WO2001059167A1 - Produit d'acier a zone de soudure traitee d'une excellente rigidite - Google Patents

Produit d'acier a zone de soudure traitee d'une excellente rigidite Download PDF

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Publication number
WO2001059167A1
WO2001059167A1 PCT/JP2000/007999 JP0007999W WO0159167A1 WO 2001059167 A1 WO2001059167 A1 WO 2001059167A1 JP 0007999 W JP0007999 W JP 0007999W WO 0159167 A1 WO0159167 A1 WO 0159167A1
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Prior art keywords
steel
steel material
toughness
mass
affected zone
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PCT/JP2000/007999
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English (en)
Japanese (ja)
Inventor
Masanori Minagawa
Toshihiko Koseki
Yuji Funatsu
Jun Ohtani
Tomohiko Hada
Tadashi Ishikawa
Masaaki Nagahara
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Nippon Steel Corporation
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Priority claimed from JP2000033242A external-priority patent/JP2001226739A/ja
Application filed by Nippon Steel Corporation filed Critical Nippon Steel Corporation
Priority to EP00974966A priority Critical patent/EP1262571B1/fr
Priority to DE60021919T priority patent/DE60021919T2/de
Publication of WO2001059167A1 publication Critical patent/WO2001059167A1/fr

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    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the present invention relates to a steel material for a welded structure having excellent toughness in a heat affected zone (hereinafter, referred to as HAZ) used for ships, marine structures, middle and high-rise buildings, and the like.
  • HAZ heat affected zone
  • Japanese Patent Publication No. 55-26164 there is a method of reducing the austenite grains of HAZ and improving the toughness by securing fine Ti nitrides in the steel. is there.
  • Japanese Patent Application Laid-Open No. 3-264614 proposes a method for improving the toughness of HAZ by utilizing a composite precipitate of Ti nitride and MnS as a transformation nucleus of ferrite.
  • Japanese Patent Application Laid-Open No. 4-143246 proposes a method of improving the toughness by utilizing a composite precipitate of ⁇ -nitride and BN as a precipitation nucleus of grain boundary phenylite.
  • Ti nitride has a maximum temperature of 1400 ° C in HAZ.
  • the weld bond In the vicinity of the boundary with the weld metal (called the weld bond), the solid solution is almost completely dissolved, and the effect of improving the toughness is degraded. It is difficult to achieve HAZ toughness in heat input welding.
  • steels containing oxides are used in various fields such as thick plates and section steels.
  • steels containing oxides are very effective in improving the toughness of large heat input welds. Therefore, its application to high-tensile steel is promising.
  • This principle is based on the fact that peroxides, which are stable even at the melting point of steel, are used as sites, and Ti nitrides, MnS, etc. precipitate during the lowering of the temperature after welding, and they are used as sites. Fine ferrite is generated, and as a result, generation of coarse ferrite harmful to toughness is suppressed, and deterioration of toughness can be prevented.
  • Ti oxides cannot increase the number dispersed in the steel.
  • the cause is the coarsening and agglomerated coalescence of ⁇ ⁇ oxide. If the number of ⁇ ⁇ oxides is to be increased, coarse ⁇ ⁇ oxides of 5; am or more, so-called inclusions, will increase. U. These inclusions of 5 m or more are harmful as a starting point for structural destruction and cause a decrease in toughness. Therefore, in order to further improve the HAZ toughness, it is necessary to use an oxide which is less likely to be coarsened and aggregated and which is more finely dispersed than a Ti oxide.
  • such a method of dispersing Ti oxide in steel is by adding Ti to molten steel substantially free of a strongly deoxidizing element such as A1.
  • a strongly deoxidizing element such as A1.
  • problems such as insufficient number of Ti oxides and fluctuation of toughness in the thickness direction of a thick plate. Is recognized.
  • the upper limit of the amount of A1 is limited to a very small amount of 0.007% in order to easily form a peroxide. If the amount of A1 in the steel material is small, the toughness of the base metal may decrease due to a shortage of A1N precipitates and other causes. Further, when a steel sheet having a small amount of A1 is welded using a commonly used welding material, the toughness of the weld metal may be reduced.
  • Japanese Patent Application Laid-Open No. 6-293937 proposes a technique that utilizes the Ti-A1 composite oxide generated by adding A1 immediately after the addition.
  • large heat input welding HAZ toughness can be greatly improved, but in recent years, in the shipbuilding industry and the construction industry, welding heat input of over 200 kJZcm and as large as 100 kJZcm has been achieved.
