It may be less than or equal to 0.4000%, 0.3000% or less, or 0.2000% or less.
  • Tin (Sn) is an element effective for improving corrosion resistance.
  • the Sn content may be 0%, but in order to obtain such an effect, the Sn content is preferably 0.001% or more.
  • the Sn content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.050% or more.
  • the Sn content is 0.300% or less.
  • the Sn content may be 0.250% or less, 0.200% or less, or 0.150% or less.
  • Antimony (Sb) is an element effective for improving corrosion resistance like Sn, and the effect can be increased by including it in combination with Sn.
  • the Sb content may be 0%, but in order to obtain the effect of improving the corrosion resistance, the Sb content is preferably 0.001% or more.
  • the Sb content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.050% or more.
  • excessive content of Sb may lead to a decrease in toughness, particularly low temperature toughness. Therefore, the Sb content is 0.300% or less.
  • the Sb content may be 0.250% or less, 0.200% or less, or 0.150% or less.
  • Tellurium is an element effective for improving the machinability of steel because it forms a low melting point compound with Mn, S and the like to enhance the lubricating effect.
  • the Te content may be 0%, but in order to obtain such an effect, the Te content is preferably 0.001% or more.
  • the Te content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.040% or more.
  • the Te content is 0.100% or less.
  • the Te content may be 0.090% or less, 0.080% or less, or 0.070% or less.
  • Selenium (Se) is an effective element for improving the machinability of steel because the selenium produced in the steel changes the shear-plastic deformation of the work material and the chips are easily crushed. ..
  • the Se content may be 0%, but in order to obtain such an effect, the Se content is preferably 0.001% or more.
  • the Se content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.040% or more.
  • the Se content is 0.100% or less.
  • the Se content may be 0.090% or less, 0.080% or less, or 0.070% or less.
  • Arsenic (As) is an element effective in improving the machinability of steel.
  • the As content may be 0%, but in order to obtain such an effect, the As content is preferably 0.001% or more.
  • the As content may be 0.005% or more or 0.010% or more.
  • the As content is 0.050% or less.
  • the As content may be 0.040% or less, 0.030% or less, or 0.020% or less.
  • Bismuth (Bi) is an element effective in improving the machinability of steel.
  • the Bi content may be 0%, but in order to obtain such an effect, the Bi content is preferably 0.001% or more.
  • the Bi content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.050% or more.
  • the Bi content is 0.500% or less.
  • the Bi content may be 0.400% or less, 0.300% or less, or 0.200% or less.
  • Pb 0 to 0.500%
  • Lead (Pb) is an element effective for improving the machinability of steel because it melts when the temperature rises due to cutting and promotes the growth of cracks.
  • the Pb content may be 0%, but in order to obtain such an effect, the Pb content is preferably 0.001% or more.
  • the Pb content may be 0.010% or more, 0.020% or more, 0.030% or more, or 0.050% or more.
  • the Pb content is 0.500% or less.
  • the Pb content may be 0.400% or less, 0.300% or less, or 0.200% or less.
  • the balance other than the above elements consists of Fe and impurities.
  • Impurities are components that are mixed in by various factors in the manufacturing process, including raw materials such as ore and scrap, when steel materials are industrially manufactured.
  • the effective amount of the Z element consisting of Zr and Hf is determined by the left side of the following formula 1, and the value thereof satisfies the following formula 1. 0.61 [Zr] +0.31 [Hf] -1.75 [O] -3.99 [N] -1.74 [S] ⁇ 0.0003 ⁇ ⁇ ⁇ Equation 1
  • [Zr], [Hf], [O], [N], and [S] are the content [mass%] of each element, and are 0 when the element is not contained.
  • the effective amount of the Z element By making the effective amount of the Z element satisfy the above formula 1, it is possible to react the Z element existing in austenite with P in the steel to form a phosphide, and such a phosphide can be formed. It is possible to suppress the grain growth of the metal structure due to the formation of the metal structure. More specifically, these Z elements (hereinafter, also simply referred to as “Z”) are combined with O (oxygen), N (nitrogen) and S (sulfur) present in steel to form an oxide (ZO 2 ). , Tends to form inclusions consisting of nitrides (ZN) and sulfides (ZS). Once the inclusions are formed, at least the Z element in these inclusions cannot contribute to the reaction with P. Therefore, in order to promote the reaction with P and form a phosphide, which is a pinning particle, it is necessary to increase the amount of Z element that can form a phosphide in austenite without forming inclusions. ..
  • the amount of Z element that can form a phosphide is the amount of Z element contained in the steel minus the maximum amount that can be consumed to form inclusions (oxides, nitrides and sulfides). It is possible to estimate by. Therefore, in the embodiment of the present invention, the amount of Z element effective for forming the phosphide estimated in this way (that is, "effective amount of Z element") is specifically determined by the following formula A. Defined.
