EP1029938A2 - Acier laminé ayant peu de défauts d'inclusions - Google Patents

Acier laminé ayant peu de défauts d'inclusions Download PDF

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Publication number
EP1029938A2
EP1029938A2 EP00102280A EP00102280A EP1029938A2 EP 1029938 A2 EP1029938 A2 EP 1029938A2 EP 00102280 A EP00102280 A EP 00102280A EP 00102280 A EP00102280 A EP 00102280A EP 1029938 A2 EP1029938 A2 EP 1029938A2
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EP
European Patent Office
Prior art keywords
mass
principal component
crystallized
crystallized phase
steel
Prior art date
Legal status (The legal status 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 status listed.)
Withdrawn
Application number
EP00102280A
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German (de)
English (en)
Other versions
EP1029938A3 (fr
Inventor
Toshiaki Mizoguchi
Yoshiyuki Ueshima
Katsumi Kondo
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel Corp
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
Priority claimed from JP03964799A external-priority patent/JP3462779B2/ja
Priority claimed from JP10980599A external-priority patent/JP3462790B2/ja
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of EP1029938A2 publication Critical patent/EP1029938A2/fr
Publication of EP1029938A3 publication Critical patent/EP1029938A3/fr
Withdrawn legal-status Critical Current

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Classifications

    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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 rolled steel having few inclusion defects suitable for producing steel sheets for automobile use, steel sheets for making deeply drawn cans, and steel pipes.
  • pieces of rolled steel such as steel sheets and steel pipes are made of aluminum killed steel obtained when molten steel made by a converter, which has not been deoxidized yet, is deoxidized by aluminum.
  • surface defects and internal defects such as sliver flaws (linear flaws) caused in the process of cold rolling, cracks and pin holes caused in the case of deep drawing and defects detected in weld zones of steel pipes by the ultrasonic test are caused by inclusions in some cases. It is known that those inclusion defects are caused by the inclusion of oxides, such as alumina, created in the process of deoxidation conducted in molten steel in refining.
  • particles of CaO-Al 2 O 3 which are created when Ca is added into molten steel, are enlarged, and the thus created particles of CaO-Al 2 O 3 can not be raised to the surface of molten steel, that is, the thus created particles of CaO-Al 2 O 3 remain in molten steel. In this case, defects are caused by the particles of CaO-Al 2 O 3 .
  • the present invention has been accomplished to solve the above conventional problems. It is an object of the present invention to provide rolled steel having few inclusion defects in which particles of oxide inclusions are kept fine and capable of being dispersed in rolled steel.
  • the present invention provides rolled steel having few inclusion defects, the basic composition of which is C: 0.0002 to 0.7 mass %, Si: 0.001 to 0.5 mass %, Mn: 0.005 to 2.0 mass %, P: 0.001 to 0.05 mass %, S: 0.0005 to 0.15 mass %, Ti: 0.001 to 0.25 mass % and dissolved Al: 0.001 to 0.1 mass %, wherein created oxide inclusions are mainly composed of a crystallized phase, the principal component of which is titanium-oxide, and a crystallized phase, the principal component of which is alumina, and the crystallized phases of oxide inclusions exist in steel.
  • the present invention provides rolled steel having few inclusion defects, the basic composition of which is C: 0.0002 to 0.7 mass %, Si: 0.001 to 0.5 mass %, Mn: 0.005 to 2.0 mass %, P: 0.001 to 0.05 mass %, S: 0.0005 to 0.15 mass %, Ti: 0.001 to 0.25 mass % and dissolved Al: 0.001 to 0.1 mass %, the selective composition of which is Ca: not more than 50 ppm and Mg: not more than 50 ppm, at least one of Ca and Mg being contained, wherein created oxide inclusions are mainly composed of a crystallized phase, the principal component of which is titanium-oxide, and a crystallized phase, the principal component of which is alumina, and further composed of at least one of a crystallized phase, the principal component of which is CaO, and a crystallized phase, the principal component of which is MgO, and the crystallized phases of oxide inclusions exist
  • the crystallized phases of oxide inclusions are dispersed in rows in the direction of rolling near the center of a piece of rolled steel. It is preferable that Micro-Vickers hardness of the oxide inclusions at the room temperature is in a range from 600 to 1300 Hv. Further, it is preferable that the maximum diameter of the particles of oxide inclusions obtained by slime extraction is not more than 300 ⁇ m. Furthermore, it is preferable that the number of the particles of oxide inclusions obtained by slime extraction, the diameter of which is not less than 38 ⁇ m, is not more than 50 pieces/kg.
  • rolled steel includes steel sheets, steel pipes, shape steel, bar steel and wire rods.
  • the basic composition of the rolled steel is C: 0.0002 to 0.7 mass %, Si: 0.001 to 0.5 mass %, Mn: 0.005 to 2.0 mass %, P: 0.001 to 0.05 mass %, S: 0.0005 to 0.15 mass %, Ti: 0.001 to 0.25 mass % and dissolved Al: 0.001 to 0.1 mass %.
  • rolled steel includes steel sheets, steel pipes, shape steel, bar steel and wire rods.
  • the basic composition of the rolled steel is C: 0.0002 to 0.7 mass %, Si: 0.001 to 0.5 mass %, Mn: 0.005 to 2.0 mass %, P: 0.001 to 0.05 mass %, S: 0.0005 to 0.15 mass %, Ti: 0.001 to 0.25 mass % and dissolved Al: 0.001 to 0.1 mass %, and the selective composition of the rolled steel is Ca: not more than 50 ppm and Mg: not more than 50 ppm, wherein at least one of Ca and Mg is contained.
