EP1637241B1 - Verfahren zur herstellung eines nahtlosen rohres aus einer fe- cr- legierung - Google Patents

Verfahren zur herstellung eines nahtlosen rohres aus einer fe- cr- legierung Download PDF

Info

Publication number
EP1637241B1
EP1637241B1 EP04734124A EP04734124A EP1637241B1 EP 1637241 B1 EP1637241 B1 EP 1637241B1 EP 04734124 A EP04734124 A EP 04734124A EP 04734124 A EP04734124 A EP 04734124A EP 1637241 B1 EP1637241 B1 EP 1637241B1
Authority
EP
European Patent Office
Prior art keywords
scale
billet
steel ingot
blooming
reduction rate
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.)
Expired - Fee Related
Application number
EP04734124A
Other languages
English (en)
French (fr)
Other versions
EP1637241A1 (de
EP1637241A4 (de
Inventor
Yasuyoshi Hidaka
Toshiro Anraku
Tomio Yamakawa
Yasufumi Kitamura
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
Sumitomo Metal Industries Ltd
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 Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Publication of EP1637241A1 publication Critical patent/EP1637241A1/de
Publication of EP1637241A4 publication Critical patent/EP1637241A4/de
Application granted granted Critical
Publication of EP1637241B1 publication Critical patent/EP1637241B1/de
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

Links

Images

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/026—Rolling
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B2001/022—Blooms or billets
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B9/00—Measures for carrying out rolling operations under special conditions, e.g. in vacuum or inert atmosphere to prevent oxidation of work; Special measures for removing fumes from rolling mills