  • steel materials with even higher HAZ toughness are needed. In this case, it is necessary to improve the toughness especially in the vicinity of the weld fusion zone. Disclosure of the invention
  • An object of the present invention was to provide a steel material having HAZ toughness and having excellent heat-affected zone toughness.
  • the present invention has been made to solve the above-mentioned problems, and the gist thereof is as follows.
  • the balance is steel consisting of Fe and unavoidable impurities.
  • Also, oxide particles with a circle equivalent diameter of 0.005 to 2.0 m in the above steel have a number density of 100 to 3,000 particles per unit area per unit area.
  • mm 2 contain, Ca also less composition of the oxide particles include Al, 0, elemental mass 0/0 except for 0, Ca: 5% or more, A1: containing 5% or more, A steel material with excellent toughness in the heat affected zone, characterized by the balance consisting of Fe and other unavoidable impurities.
  • the steel material further contains Mg: 0.0001 to 0.002% by mass, and the composition of the oxide particles when Mg is contained contains at least Ca, Al, Mg, ⁇ , and 0 is excluded.
  • the composition of the oxide particles of the steel material contains at least Ca, Al, Mg, ⁇ , and S, and the elements excluding ⁇ are mass%.
  • Ca 5% or more
  • A1 5% or more
  • the steel material further contains B: 0.0005 to 0.003% by mass%
  • FIG. 1 is a diagram showing the relationship between the number of oxide particles in steel and the HAZ toughness in claims 1 to 4 of the present invention.
  • FIG. 2 is a diagram showing the relationship between the number of oxide particles in steel and HAZ toughness according to claim 5 of the present invention.
  • FIG. 3 is a diagram showing the scope of the present invention in relation to the equivalent equation EN and HAZ toughness.
  • FIG. 4 is a diagram showing a preferred range of the present invention in relation to the equivalent equation EN and HAZ toughness.
  • the present inventors studied the use of oxides to achieve reheating austenite grain refinement in the HAZ region heated to 1400 ° C or higher as a metal structure factor that improves HAZ toughness. .
  • nitrides and oxides are effective as one of the dispersed particles having such an effect.
  • nitrides have a high pinning effect at high temperatures of 1400 ° C or higher, so the pinning effect is reduced.
  • oxides that are stable at high temperatures as pinning particles.
  • the pinning effect of the crystal grain boundaries by the dispersed particles increases as the volume ratio of the dispersed particles increases and as the diameter of one particle increases.
  • the volume fraction of the dispersed particles has an upper limit depending on the concentration of the elements constituting the particles contained in the steel, if the volume fraction is assumed to be constant, a smaller particle diameter is more effective for pinning. It is. From such a viewpoint, the present inventors have conducted various studies to increase the volume fraction of the oxide and to obtain an appropriate particle diameter.
  • A1 is generally used as a substance having a small solubility product with oxygen, that is, as a strong deoxidizing element.
  • A1 alone is not enough to fully utilize oxygen, and requires a stronger deoxidizing element than A1, and utilizes Ca, which is commonly used in the steel deoxidation process. It is important to. Because Ca has a small solubility product with oxygen, it can produce more oxide than A 1 for the same amount of oxygen.
  • the composition of oxide particles generated in steel was found to contain 3% or more of Ca and 1% or more of A1. It has been found that it is possible to increase the volume fraction of oxides, that is, the amount of oxides. Based on these results, the composition of the oxide particles contained in the steel was determined to be at least 3% or more by mass, with elements other than 0 containing at least 3% Ca and 1 % Or more.
  • Mg is also effective in producing a large number of oxides.
  • Mg is not as effective as Ca, it is a stronger deoxidizing element than A 1 and has a lower solubility product with oxygen. Therefore, it is possible to further increase the number of oxides by combining Mg with Ca and using it for deoxidation.
  • the inventors conducted an experiment using Ca as a deoxidizing element. As a result, the composition of oxide particles formed in steel was 5% or more for Ca, 5% or more for A1, and 1% for Mg. It has been found that the inclusion of at least% makes it possible to further increase the volume fraction of the oxide, that is, the amount of the oxide. Based on these results, the composition of the oxide particles contained in the steel was determined to include at least Ca, A, Mg, and % And Mg was set to 1% or more.