  • Effective amount of Z [atomic%] ⁇ (M [Fe] / M [Z] ) x [Z]-(M [Fe] / M [O] ) x [O] x 1 / 2- (M [Fe ] ] / M [N] ) x [N]-(M [Fe] / M [S] ) x [S] ... Equation A
  • Z represents each Z element of Zr and Hf
  • M [Z] is the atomic weight of the Z element
  • M [Fe] is the atomic weight of Fe
  • M [O] is the atomic weight of O
  • M [N] is N.
  • M [S] represents the atomic weight of S
  • [Z], [O], [N] and [S] are the corresponding element content [mass%], respectively, and when no element is contained. It is 0.
  • the steel material according to the embodiment of the present invention contains various alloying elements, the steel material as a whole is almost composed of Fe or is an optional element.
  • the steel material when a certain Ni and / or Cr is contained in a relatively large amount (the maximum contents are 60.00% and 30.00%, respectively), it is clear that it is almost composed of Ni and / or Cr in addition to Fe. Is.
  • the atomic weights of Ni and Cr are equivalent to the atomic weights of Fe. Therefore, even when the steel material contains a relatively large amount of Ni and / or Cr, the atomic% of each Z element of Zr and Hf is approximately Fe in the content [mass%] of each Z element.
  • phosphorus is subtracted from the atomic% of the total Z element by subtracting the maximum amount (atomic%) that can be consumed to form oxides (ZO 2 ), nitrides (ZN) and sulfides (ZS).
  • the amount of element Z in steel that can effectively act to form the compound can be calculated.
  • the maximum amount (atomic%) of Z element that can be consumed to form oxides (ZO 2 ), nitrides (ZN) and sulfides (ZS) is for the same reasons as described above.
  • M [Fe] / M [O] ⁇ [O] ⁇ 1/2, respectively.
  • the effective amount of Z element for forming a phosphide can be defined by the following formula A.
  • Effective amount of Z [atomic%] ⁇ (M [Fe] / M [Z] ) x [Z]-(M [Fe] / M [O] ) x [O] x 1 / 2- (M [Fe ] ] / M [N] ) x [N]-(M [Fe] / M [S] ) x [S] ... Equation A
  • [Zr], [Hf], [O], [N], and [S] are the content [mass%] of each element, and are 0 when the element is not contained.
  • the effective amount of the Z element determined by the above formula B is 0.0003% or more, that is, at least satisfy the following formula 1. 0.61 [Zr] +0.31 [Hf] -1.75 [O] -3.99 [N] -1.74 [S] ⁇ 0.0003 ⁇ ⁇ ⁇ Equation 1
  • the effective amount of the Z element may be, for example, 0.0005% or more or 0.0007% or more, preferably 0.0010% or more, more preferably 0.0015% or more, still more preferably 0.0030%. The above is most preferably 0.0050% or more or 0.0100% or more.
  • the effective amount of the Z element is preferably 2.000% or less, for example, 1.8000% or less, 1.5000% or less, 1.2000% or less, 1.000% or less, or 0.8000% or less. You may.
  • the amount of P contained in the phosphide measured by the extraction residue method is 0.0003 atomic% or more with respect to the steel material
  • element Z needs to react with P to form a phosphide and be present in the steel in an amount capable of the phosphide effectively functioning as pinning particles.
  • the phosphoric substance containing the Z element is present in the steel, and the amount of P contained in the phosphoric substance measured by the extraction residue method is required to be 0.0003 atomic% or more with respect to the steel material.
  • the phosphonic acid product effectively functions as a pinning particle, and the grain growth of the metal structure can be remarkably suppressed.
  • the above amount of P is preferably 0.0005 atom% or more, more preferably 0.0010 atom% or more, still more preferably 0.0030 atom% or more, most preferably 0.0050 atom% or more or 0.0100 atom. % Or more.
  • the upper limit of the amount of P is not particularly limited, but even if the amount of P is excessively increased, the effect is saturated and the production cost increases (the alloy cost due to the increase in the content of Z element for forming a phosphite). It is not always preferable because it causes an increase and / or an increase in the refining cost for O, N and S).
  • the amount of P is preferably 0.5000 atom% or less, for example, 0.4000 atom% or less, 0.3000 atom% or less, 0.2000 atom% or less, 0.1500 atom% or less, or 0.1000 atom. It may be less than or equal to%.
  • the amount of P contained in the phosphide is determined as follows by the extraction residue method. First, a sample containing a depth of 0.5 mm from the surface of the steel material collected from the steel material is electrolyzed with 1 g or more of the steel material by constant current electrolysis, and then filtered using a membrane filter having a pore size of 0.2 ⁇ m to form a precipitate (phosphide). Is separated. Next, the separated precipitate was decomposed with a solution such as nitrate (HNO 3 ), and then the obtained residue was measured by ICP-MS (inductively coupled plasma mass spectrometer). The amount of P present as is obtained. Finally, the ratio (atomic%) of the amount of P contained in the phosphide to the whole steel material is determined from the amount of P and the specific amount of the electrolyzed steel material.