Definitions

  • the present invention relates to a method of manufacturing a seamless steel pipe using an iron base alloy (in the specification simply referred to as "Fe-Cr alloy”) billet containing Cr in the range of 5 to 17 %, in more detail, a method that can largely reduce the surface treatment of a billet before manufacturing of seamless steel pipes by blooming.
  • Fe-Cr alloy iron base alloy
  • Such surface defects are caused owing to scale defects on a billet surface prior to tube-making. That is, owing to descaling failure in a manufacturing process of a billet, scales are left without being removed, the scales are squeezed in or rolled together to be the scale defects, and when the billet is subjected to tube-making with the scale defects remained thereon, the surface defects are caused.
  • a billet used for manufacturing the Fe-Cr alloy seamless steel pipe is, as shown in Figs. 1 and 2 that are described later, manufactured by blooming a steel ingot made of the same alloy.
  • the steel ingot after being heated to substantially 1200 °C, is processed by the blooming by means of a box type or grooved roll. At that time, with a multi-stage roll, while gradually reducing it and making a diameter of the material smaller, the steel ingot is finished into a billet shape.
  • Japanese Patent Application Publication No. 07-258740 proposes, a continuous heating method characterized in that when the steel ingot such as a slab or billet is continuously heated with a combustion burner, the generation of oxidation scale is suppressed during heating, the steel ingot after the heating is oxidized to generate scales excellent in peelability, and thereby surface defects are removed.
  • a large-scale improvement and remodeling of a continuous heating furnace become necessary.
  • Japanese Patent Application Publication No. 10-277912 proposes a method of treating surface flaws characterized in that after marking on a steel ingot, image data thereof is collected, and from the image data, surface flaw data is extracted.
  • a lot of equipment and expenses are necessary; accordingly, it is not suitable for a method of treating the billet.
  • JP08-174034 discusses a method of manufacturing stainless steel sheet wherein the surface of the slab is shot with blasting material through the blasting treatment and part of the blasting material is left therein before the ferritic stainless steel slab is charged in a slab heating furnace in order to easily form a uniform and thick scale during the slab heating. Hot rolling is carried out thereafter.
  • JP11-342404 relates to a method of hot rolling a stainless steel ingot wherein before heating in a heating furnace, one or two compounds selected from calcium compounds and barium compounds and an agent which adheres the compound to the stainless steel surface are applied.
  • JP07-178420 relates to a method of hot rolling stainless steel slabs which involves soaking and holding the steel slabs in a temperature range of 1000 to 100°C for one to three hours, and then holding the slabs in a temperature range of from 150 to 1520°C, for two or more hours prior to hot rolling in order to reduce scale flaws generated during the hot rolling process.
  • JP07-204703 relates to a method for generating thin oxide scale of 1 to 7 micron in thickness prior to passing the steel through the finish stands in the temperature range of 950°C or less.
  • Fig. 2 is a diagram of one example for explaining in detail situations of change in a shape of the cross section of the steel ingot in the blooming process in the manufacture of the billet.
  • the cross section of the steel ingot 1 is gradually reduced and finally finished to a billet 2 after rolling ten passes.
  • the steel ingot 1 before the blooming is placed so as being laid on the shorter side (corresponding to Fig. 1(a) ), and processed so as to be the steel ingot 1 having a rectangular cross section after the rolling of a seven pass at the first stand (corresponding to Fig. 1(b) ).
  • the steel ingot having the rectangular cross section is subjected to the eighth through tenth rolling at the second stand and finished into the final billet 2 (corresponding to Fig. 1(c) ).
  • the first, second, fourth, sixth, eighth and tenth passes show the rolling in the vertical reduction direction
  • the third, fifth, seventh and ninth passes show the rolling in the horizontal reduction direction.
  • the steel ingot is rotated 90° to change a rolling reduction direction.
  • the steel ingot 1 shown in Fig. 1(a) is divided into a high reduction rate surface 3 and a low reduction rate surface 4, the high reduction rate surface 3 showing a surface that becomes higher in the reduction rate in the blooming, the low reduction rate surface 4 showing other surface thereof.
  • the steel ingot before the blooming is disposed in the longitudinal direction; accordingly, the high reduction rate surface 3 becomes a surface of shorter side in the slab-shaped steel ingot, the low reduction rate surface 4 becoming a surface of longer side.
  • a cross section of the billet 2 after the blooming shown in Fig. 1(c) is equally divided into four portions of two high reduction rate surfaces 3' (portion reduced with high reduction rate of the steel ingot 1) and two low reduction rate surfaces 4' (portion reduced with low reduction rate of the steel ingot 1) and a central angle ⁇ (an angle occupying in a surface portion of the billet 2) of the high reduction rate surface 3' shown in the same drawing becomes 90°.
  • Fig. 3 is a perspective view showing an entire configuration of the billet after the blooming.
  • a center portion of the low reduction rate surface 4 is not directly restrained by a reduction roll, or, even when restrained, is only slightly restrained compared to other portions. Accordingly, in the billet 2 after the blooming, as shown in Fig. 3 , wrinkles 5 are generated in the longitudinal direction of the billet.
  • the box type roll As the grooved roll that is used in the blooming, a box type roll, a diamond type roll or an oval type roll can be illustrated.
  • the box type roll is effective in preventing the steel ingot from inclining/falling. Accordingly, in view of the stability of the blooming, the box type roll is adopted in many cases.
  • the high reduction rate surface 3' can be specified in a range of a central angle of ⁇ 45° ( ⁇ /2) with a surface h that is orthogonal to the wrinkles 5 as a center of the billet 2.
  • the present invention was achieved based on the above findings and a method of manufacturing a seamless pipe using an Fe-Cr alloy billet according to (1) through (3) below are the gist of the invention.