  • the present inventors have found that sulfides such as CaS and MgS are precipitated around the oxide, thereby further increasing the volume fraction of the oxide and the sulfide together. They found that it was possible. Based on this result, the composition of the particles contained in the steel should be at least Ca, A 1, 0, S The elements excluding 0 are, by mass ratio, at least 5% of Ca, at least 5% of Al,
  • S is 1% or more, or at least contains Ca, A and Mg, 0, S,
  • the elements excluding ⁇ were determined to have a mass ratio of Ca of 5% or more, A1 of 5% or more, Mg of 1% or more, and S of 1% or more.
  • the effect of the present invention is effective even if Mg or / and REM having deoxidizing power between A1 and Ca is included as the remaining oxide constituent element.
  • the effects of the present invention are not affected even if deoxidizing elements weaker than Al such as Si, ⁇ and ⁇ ⁇ ⁇ which are inevitably mixed and / or impurity elements such as Ca which are unavoidably mixed with Ca are included. Confirmed that there is not.
  • the size of oxide particles effective for pinning will be described.
  • the effect of the dispersed particles on the pinning of the grain boundaries is larger as the volume fraction of the dispersed particles is larger and as the diameter of one particle is larger, but when the volume ratio of the particles is constant, the size of one oxide particle is smaller. It is thought that the larger the number of particles, the greater the pinning effect. However, if the particle size is too small, the proportion of the particles present at the grain boundaries will be small, so the effect is considered to be reduced.
  • a detailed examination of the austenite particle size when heated to a high temperature using test specimens with various particle sizes revealed that the pinning used was 0.005 to 2. We found that the one with 0 im had a greater effect.
  • HAZ toughness varies in a complex manner depending on the application and the welding method used. In particular, in order to satisfy the HAZ toughness required for large heat input welding of high-strength shipbuilding steel, which is considered to have strict requirements, for example, to achieve an absorbed energy of 50 J or more at a test temperature of -40 ° C.
  • the number of oxide particles with a circle equivalent diameter of 0.005 to 2.0 ⁇ m was required to be 100 particles / band 2 or more, as shown in Fig. 1.
  • the upper limit of the number of grains child is 3,000 Z ⁇ 2 is appropriate.
  • the size and number of the oxide particles are measured, for example, in the following manner. To prepare an extraction replica of a steel plate as a base material, it at 1 0000 times with an electron microscope 20 field of view over the size and number of the oxide in the observation child to 1 000 m 2 or more in the observation area Is measured. In the measurement of the size, for example, a circle-equivalent diameter is obtained based on a photograph of a particle. At this time, the extracted replica from any part from the surface layer to the center of the steel plate may be used. If the particles can be observed properly, the observation magnification may be reduced.
  • Oxide particles are generated when deoxidizing molten steel. This is called a primary oxide. Furthermore, during rusting and solidification, Ti-Al-Ca oxide is generated with a decrease in the temperature of the molten steel. This is called a secondary oxide. In the present invention, either a primary oxide or a secondary oxide may be used.
  • the present inventors have further studied to dramatically improve the effect of improving the toughness by making the HAZ structure finer.
  • the reheated austenite grains are refined by dispersing a large number of fine oxides, it is necessary to suppress the growth of ferrite at grain boundaries and grain boundary triple points during the formation process of the HAZ structure.
  • B were found to be extremely effective.
  • the balance between B and N is important, and B is completely trapped in N at the stage where phenylite formation occurs during cooling of the welding heat cycle.
  • the solid solution remained and increased the effect of adding B, significantly improving the toughness of fine-grained HAZ and stabilizing it.
  • the equivalent value is in the range of 0.004 to -0.0005, preferably in the range of 0 to 0.002
  • the equivalent value is less than -0.004
  • the iron and B become a solid solution at the same time as B, and the toughness deteriorates due to a marked increase in hardenability.
  • it exceeds 0 0.0005 solid solution cannot be secured, and there is no effect of miniaturizing the fly.
  • oxides are not affected by the process of producing steel, whether it is normal rolling, controlled rolling, a combination of controlled rolling and tempering, or a combination of quenching and tempering. .
  • the lower limit of C is 0.03% as an effective component to improve the strength of steel, and the upper limit is 0.18% because excessive addition significantly reduces the weldability and toughness of steel materials.
  • Si is a component necessary for securing the strength of the base material and deoxidizing, but the upper limit is set to 0.5% in order to prevent the toughness from decreasing due to the hardening of HAZ.