  • Carbon is an essential element to stably enhance the mechanical strength of steel. Therefore, the content of carbon is adjusted in a range from 0.0002 to 0.7% according to the desired mechanical strength of material. In order to ensure the mechanical strength or hardness, it is necessary that rolled steel contains carbon at not less than 0.0002%, however, when the content of carbon is higher than 0.7%, the workability is lowered. Therefore, the content of carbon is kept so that it cannot exceed 0.7%.
  • the reason why the content of Si is kept in a range from 0.001 to 0.5% is described below.
  • the content of Si is in a range lower than 0.001%, it becomes necessary to conduct pretreatment of material, and the cost of refining is increased, that is, it is not economical to keep the content of Si in a range lower than 0.001%.
  • the content of Si is higher than 0.5%, defects are caused in the process of plating, and the surface property and the corrosion resistance are impaired.
  • the reason why the content of Ti is kept in a range from 0.001 to 0.25% is described below.
  • the content of Ti is lower than 0.001%, it becomes difficult to cast molten steel.
  • the content of Ti is higher than 0.25%, only titanium oxide, which tends to become clusters, is created, and the diameters of inclusion particles are enlarged. As a result, sliver flaws are caused in the same manner as that of alumina.
  • the present invention provides rolled steel, the basic composition of which is described above, and the oxide inclusions created in the processes of deoxidation and coagulation are mainly composed of a crystallized phase, the principal component of which is Ti oxide, and a crystallized phase, the principal component of which is alumina, and the crystallized phases of oxide inclusions are dispersed in steel.
  • the present invention provides rolled steel, the basic composition and the selective composition of which are described above, and the oxide inclusions created in the processes of deoxidation and coagulation are mainly composed of a crystallized phase, the principal component of which is Ti oxide, and a crystallized phase, the principal component of which is alumina, and also composed of at least one of a crystallized phase, the principal component of which is CaO, and a crystallized phase, the principal component of which is MgO, and the crystallized phases of oxide inclusions are dispersed in steel.
  • the crystallized phase is a crystal phase in a solid state, that is, the crystallized phase does not include a glass phase in a solid state.
  • a crystallized phase composed of at least two phases of the crystallized phase, the principal component of which is Ti oxide, and the crystallized phase, the principal component of which is alumina
  • a crystallized phase composed of at least three phases of the crystallized phase, the principal component of which is Ti oxide, the crystallized phase, the principal component of which is alumina, and at least one of the crystallized phase, the principal component of which is CaO
  • the crystallized phase, the principal component of which is MgO the crystallized phase itself is made to be fine, and further the crystallized phase is easily crushed to more fine particles.
  • the crystallized phases of oxide inclusions are dispersed in rows in the direction of rolling near the center with respect to the thickness of a piece of rolled steel. Since the oxide inclusions seldom exist on the surface of the piece of rolled steel, it is possible to obtain rolled steel having few inclusion defects.
  • Micro-Vickers hardness of oxide inclusions at the room temperature is in a range from 600 to 1300 Hv.
  • the reason why the hardness is kept in the above range is described as follows.
  • the hardness is lower than 600 Hv, the inclusions are excessively elongated.
  • the hardness is higher than 1300 Hv, the inclusions are seldom elongated, and it becomes difficult to crush and disperse the inclusions by rolling.
  • the maximum diameter of the particles of oxide inclusions obtained by slime extraction is not larger than 300 ⁇ m and further the number of the particles of oxide inclusions, the diameters of which are not less than 38 ⁇ m, is kept to be not more than 50 pieces/kg, there is little possibility that the particles of oxide inclusions on the surface of rolled steel are drawn out in rows, and it is possible to obtain rolled steel having few inclusion defects.
  • the present invention provides rolled steel, the characteristics of which are described as follows.
  • Oxide inclusions created in the processes of deoxidation and coagulation are mainly composed of a crystallized phase, the principal component of which is Ti oxide, and a crystallized phase, the principal component of which is alumina.
  • oxide inclusions are made to be oxides composed of the two phases of the crystallized phase, the principal component of which is Ti oxide, and the crystallized phase, the principal component of which is alumina, and the crystallized phases of the oxides are made to be fine.
  • the oxide inclusions are further crushed and dispersed by rolling in rows on an interface of the crystallized phase, the particles of which are made to be fine.
  • the inclusion when the inclusion is made to be inclusion of the crystallized phase, the principal component of which is fine particles of Ti oxide, and/or the crystallized phase, the principal component of which is alumina, the product defects, which are caused by oxide inclusions, such as sliver flaws in the process of cold rolling, cracks, pin holes and defects detected in the process of UST, can be greatly reduced.
  • oxide inclusions created in the processes of deoxidation and coagulation are mainly composed of a crystallized phase, the principal component of which is Ti oxide, and a crystallized phase, the principal component of which is alumina. Further, oxide inclusions created in the processes of deoxidation and coagulation are mainly composed of at least one of the crystallized phase, the principal component of which is CaO, and the crystallized phase, the principal component of which is MgO.