  • the average particle size of the phosphide is preferably 90 nm or less, more preferably 80 nm or less, even more preferably 60 nm or less, and most preferably 50 nm or less or 40 nm or less.
  • the lower limit of the average particle size of the phosphide is not particularly limited, but may be, for example, 5 nm or more, and may be 8 nm or more, 10 nm or more, 15 nm or more, 20 nm or more, or 25 nm or more.
  • the average particle size of the phosphide is determined by the TEM replica method as follows. First, a test piece for observing precipitates is collected from the steel material, the cross section is polished parallel to the rolling direction and at a depth of 0.5 mm from the surface of the steel material, and then etching is performed by the SPEED method (selective constant potential electrolytic etching method). Then, the precipitate is extracted into a carbon film by the blank replica method and held on the Cu mesh.
  • the prepared carbon extraction replica sample was analyzed by EDS (energy dispersion type X-ray spectroscope) to identify the phosphonic acid, and TEM (transmission electron microscope, acceleration voltage 200 kV) was applied to the phosphonic acid.
  • EDS energy dispersion type X-ray spectroscope
  • TEM transmission electron microscope, acceleration voltage 200 kV
  • the steel material according to the embodiment of the present invention may be any steel material on which a phosphide containing a Z element is formed, and is not particularly limited.
  • the steel material according to the embodiment of the present invention includes, for example, thick steel plates and thin steel plates which are steel materials after hot rolling, as well as steel bars, wire rods, shaped steels, steel pipes, and the like.
  • the steel material according to the embodiment of the present invention can be manufactured by any suitable method known to those skilled in the art, depending on the form of the final product and the like.
  • the manufacturing method includes a step generally applied when manufacturing the thick steel plate, for example, a step of casting a slab having the chemical composition described above, and casting. It includes a step of hot rolling the slab and a step of cooling the obtained rolled material, and may further include heat treatment such as a quenching step and a tempering step, if necessary.
  • the steel material manufacturing process according to the embodiment of the present invention may be a thermal processing control process (TMCP) that combines controlled rolling and accelerated cooling.
  • TMCP thermal processing control process
  • the manufacturing method includes a step generally applied when manufacturing the thin steel plate, for example, a step of casting a slab having the chemical composition described above, and casting. It may further include a step of hot rolling the slab, a step of cooling and winding the obtained rolled material, a cold rolling step, a baking step and the like, if necessary.
  • a step generally applied when manufacturing steel bars and other steel materials is included, and for example, a steelmaking process for forming molten steel having the chemical composition described above is formed. It includes a step of casting slabs, billets, blooms, etc.
  • the thermal history in the hot rolling process is important for the formation of phosphide.
  • the temperature and time range (phosphorization nose) at which the phosphite of each Z element is precipitated is determined in advance, and the hotness is determined.
  • the thermal history of the rolling process may be guided within this temperature and time range (ie, within the precipitation nose of the phosphite). It will be described in more detail below with reference to the drawings.
  • FIG. 1 is a schematic diagram showing a precipitation nose of a phosphide containing the Z element.
  • FIG. 1 is a schematic diagram as described above, and the curve of the precipitation nose actually changes depending on the Z element or the like specifically used.
  • the precipitation nose of the phosphide shifts to the short-time side.
  • strain in the range of 950 to 1100 ° C. it is held in this temperature range for a relatively short time of about 30 seconds or more (about 70 seconds or more in the case of a lower temperature), and then cooled. Since the thermal history in the hot rolling process passes through the precipitation nose, the Z element and P in the steel can be reacted to form a phosphide.
  • even when processing by hot rolling is performed for example, when strain is applied at a high temperature of 1100 ° C.
  • the mixture is held in the range of 950 to 1100 ° C. for a short time of about 10 seconds and then cooled.
  • the heat history in the hot rolling process does not pass through the precipitation nose and phosphide cannot be formed.
  • retention includes a case where the temperature gradually decreases due to cooling, air cooling, or the like within the above temperature range.
  • the hot rolling process is a process from heating the slab, billet, and bloom to the end of rough rolling and / or finish rolling.