  • Mn is an effective component for securing the strength and toughness of the base material, and it is necessary to add 0.4% or more, but the upper limit is 2.0% within the allowable range of the toughness and cracking of the weld.
  • A1 is an important deoxidizing element, and the lower limit was set to 0.005%. In addition, the upper limit was set to 0.04% because the presence of a large amount of A1 deteriorates the surface quality of the cypress.
  • Ti is added in an amount of 0.005% or more in order to combine with N to form a nitride.
  • the upper limit is 03%.
  • Ca must be added in an amount of 0.0005% or more in order to form a Ca-based oxide.
  • the upper limit was set to 0.003%, since excessive addition generates coarse inclusions.
  • Mg must be added in an amount of 0.0001% or more to generate Mg-based oxides. However, excessive addition causes coarse inclusions to be formed, so the upper limit was 0.002%.
  • N has the effect of improving HAZ toughness by precipitating as TiN, the lower limit was made 0.0005%. However, the increase in solute N leads to a decrease in HAZ toughness, so the upper limit was made 0.007%.
  • B is an effective element that suppresses the growth of ferrite formed at the grain boundaries of the heated austenite grains in a solid solution state, and is added at least 0.0005%. However, if added in large amounts, the toughness of the steel will deteriorate, so the upper limit was made 0.003%.
  • Cu is effective for improving the strength of steel, but if it exceeds 1.0%, the HAZ toughness is reduced, so the upper limit was set to 1.0%.
  • Ni is effective in improving the strength and toughness of the steel material, but the increase in the amount of Ni increases the production cost, so the upper limit was 1.5%.
  • Nb is an effective element for improving the strength and toughness of the base material by improving the hardenability, but in the HAZ part, excessive addition significantly reduces toughness, so 0.04% The upper limit was set.
  • REN has the deoxidizing power next to Ca in molten steel and has the function of assisting the formation of fine oxides due to Ca.However, excessive addition of REN increases the cost as compared with Ca, and reduces coarse inclusions.
  • the upper limit is set to 0.05% because the steel sheet and HAZ are made to prevent the toughness.
  • a 50 kg steel was prototyped with the chemical composition shown in Table 1.
  • 1 to 8 are steels of the present invention, and 9 to 14 are comparative steels.
  • the prototype steel is melted in a converter and deoxidized during vacuum degassing at RH. ⁇ Adjust the dissolved oxygen of molten steel with Si before charging, then add Ti and A1 in order to perform deoxidation. After rolling, it was manufactured as a steel sheet with a thickness of 45 mm. The obtained steel sheet was subjected to one-pass SEGARC welding. Heat input is about 200 kJ / cm 2.
  • Table 2 shows the composition of the oxide particles, the number of particles having a particle size of 0.005 to 2.0 m, the rolling conditions of the steel sheet, the properties of the base material, and the toughness of HAZ.
  • the Charpy value for the HAZ toughness evaluation is the average value of nine tests performed on a fusion linker, HAZ 1 mm site.
  • the steels of the present invention 1 to 8 have excellent HAZ toughness as compared with the comparative steel. That is, since the particle diameter, the number of particles, and the amount of the composition of the oxide are within the range of the present invention, the HAZ toughness at ⁇ 40 is extremely excellent. Further, in the present invention steel, the oxide particle size 0.1 to 2.0 m is invention steel 3 is in the range of 100 to 3000 pieces / 111111 2, 4, 5, 6, 8, Mg oxide particles composition 1 Inventive steels 2, 4, 5, 6, 7, 8, which have a HAZ toughness better than those of the present invention. I understand that there is.
  • Comparative Examples 9 to 16 all showed only Charpy test—low toughness of less than 40 J at 40 ° C. This is because in Comparative Example 9, the Ca content, the Mg content, and the number of oxide particles, which are the oxide particle compositions, were outside the lower limits of the present invention, and in Comparative Example 10, the Ca content of the oxide particles and the number of oxide particles were small. Is outside the lower limit of the present invention. Further, Comparative Examples 11 to 15 are because the number of oxide particles was outside the lower limit of the present invention.
  • a 50-60 kg steel was prototyped with the chemical composition shown in Table 3. 17 to 24 are steels of the present invention, and 25 to 31 are comparative steels.
  • the prototype steel is melted in a converter and deoxidized during vacuum degassing at RH. ⁇ Adjust the dissolved oxygen of molten steel with Si before charging, then add Ti, A and Ca in order, deoxidize, rust into 280mm thick cylin flakes by continuous forging, then heat roll, It was manufactured as a steel plate with a thickness of 50 mm.