  • oxide inclusions are made to be oxides composed of at least three phases of the crystallized phase, the principal component of which is Ti oxide, the crystallized phase, the principal component of which is alumina, and at least one of the crystallized phase, the principal component of which is CaO, and the crystallized phase, the principal component of which is MgO.
  • oxide inclusions are further crushed and dispersed by rolling in rows on the interface of the crystallized phase, the particles of which are made to be fine.
  • the inclusions are made to be inclusions of the crystallized phase, the principal component of which is fine particles of Ti oxide, and/or the crystallized phase, the principal component of which is alumina, and also when the inclusions are made to be inclusions of at least one of the crystallized phase, the principal component of which is CaO, and the crystallized phase, the principal component of which is MgO, the product defects, which are caused by oxide inclusions, such as sliver flaws in the process of cold rolling, cracks, pin holes and defects detected in the process of UST, can be greatly reduced.
  • Pieces of rolled steel were produced by a vertical bend-type continuous casting machine under the condition that the slab size was 245 mm thickness ⁇ 1200 to 1600 mm width, the casting speed was 1.4 to 1.7 m/min, and the temperature of molten steel in the tundish was 1560°C. After that, the slabs were hot-rolled, and then the pieces of hot-rolled steel were subjected to acid pickling, cold rolling, annealing and secondary cold rolling when necessary. In this way, products shown on Table 1 were produced.
  • Deoxidizing alloy used in the production process and the principal components contained in the crystallized phase of oxide inclusions are shown in Table 2.
  • the hardness of oxide inclusions, the existing formation and the ratio of occurrence of defects are shown in Table 3. It can be seen from these tables that the present invention can greatly reduce the defects of products caused by oxide inclusions so that the productivity can be enhanced.
  • the components of the crystallized phase of inclusions shown in Table 2 were identified in such a manner that the inclusions extracted from a piece of rolled steel of full thickness by means of slime electrolytic extraction (the minimum mesh was 38 ⁇ m) was subjected to component identification by SEM (Scanning Electron Microscope) having EDX (Energy Dispersive X-ray Spectrometer). Further, concerning the additional component detected in the above component identification, the content was found by the integral intensity of the peak of the characteristic X-rays.
  • the full thickness of a section parallel to the rolling direction was observed by an optical microscope, and the existing inclusion formation was determined by an optical microscopic photograph (the magnification was 400 and the total number of field of view was 50) which was taken at a position where the inclusion exists.
  • the full thickness of a section parallel to the drawing direction was observed by an optical microscope, and the existing inclusion formation was determined by an optical microscopic photograph (the magnification was 400 and the total number of field of view was 50) which was taken at a position where the inclusion exists.
  • Pieces of rolled steel were produced by a vertical bend-type continuous casting machine under the condition that the slab size was 245 mm thickness ⁇ 1200 to 1600 mm width, the casting speed was 1.4 to 1.7 m/min, and the temperature of molten steel in the tundish was 1560°C. After that, the slabs were hot-rolled, and then the pieces of hot-rolled steel were subjected to acid pickling, cold rolling, annealing and secondary cold rolling when necessary. In this way, products shown in Tables 4, 7 and 10 were produced.
  • Deoxidizing alloy used in the production process and the principal components contained in the crystallized phase of oxide inclusions are shown in Tables 5, 8, 11 and 12.
  • the hardness of oxide inclusions, the existing formation and the ratio of occurrence of defects are shown in Tables 6, 9 and 13. It can be seen from these tables that the present invention can greatly reduce the defects of products caused by oxide inclusions so that the productivity can be enhanced.
  • the components of the crystallized phases of inclusions shown in Tables 5, 8 and 12 were identified in such a manner that the inclusions extracted from pieces of rolled steel of full thickness, the weight of which was 1 ⁇ 0.1 kg, by means of slime electrolytic extraction (the minimum mesh was 38 ⁇ m) were identified by SEM having EDX. Further, concerning the detected additional component, the content was found from the integral intensity of the peak of the characteristic X-rays.
  • the full thickness of a section parallel to the rolling direction was observed by an optical microscope, and the existing inclusion formation was determined by an optical microscopic photograph (the magnification was 400 and the total number of field of view was 50) which was taken at a position where the inclusion exists.
  • the full thickness of a section parallel to the drawing direction was observed by an optical microscope, and the existing inclusion formation was determined by an optical microscopic photograph (the magnification was 400 and the total number of field of view was 50) which was taken at a position where the inclusion exists.
  • the present invention provides rolled steel having few inclusion defects in which fine particles of oxide inclusions are dispersed.
  • the present invention to contribute to the development of industry by providing rolled steel having few inclusion defects in which the conventional problems are completely solved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
EP00102280A 1999-02-18 2000-02-17 Acier laminé ayant peu de défauts d'inclusions Withdrawn EP1029938A3 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP03964799A JP3462779B2 (ja) 1999-02-18 1999-02-18 介在物性欠陥が少ない圧延鋼材
JP3964799 1999-02-18
JP10980599 1999-04-16
JP10980599A JP3462790B2 (ja) 1999-04-16 1999-04-16 介在物性欠陥が少ない圧延鋼材