  • the specific thermal history in this step is not particularly limited because it changes depending on the type of Z element and the like, but the thermal history is, for example, during rough rolling and / or finish rolling, or during rough rolling and / or rough rolling and /. Alternatively, it includes holding for 30 seconds or more in a temperature range of 900 to 1100 ° C., preferably 950 to 1100 ° C. after finish rolling. Alternatively, the thermal history may include holding at 950 to 1100 ° C., preferably 980 to 1020 ° C. for 1000 seconds or longer before adding strain in hot rolling. In this case, phosphide is formed before strain is applied by hot rolling.
  • the upper limit of the holding time is not particularly limited, but may be, for example, 15,000 seconds or less or 12,000 seconds or less.
  • the Z element present in austenite can be reliably reacted with P in the steel to form a phosphide, and thus the metal can be formed by the pinning effect.
  • the grain growth of the tissue can be remarkably suppressed.
  • the Ac3 point is the temperature at which the transformation from ferrite to austenite is completed during heating.
  • the austenite particle size when the test piece is heated to 950 ° C. at a heating rate of 20 ° C./sec and held for 10 seconds is D1
  • the test piece is heated to 1050 ° C. at a heating rate of 20 ° C./sec.
  • the austenite particle size when held for 10 seconds was defined as D2.
  • Table 2 below also shows the chemical composition obtained by analyzing the sample collected from each of the obtained steel materials, the amount of P contained in the phosphide in each steel material (precipitated P amount), and the average particle size of the phosphide.
  • the amount of P contained in the phosphide and the average particle size of the phosphide were measured by the following methods.
  • the amount of P contained in the phosphide was determined as follows by the extraction residue method. First, a sample containing a depth of 0.5 mm from the surface of the steel material collected from the steel material is subjected to constant current electrolysis under the conditions of 10% acetylacetone-1% tetramethylammonium chloride-methanol solution at 500 mmA and 2 hours or more to obtain 1 g or more of the steel material. Was electrolyzed and then filtered using a membrane filter having a pore size of 0.2 ⁇ m to separate precipitates (phosphide).
  • the separated precipitate was decomposed with a solution in which nitric acid (HNO 3 ) and perchloric acid (HClO 4 ) were mixed at a ratio of 2: 1 and the obtained residue was then subjected to ICP-MS (inductively coupled plasma mass spectrometer). ) was used to obtain the amount of P present as a phosphate precipitated in the steel material. Finally, the ratio (atomic%) of the amount of P contained in the phosphide to the whole steel material was determined from the amount of P and the specific amount of the electrolyzed steel material.
  • the average particle size of the phosphide was determined by the TEM replica method as follows. First, a test piece for observing precipitates is collected from the steel material, and the cross section parallel to the rolling direction and at a depth of 0.5 mm from the steel material surface is polished (mirror-polished with emery paper or diamond paste, and then the polished surface is polished. Finish polishing with alumina abrasive grains), then etching by SPEED method (selective constant potential electrolytic etching method) (electropolishing solution: 10% acetylacetone-1% tetramethylammonium chloride-methanol, electrolytic polishing conditions: -100 mV vs.
  • SPEED method selective constant potential electrolytic etching method
  • the effective amount of the Z element is 0.0003% or more, and the amount of P contained in the phosphide and the average particle size of the phosphide are appropriate. By doing so, the grain growth of the metal structure could be sufficiently suppressed.
  • the steel material according to the embodiment of the present invention includes steel materials after hot rolling in which a phosphonic acid containing the Z element is formed, for example, thick steel plates used for bridges, construction, shipbuilding, pressure vessels, and the like, automobiles, and the like. It includes thin steel plates used for applications such as home appliances, as well as steel bars, wire rods, shaped steels, steel pipes, and the like.
  • the steel material according to the embodiment of the present invention is applied to these materials, the grain growth of the metal structure is suppressed, and therefore the fine metal structure is stably maintained. Therefore, for example, high strength and low temperature toughness. It is possible to achieve both of the contradictory characteristics of.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention fournit un matériau d'acier qui présente une composition chimique prédéfinie satisfaisant ０,６１［Ｚｒ］＋０,３１［Ｈｆ］－１,７５［Ｏ］－３,９９［Ｎ］－１,７４［Ｓ］≧０,０００３ (dans la formule, ［Ｚｒ］, ［Ｈｆ］, ［Ｏ］, ［Ｎ］ et ［Ｓ］ représentent la teneur (en % en masse) de chaque élément). La quantité de P contenu dans un phosphure mesurée selon un procédé de résidu d'extraction, est supérieure ou égale à ０,０００３%at. du matériau d'acier. Le diamètre particulaire moyen du phosphure mesuré selon un procédé de répliques TEM, est inférieur à １００ｎｍ.
PCT/JP2021/014767 2020-12-28 2021-04-07 Matériau d'acier WO2022145065A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2020-218754 2020-12-28
JP2020218754 2020-12-28