  • the obtained steel sheet was subjected to one-pass electroloss slag welding. Heat input is about 280kJ / cra 2.
  • the average diameter of austenite grains in the AZ structure, the maximum ferrite size (width) at the austenite grain boundary or the triple point of the grain boundary, and the toughness of HAZ are shown.
  • the Charpy test for evaluating the HAZ toughness was performed at -40 ° C, and the values shown are the average values of nine tests performed at 1 mm HAZ from the bond.
  • the steels of the present invention Nos. 17 to 24 have excellent HAZ toughness as compared with the comparative steels.
  • a particle diameter 0. 005-2. 0, Ca by that it is a range of the number particle of 100 to 3000 pieces / mm 2 of oxide including A 1 at a predetermined composition, as compared with comparative steel
  • the austenite grain size of the HAZ structure is small, and the austenite grain boundary or the triple point grain boundary fly is also small due to the effect of B.
  • the Charpy absorbed energy value of -40 ° C Is much higher than the average of 50 J generally required from the viewpoint of the fracture mechanics of steel structures, and it is clear that the HAZ toughness is extremely excellent.
  • 17, 18, 20, 21, 23, and 24 also had 100 particles with a particle size of 0.1 to 2.0 um and Z particles 2 or more, and were relatively austenitic compared to 19 and 22. Small in diameter and high in Charpy absorbed energy.
  • Comparative Examples 25 to 31 all showed low toughness of less than 50 J at Charpy test—40 ° C.
  • the reason for this is that in Comparative Examples 25 to 28, the chemical composition of the steel material was out of the range of the present invention, and the oxide particles did not have the composition and the number within the range of the present invention. This is because the composition and the number are within the range of the present invention, but the EN equivalent is out of the range of the present invention.
  • the steel had a higher oxygen content than other steels, and the number of oxide particles was outside the upper limit of the present invention.
  • a 50-60 kg steel was prototyped with the chemical composition shown in Table 5.
  • 32 to 39 are steels of the present invention, and 40 to 46 are comparative steels.
  • the prototype steel is melted from the converter and deoxidized during vacuum degassing at RH. ⁇ Adjust the dissolved oxygen of molten steel with Si before charging, then add T and then add Ca in order to deoxidize, form into 280-mm thick rust slab by continuous forming, and heat-roll. After that, it was manufactured as a 50 mm thick steel plate. The obtained steel plate was subjected to one-pass electrogas welding. Heat input is about 280kJ / cm 2.
  • the HAZ toughness value is calculated from the HAZ
  • the inventive steels of Nos. 32 to 39 have excellent HAZ toughness as compared with the comparative steels.
  • a particle diameter 0. 005-2. 0, Ca by that it is a range of the number particle is 100-3000 Kono ⁇ second oxide containing A 1 at a predetermined composition, as compared with comparative steel
  • the austenite grain size of the HAZ structure is small, and the austenite grain boundary or the triple point grain boundary fly is also small due to the effect of B.
  • the Charpy absorbed energy of 140 ° C is obtained.
  • the value greatly exceeds the average of 50 J generally required from the viewpoint of the fracture mechanics of steel structures, and it is clear that the HAZ toughness is extremely excellent.
  • Comparative Examples 40 to 46 showed low toughness of less than 50 J at 40 ° C. in the Charpy test. The reason is that the chemical components deviated from the range of the present invention in the range of 40 to 43, and the composition and number of the oxide particles were out of the range of the present invention. Comparative Examples 44 and 45 indicated the composition and the number of the oxide particles. Is within the scope of the present invention, but the EN equivalent is out of the scope of the present invention. In Comparative Example 46, the oxygen content in the steel was higher than that of the other steels, and the number of oxide particles was outside the upper limit of the present invention, so that the toughness was lower than that of the steel of the present invention.
  • the present invention 200 kJ / cm 2 or more high heat input welding, Ri steel der having a welded joint toughness superior even to ultra adult heat welding is used ships, marine structures, high-rise buildings, etc. bridges
  • Ri steel der having a welded joint toughness superior even to ultra adult heat welding is used ships, marine structures, high-rise buildings, etc. bridges
  • steel pipe materials such as steel plates, bars, bars, hot-rolled steel plates, etc.
  • the toughness of the weld joint can be significantly improved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Nonmetallic Welding Materials (AREA)