Publications (2)

Publication Number Publication Date
EP1029938A2 true EP1029938A2 (fr) 2000-08-23
EP1029938A3 EP1029938A3 (fr) 2003-10-15

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2853668A3 (fr) * 2003-04-08 2004-10-15 Usinor Tole fine en acier bas carbone et tres bas aluminium, notamment pour emballage, et son procede d'obtention
EP1669471A1 (fr) * 2004-12-09 2006-06-14 Kabushiki Kaisha Kobe Seiko Sho Tôle d'acier à haute ductilité et procédé de fabrication correspondant
DE10314476B4 (de) * 2002-04-29 2006-07-27 Salzgitter Mannesmann Gmbh Verfahren zur Herstellung eines Al-beruhigten Stahles
US7776162B2 (en) * 2002-07-23 2010-08-17 Nippon Steel Corporation Steels with few alumina clusters
CN105583235A (zh) * 2015-12-28 2016-05-18 钢铁研究总院 热轧钢筋的分段阶梯型冷却控制氧化铁皮结构的方法
EP3221485A1 (fr) * 2014-11-18 2017-09-27 L'Air Liquide Société Anonyme pour l'Etude et l'Exploitation des Procédés Georges Claude Matériaux de construction destinés à être utilisés pour le stockage d'hydrogène haute pression dans une caverne de sel