Publications (1)

Publication Number Publication Date
WO2022145065A1 true WO2022145065A1 (fr) 2022-07-07

Family

ID=82259385

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2021/014767 WO2022145065A1 (fr) 2020-12-28 2021-04-07 Matériau d'acier

Country Status (1)

Country Link
WO (1) WO2022145065A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2023053827A1 (fr) * 2021-09-28 2023-04-06 日本製鉄株式会社 Tôle d'acier

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008189989A (ja) * 2007-02-05 2008-08-21 Sumitomo Metal Ind Ltd 高温浸炭用鋼材
JP2011168866A (ja) * 2010-02-22 2011-09-01 Nisshin Steel Co Ltd フェライト単相系ステンレス鋼スラブおよびフェライト単相系ステンレス鋼スラブの製造方法
JP2018059135A (ja) * 2016-10-03 2018-04-12 新日鐵住金株式会社 Ｎｉ基耐熱合金部材およびその製造方法
WO2018151222A1 (fr) * 2017-02-15 2018-08-23 新日鐵住金株式会社 ALLIAGE RÉSISTANT À LA CHALEUR À BASE DE Ni ET SON PROCÉDÉ DE FABRICATION
JP2019112679A (ja) * 2017-12-25 2019-07-11 日本製鉄株式会社 鋼材、油井用鋼管、及び、鋼材の製造方法
WO2019198460A1 (fr) * 2018-04-09 2019-10-17 日本製鉄株式会社 Tuyau d'acier et procédé de production de tuyau d'acier
JP2019183218A (ja) * 2018-04-06 2019-10-24 日本製鉄株式会社 高圧水素容器、及び、高圧水素用鋼材