  • the "Fe-Cr alloy” means an iron base alloy containing 5 to 17 % of Cr and, whereby necessary, other alloy elements such as Ni and Mo may be contained.
  • the "high reduction rate surface” means, in the steel ingot, a surface where when the blooming is applied to form into a billet shape, the reduction rate becomes higher, and, in the billet, a portion that was the high reduction rate surface in the steel ingot before the rolling. Normally, in the steel ingot having a slab shape, the high reduction rate surface becomes a shorter side surface.
  • the "high reduction rate surface" in the billet can be specified in a range where a central angle is ⁇ 45° ( ⁇ /2) with a central surface orthogonal to the wrinkles with respect to a center of the billet.
  • results of macro-observation of a cross section of the billet can be used.
  • Fig. 4 is a diagram showing one example of observation results of macro-photographs of the billet cross section.
  • segregation correlated with a direction of the cross section of the steel ingot before the blooming can be observed. That is, since a position where the segregation occurs coincides with a final solidifying position of the steel ingot the final solidifying position depends on a shape of cross section made of a longer side surface 4 and a shorter side surface 3 of the steel ingot.
  • the area ratios of the high reduction rate surface and the low reduction rate surface on an external surface of the billet after the manufacture become almost the same, and the cross section of the billet is equally divided into four portions of two high reduction rate surfaces and two low reduction surfaces. Accordingly, a value of an "area rate of the high reduction rate surface" (a ratio of area of scales in the high reduction rate surface) stipulated according to the invention, when multiplied by 1/2, can be replaced by a “total area rate (of billet)" (a ratio of area of scales in an entire area of the billet).
  • the external layer scale is made of Fe 2 O 3 , Fe 3 O 4 and FeO and the internal layer scale is made of FeCr 2 O 4 and FeO.
  • the external layer scale is made of Fe 2 O 3 and Fe 3 O 4 and the internal layer scale is made of FeCr 2 O 4 and Fe 3 O 4 .
  • Test materials were 5 to 17 % Cr-containing alloys A, B and C, and as a steel ingot starting material, a bloom CC material having a short side of 280 mm x long side of 600 mm x length of 7400 mm was used.
  • the steel ingot was subjected to heating at 1200 °C for 6 hr in an atmospheric heating furnace (not containing steam).
  • the manufacture was carried out under two conditions, that is, in one, descaling was applied with a high-pressure water descaler having a pressure of 100 kg/cm 2 and in the other, descaling was not applied.
  • the blooming of the steel ingot was performed at the first and second stand respectively by reverse rolling.
  • the first pass of the rolling at the first stand was differentiated by whether the high reduction rate surface was reduced or the low reduction rate surface was reduced.
  • the steel ingot was reduced to a cross sectional shape of substantially short side of 250 mm ⁇ long side of 400 mm, followed by finishing, at the second stand, into a billet of a final size of a diameter of 225 ⁇ .
  • flaw detection was performed by use of an NDI flaw detector due to magnetic leakage flux flaw detecting method.
  • flaws having a depth of 0.5 mm or more were detected.
  • the flaw having a depth of 0.5 mm or more when subjected to rolling and tubing as it is without treating, becomes a flaw on a surface of a steel tube; accordingly, it is necessary to treat a surface.
  • a criterion was not determined on a length of defect. However, in consideration of being stretched to a final product, a defect having a small length such as several tens millimeters was checked.
  • the rate of incidence of defects was evaluated in terms of number ratio (number of generated defects/total number).
  • an area rate with which the scale covers a surface of the billet was investigated.
  • the area rate of the scale was measured in such a manner that a cross section observation sample was sampled from the high reduction rate surface of the billet for each 1 m, a length of peeled scale was observed by micro-observation, and ⁇ (average length of peeled scale in a vertical direction ⁇ average length of peeled scale in a horizontal direction) / total area ⁇ was calculated as an area rate.
  • the area rate of the scale an average value of the area rates of all samples in the respective billets was used.
  • Tables 3 through 5 The frequencies of incidence of defects and the area rates of scales that cover the high reduction rate surface of the billet at this time are shown in Tables 3 through 5.
  • Table 3 shows results of 5 % Cr-containing alloy A was used as a test sample;
  • Table 4 shows results of 13 % Cr-containing alloy B was used as a test sample; and
  • Table 5 shows results of 17 % Cr-containing alloy C was used as a test sample.
  • Example 1 in each case where any of the test samples was used, thicknesses of scales formed on steel ingots immediately after taking out of a heating furnace were substantially 1000 ⁇ m, and the scale structure was made of an external layer scale of Fe 2 O 3 and Fe 3 O 4 and an internal layer scale of FeCr 2 O 4 and Fe 3 O 4 . Furthermore, thicknesses of scales covering surfaces of the billets immediately after the manufacture were 150 ⁇ m or more. Table 3 Test No.
  • the scale coverage was in the range of 45 to 50 % by the area rate of the high reduction rate surface (22.5 to 25 % in terms of the total area), the rate of incidence of defects was nearly the total number, and with the number rate of 92 to 98 % surface treatment was necessary
  • the scale coverage of the high reduction rate surface was such high as in the range of 70 to 73 % by the area rate of the high reduction rate surface (35 to 36.5 % in terms of the total area), the rate of incidence of defects were dropped as much as 44 to 47 %. That is, one half that of the comparative examples.
  • Table 6 shows results when 5 % Cr-containing alloy A was used as a test sample
  • Table 7 shows results when 13 % Cr-containing alloy B was used as a test sample
  • Table 8 shows results when 17 % Cr-containing alloy A was used as a test sample.
  • a thickness of the scale that covers the surface of the billet was 150 ⁇ m or more.
  • the pipes can be manufactured at low manufacturing costs and efficiently, and the method can be widely applied in the field of manufacturing hot seamless steel pipes.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Extraction Processes (AREA)
  • Forging (AREA)