Abstract

L'invention porte sur un produit d'acier à zone de soudure traitée d'une excellente rigidité dont la composition spécifique satisfait à 0 ≤ EN ≤ 0,002 dans une formule équivalente EN est représenté par (%N), (%Ti) et (%B) et contient au mm2 de 100 à 3000 particules d'oxyde d'un diamètre équivalent cercle compris entre 0,005 et 2 νm et de préférence entre 0,1 et 2 νm, et contenant du Ca, de l'Al et de l'O à raison de 3 % ou plus de la masse de C.a., et d'Al, et de moins de 1 % de la masse sans O, le reliquat étant constitué d'autres éléments hormis l'oxygène, et des impuretés inévitables. L'accroissement de la taille des grains d'austénite est pratiquement supprimée, ce qui améliore les caractéristiques HAZ dont la rigidité HAZ, qui sont notablement accrues.
PCT/JP2000/007999 2000-02-10 2000-11-13 Produit d'acier a zone de soudure traitee d'une excellente rigidite WO2001059167A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP00974966A EP1262571B1 (fr) 2000-02-10 2000-11-13 Acier a zone affectee thermiquement par soudage presentant une excellente tenacite
DE60021919T DE60021919T2 (de) 2000-02-10 2000-11-13 Stahl mit schweißwärmebeeinflusster Zone mit ausgezeichneter Zähigkeit

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JP2000033241 2000-02-10
JP2000033242A JP2001226739A (ja) 2000-02-10 2000-02-10 溶接熱影響部靭性に優れた鋼材
JP2000-33242 2000-02-10
JP2000068210 2000-03-13
JP2000-33241 2000-03-31
JP2000-68210 2000-03-31

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Cited By (5)

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Publication number Priority date Publication date Assignee Title
EP1416059A1 (fr) * 2002-10-29 2004-05-06 The Japan Steel Works, Ltd. Materiau de base pour une plaque d'acier plaqué ayant une bonne résistance mécanique à basse température dans la zone affectée par la chaleur de soudage et méthode de production de plaque en acier
WO2013077022A1 (fr) * 2011-11-25 2013-05-30 新日鐵住金株式会社 Matériau à base d'acier soudable
WO2014201887A1 (fr) 2013-06-19 2014-12-24 宝山钢铁股份有限公司 Tôle d'acier ht550 de résistance ultraélevée et d'excellente soudabilité et son procédé de production
WO2014201877A1 (fr) 2013-06-19 2014-12-24 宝山钢铁股份有限公司 Tôle d'acier présentant une résistance à la fissuration induite par le zinc et son procédé de production
US9403242B2 (en) 2011-03-24 2016-08-02 Nippon Steel & Sumitomo Metal Corporation Steel for welding