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008189989A (ja) * 2007-02-05 2008-08-21 Sumitomo Metal Ind Ltd 高温浸炭用鋼材
JP2011168866A (ja) * 2010-02-22 2011-09-01 Nisshin Steel Co Ltd フェライト単相系ステンレス鋼スラブおよびフェライト単相系ステンレス鋼スラブの製造方法
JP2018059135A (ja) * 2016-10-03 2018-04-12 新日鐵住金株式会社 Ｎｉ基耐熱合金部材およびその製造方法
WO2018151222A1 (fr) * 2017-02-15 2018-08-23 新日鐵住金株式会社 ALLIAGE RÉSISTANT À LA CHALEUR À BASE DE Ni ET SON PROCÉDÉ DE FABRICATION
JP2019112679A (ja) * 2017-12-25 2019-07-11 日本製鉄株式会社 鋼材、油井用鋼管、及び、鋼材の製造方法
JP2019183218A (ja) * 2018-04-06 2019-10-24 日本製鉄株式会社 高圧水素容器、及び、高圧水素用鋼材
WO2019198460A1 (fr) * 2018-04-09 2019-10-17 日本製鉄株式会社 Tuyau d'acier et procédé de production de tuyau d'acier

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2023053827A1 (fr) * 2021-09-28 2023-04-06 日本製鉄株式会社 Tôle d'acier

Similar Documents

Publication Publication Date Title
JP4834292B2 (ja) 金属間化合物の形成が抑制された耐食性、耐脆化性、鋳造性及び熱間加工性に優れたスーパー二相ステンレス鋼
JP5838796B2 (ja) 伸びフランジ性に優れた高強度熱延鋼板およびその製造方法
KR100733016B1 (ko) Тｉ첨가 페라이트계 스테인레스 강판 및 그 제조방법
EP4269642A1 (fr) Matériau d'acier
WO2022145065A1 (fr) Matériau d'acier
WO2022145067A1 (fr) Matériau d'acier
EP2895637A1 (fr) Produits d'acier à haute résistance et de faible densité renforcé par des particules de tic présentant un module e amélioré et procédé pour la production dudit produit
CN108138288B (zh) 热锻造用钢及热锻造品
EP2738281B1 (fr) Acier inoxydable austénitique à haute teneur en si
JP6390573B2 (ja) 冷延鋼板およびその製造方法
JP7469714B2 (ja) 鋼材
WO2022145066A1 (fr) Matériau d'acier
JP2020164956A (ja) フェライト系ステンレス鋼板およびその製造方法
TWI768941B (zh) 耐疲勞特性優異的析出硬化型麻田散鐵系不銹鋼板
WO2022145068A1 (fr) Matériau d'acier
WO2022145070A1 (fr) Acier
TW202233864A (zh) 麻田散鐵系不鏽鋼材及其製造方法
JP7303414B2 (ja) 鋼板
WO2023053827A1 (fr) Tôle d'acier
JP3149476B2 (ja) 希土類元素含有低窒素鋼の造塊方法
JP6950071B2 (ja) Ｎｉ−Ｃｒ−Ｍｏ−Ｎｂ合金
WO2022138194A1 (fr) Acier inoxydable martensitique durci par précipitation, doté d'excellentes caractéristiques de résistance à la fatigue
JP3513001B2 (ja) 超大入熱溶接熱影響部の靱性に優れた溶接用高張力鋼
WO2022145069A1 (fr) Matériau d'acier
JP2003342670A (ja) 靭性の優れた非調質高張力鋼

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 21914927

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 21914927

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: JP