Claims (4)

  1. Verfahren zum Herstellen eines nahtlosen Stahlrohrs, welches das Unterziehen eines Stahlrohblocks (1) einem Vorblocken, um einen Knüppel (2) aus Fe-Cr-Legierung herzustellen, wobei der Rohblock vor dem Vorblocken erwärmt wird, um auf dessen Oberfläche einen Zunder zu erzeugen, und wobei das Vorblocken ohne Durchführen von Entzundern des Stahlrohblocks durchgeführt wird, und Herstellen des nahtlosen Stahlrohrs aus dem Knüppel (2) aus Fe-Cr-Legierung umfasst.
  2. Verfahren nach Anspruch 1, wobei ein Zunder mit einer Dicke von 1000 µm oder mehr auf dem Stahlrohblock erzeugt wird.
  3. Verfahren nach Anspruch 2, wobei eine Oberfläche (3) hoher Reduktionsrate des Stahlrohblocks zuerst reduziert wird.
  4. Verfahren nach Anspruch 2 oder 3, wobei der Stahlrohblock 2 Stunden oder länger in einer nach Volumenprozent 2,5% oder mehr Dampf enthaltenden Atmosphäre bei einer Erwärmungstemperatur von 1200 °C oder mehr gehalten wird, um den Zunder zu erzeugen.
EP04734124A 2003-05-22 2004-05-20 Verfahren zur herstellung eines nahtlosen rohres aus einer fe- cr- legierung Expired - Fee Related EP1637241B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2003144557 2003-05-22
PCT/JP2004/007223 WO2004103589A1 (ja) 2003-05-22 2004-05-20 Ｆｅ－Ｃｒ合金ビレットおよびその製造方法

Publications (3)

Publication Number Publication Date
EP1637241A1 EP1637241A1 (de) 2006-03-22
EP1637241A4 EP1637241A4 (de) 2007-03-28
EP1637241B1 true EP1637241B1 (de) 2012-09-12

Family

ID=33475208

Family Applications (1)

Application Number Title Priority Date Filing Date
EP04734124A Expired - Fee Related EP1637241B1 (de) 2003-05-22 2004-05-20 Verfahren zur herstellung eines nahtlosen rohres aus einer fe- cr- legierung

Country Status (9)

Country Link
EP (1) EP1637241B1 (de)
JP (1) JP4265603B2 (de)
CN (1) CN100417460C (de)
BR (1) BRPI0410554B1 (de)
CA (1) CA2525147C (de)
MX (1) MXPA05012509A (de)
RU (1) RU2313409C2 (de)
WO (1) WO2004103589A1 (de)
ZA (1) ZA200510009B (de)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5320084B2 (ja) * 2008-04-16 2013-10-23 株式会社神戸製鋼所 デスケーリング性のよい高Ｃｒ含有鋼材の製法
CN101856669B (zh) * 2010-06-02 2012-01-04 东北大学 热轧带钢表面氧化铁皮柔性化控制方法
JP5423641B2 (ja) * 2010-10-13 2014-02-19 新日鐵住金株式会社 高純度フェライト系ステンレス鋼の分塊圧延方法
JP6314785B2 (ja) * 2014-10-14 2018-04-25 新日鐵住金株式会社 分塊圧延方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2720693B2 (ja) * 1992-02-19 1998-03-04 住友金属工業株式会社 オーステナイト系ステンレス鋼連続鋳造鋳片の分塊圧延法
JPH06100931A (ja) * 1992-09-17 1994-04-12 Kawasaki Steel Corp マルテンサイト系ステンレス継目無管製造用丸ビレットの製造方法
JPH06306455A (ja) * 1993-04-26 1994-11-01 Nippon Steel Corp 表面疵の少ないフェライト系ステンレス鋼の製造方法
JP2738281B2 (ja) * 1993-12-22 1998-04-08 日本鋼管株式会社 ステンレス鋼スラブの熱間圧延方法
JPH07204703A (ja) * 1994-01-21 1995-08-08 Sumitomo Metal Ind Ltd ステンレス熱延鋼板の製造方法
JPH08174034A (ja) * 1994-12-21 1996-07-09 Nippon Steel Corp Ｃｒ系ステンレス鋼板の製造方法
JPH10277912A (ja) 1997-04-04 1998-10-20 Nippon Steel Corp 鋼片の表面疵処理方法
JP3552579B2 (ja) * 1998-03-31 2004-08-11 Ｊｆｅスチール株式会社 ステンレス鋼片の熱間圧延方法および熱間圧延前のステンレス鋼片塗布用薬剤