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4972451B2 (ja) * 2007-04-20 2012-07-11 株式会社神戸製鋼所 溶接熱影響部および母材の低温靭性に優れた低降伏比高張力鋼板並びにその製造方法
JP4399018B1 (ja) 2008-07-15 2010-01-13 新日本製鐵株式会社 溶接熱影響部の靭性に優れた鋼板
EP2729590B1 (fr) * 2011-07-10 2015-10-28 Tata Steel IJmuiden BV Bande d'acier haute résistance laminée à chaud avec résistance élevée au ramollissement haz et son procédé de production
WO2014141632A1 (fr) * 2013-03-12 2014-09-18 Ｊｆｅスチール株式会社 Tôle épaisse en acier présentant d'excellentes propriétés ctod dans des joints soudés multicouches, et procédé de fabrication de tôle épaisse en acier

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08158006A (ja) * 1994-12-06 1996-06-18 Kobe Steel Ltd 溶接熱影響部の靭性が優れた高強度鋼
JPH10183295A (ja) * 1996-12-19 1998-07-14 Nippon Steel Corp 大入熱溶接の熱影響部靭性の優れた鋼材およびその製造方法
JPH11229078A (ja) * 1998-02-16 1999-08-24 Kobe Steel Ltd 母材および大入熱溶接熱影響部の靱性に優れた高張力鋼板およびその製造方法
JP2000001738A (ja) * 1998-04-15 2000-01-07 Nippon Steel Corp 溶接熱影響部の靱性に優れた鋼板

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08158006A (ja) * 1994-12-06 1996-06-18 Kobe Steel Ltd 溶接熱影響部の靭性が優れた高強度鋼
JPH10183295A (ja) * 1996-12-19 1998-07-14 Nippon Steel Corp 大入熱溶接の熱影響部靭性の優れた鋼材およびその製造方法
JPH11229078A (ja) * 1998-02-16 1999-08-24 Kobe Steel Ltd 母材および大入熱溶接熱影響部の靱性に優れた高張力鋼板およびその製造方法
JP2000001738A (ja) * 1998-04-15 2000-01-07 Nippon Steel Corp 溶接熱影響部の靱性に優れた鋼板

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP1262571A4 *

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1416059A1 (fr) * 2002-10-29 2004-05-06 The Japan Steel Works, Ltd. Materiau de base pour une plaque d'acier plaqué ayant une bonne résistance mécanique à basse température dans la zone affectée par la chaleur de soudage et méthode de production de plaque en acier
US9403242B2 (en) 2011-03-24 2016-08-02 Nippon Steel & Sumitomo Metal Corporation Steel for welding
WO2013077022A1 (fr) * 2011-11-25 2013-05-30 新日鐵住金株式会社 Matériau à base d'acier soudable
JP5201301B1 (ja) * 2011-11-25 2013-06-05 新日鐵住金株式会社 溶接用鋼材
WO2014201887A1 (fr) 2013-06-19 2014-12-24 宝山钢铁股份有限公司 Tôle d'acier ht550 de résistance ultraélevée et d'excellente soudabilité et son procédé de production
WO2014201877A1 (fr) 2013-06-19 2014-12-24 宝山钢铁股份有限公司 Tôle d'acier présentant une résistance à la fissuration induite par le zinc et son procédé de production

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DE60021919D1 (de) 2005-09-15
EP1262571A4 (fr) 2003-03-26
EP1262571A1 (fr) 2002-12-04
KR20020073579A (ko) 2002-09-27
EP1262571B1 (fr) 2005-08-10
EP1520912A3 (fr) 2005-04-27
DE60033070D1 (de) 2007-03-08
DE60033070T2 (de) 2007-05-31
EP1520912A2 (fr) 2005-04-06
EP1520912B1 (fr) 2007-01-17
KR100514667B1 (ko) 2005-09-14
DE60021919T2 (de) 2006-06-08

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