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05117804A (ja) * 1991-10-24 1993-05-14 Kobe Steel Ltd 加工性および転動疲労性に優れた軸受用鋼
JPH06293936A (ja) * 1993-04-06 1994-10-21 Nippon Steel Corp Ｔｉ−Ａｌ複合系酸化物が分散した溶接部の靭性に優れた溶接低温用鋼の製造方法
JPH0924448A (ja) * 1995-07-12 1997-01-28 Nippon Steel Corp 溶接熱影響部の靱性に優れた鋼板の製造方法
EP0785283A1 (fr) * 1996-01-19 1997-07-23 Kawasaki Steel Corporation Procédé de production d'un acier à pourcentage ultra-bas de carbon
JPH10152755A (ja) * 1996-11-25 1998-06-09 Nippon Steel Corp 欠陥の少ない缶用鋼板用鋼材および製造方法
JPH10176213A (ja) * 1996-12-18 1998-06-30 Kawasaki Steel Corp 低炭素鋼の脱酸方法
JPH10226843A (ja) * 1997-02-19 1998-08-25 Nippon Steel Corp 欠陥が少なくプレス成形性に優れた薄鋼板およびその製造方法
EP0906960A1 (fr) * 1997-09-29 1999-04-07 Kawasaki Steel Corporation Acier calmé par la titane et procédé pour sa fabrication
JPH11264052A (ja) * 1998-03-18 1999-09-28 Nippon Steel Corp 欠陥が少なく面内異方性の小さい缶用鋼板およびその製造方法

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05117804A (ja) * 1991-10-24 1993-05-14 Kobe Steel Ltd 加工性および転動疲労性に優れた軸受用鋼
JPH06293936A (ja) * 1993-04-06 1994-10-21 Nippon Steel Corp Ｔｉ−Ａｌ複合系酸化物が分散した溶接部の靭性に優れた溶接低温用鋼の製造方法
JPH0924448A (ja) * 1995-07-12 1997-01-28 Nippon Steel Corp 溶接熱影響部の靱性に優れた鋼板の製造方法
EP0785283A1 (fr) * 1996-01-19 1997-07-23 Kawasaki Steel Corporation Procédé de production d'un acier à pourcentage ultra-bas de carbon
JPH10152755A (ja) * 1996-11-25 1998-06-09 Nippon Steel Corp 欠陥の少ない缶用鋼板用鋼材および製造方法
JPH10176213A (ja) * 1996-12-18 1998-06-30 Kawasaki Steel Corp 低炭素鋼の脱酸方法
JPH10226843A (ja) * 1997-02-19 1998-08-25 Nippon Steel Corp 欠陥が少なくプレス成形性に優れた薄鋼板およびその製造方法
EP0906960A1 (fr) * 1997-09-29 1999-04-07 Kawasaki Steel Corporation Acier calmé par la titane et procédé pour sa fabrication
JPH11264052A (ja) * 1998-03-18 1999-09-28 Nippon Steel Corp 欠陥が少なく面内異方性の小さい缶用鋼板およびその製造方法

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* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 017, no. 478 (C-1104), 31 August 1993 (1993-08-31) -& JP 05 117804 A (KOBE STEEL LTD), 14 May 1993 (1993-05-14) *
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 01, 28 February 1995 (1995-02-28) -& JP 06 293936 A (NIPPON STEEL CORP), 21 October 1994 (1994-10-21) *
PATENT ABSTRACTS OF JAPAN vol. 1997, no. 05, 30 May 1997 (1997-05-30) -& JP 09 024448 A (NIPPON STEEL CORP), 28 January 1997 (1997-01-28) *
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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10314476B4 (de) * 2002-04-29 2006-07-27 Salzgitter Mannesmann Gmbh Verfahren zur Herstellung eines Al-beruhigten Stahles
US7776162B2 (en) * 2002-07-23 2010-08-17 Nippon Steel Corporation Steels with few alumina clusters
FR2853668A3 (fr) * 2003-04-08 2004-10-15 Usinor Tole fine en acier bas carbone et tres bas aluminium, notamment pour emballage, et son procede d'obtention
EP1669471A1 (fr) * 2004-12-09 2006-06-14 Kabushiki Kaisha Kobe Seiko Sho Tôle d'acier à haute ductilité et procédé de fabrication correspondant
EP3221485A1 (fr) * 2014-11-18 2017-09-27 L'Air Liquide Société Anonyme pour l'Etude et l'Exploitation des Procédés Georges Claude Matériaux de construction destinés à être utilisés pour le stockage d'hydrogène haute pression dans une caverne de sel
CN105583235A (zh) * 2015-12-28 2016-05-18 钢铁研究总院 热轧钢筋的分段阶梯型冷却控制氧化铁皮结构的方法
CN105583235B (zh) * 2015-12-28 2017-06-23 钢铁研究总院 热轧钢筋的分段阶梯型冷却控制氧化铁皮结构的方法

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