Also Published As

Publication number Publication date
CA2525147C (en) 2009-08-18
BRPI0410554B1 (pt) 2014-04-08
RU2313409C2 (ru) 2007-12-27
JP4265603B2 (ja) 2009-05-20
CN1791477A (zh) 2006-06-21
BRPI0410554A (pt) 2006-06-20
EP1637241A1 (de) 2006-03-22
RU2005140109A (ru) 2007-07-10
JPWO2004103589A1 (ja) 2006-07-20
EP1637241A4 (de) 2007-03-28
CA2525147A1 (en) 2004-12-02
CN100417460C (zh) 2008-09-10
MXPA05012509A (es) 2006-02-08
ZA200510009B (en) 2006-12-27
WO2004103589A1 (ja) 2004-12-02

Similar Documents

Publication Publication Date Title
EP1637241B1 (de) Verfahren zur herstellung eines nahtlosen rohres aus einer fe- cr- legierung
EP1683884B1 (de) Rohr aus nichtrostendem martensitischem stahl und herstellungsverfahren dafür
EP2025421B1 (de) Verfahren zur herstellung eines nahtlosen rohrs aus rostfreiem stahl
EP4282990A1 (de) Duplexedelstahlrohr und verfahren zur herstellung davon
CN110461487B (zh) 黑皮热轧钢板及其制造方法
JP2008068307A (ja) 条鋼材の熱間圧延方法
JP2003171739A (ja) 酸洗性に優れた鋼材及びその製造方法
JP4316034B2 (ja) ステンレス鋼板の表面処理方法
JP4314884B2 (ja) 熱間継目無管圧延用マンドレルバー
JP3425017B2 (ja) 熱延鋼板の製造方法
JP3303344B2 (ja) 表面疵の少ないチタンまたはチタン合金の冷間圧延板の製造方法
JP2009046731A (ja) スケール剥離性に優れたＳｉ、Ｃｒ含有条鋼材の製造方法
JP3245806B2 (ja) フェライト系ステンレス鋼の製造方法
JP2020163402A (ja) フェライト系ステンレス薄板の製造方法およびフェライト系ステンレス薄板
JPH05228526A (ja) 表面性状の優れた鋼板の製造方法
JP7111092B2 (ja) 継目無鋼管圧延用プラグ、継目無鋼管圧延用プラグの製造方法、継目無鋼管圧延用プラグミル、継目無鋼管の圧延方法および継目無鋼管の製造方法
JP2001123249A (ja) マルテンサイト系ステンレス鋼材
EP4321632A1 (de) Hochfestes warmgewalztes stahlblech und herstellungsverfahren dafür sowie hochfestes widerstandsgeschweisstes stahlrohr und herstellungsverfahren dafür
JP2007118028A (ja) 鋼材のメカニカルデスケーリング方法
JP2672392B2 (ja) 薄スケール熱延鋼板の製造方法
JP3226723B2 (ja) メカニカルデスケーリング性に優れた線材
JPH05271781A (ja) 冷間圧延用ステンレス予備処理鋼帯の製造方法及び装置
JP2944874B2 (ja) 圧延疵の発生を低減したｓｕｓ４２０系シームレス鋼管の圧延方法
JP2000343107A (ja) 高合金継目無鋼管の製造方法
JPH05311243A (ja) 冷間圧延用ステンレス予備処理鋼帯の製造方法及び装置

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20051206

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): DE FR GB IT

DAX Request for extension of the european patent (deleted)
RBV Designated contracting states (corrected)

Designated state(s): DE FR GB IT

A4 Supplementary search report drawn up and despatched

Effective date: 20070226

RIC1 Information provided on ipc code assigned before grant

Ipc: B21B 1/02 20060101AFI20041209BHEP

Ipc: C22C 38/18 20060101ALI20070220BHEP

Ipc: C22C 38/00 20060101ALI20070220BHEP

17Q First examination report despatched

Effective date: 20090130

RTI1 Title (correction)

Free format text: METHOD OF MANUFACTURING A SEAMLESS STEEL PIPE USING AN FE- CR- ALLOY

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RIN1 Information on inventor provided before grant (corrected)

Inventor name: KITAMURA, YASUFUMI

Inventor name: YAMAKAWA, TOMIO

Inventor name: ANRAKU, TOSHIRO

Inventor name: HIDAKA, YASUYOSHI

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE FR GB IT

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602004039295

Country of ref document: DE

Effective date: 20121108

RAP2 Party data changed (patent owner data changed or rights of a patent transferred)

Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20130613

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602004039295

Country of ref document: DE

Effective date: 20130613

REG Reference to a national code

Ref country code: GB

Ref legal event code: 732E

Free format text: REGISTERED BETWEEN 20131010 AND 20131016

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602004039295

Country of ref document: DE

Representative=s name: RECHTS- UND PATENTANWAELTE LORENZ SEIDLER GOSS, DE

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602004039295

Country of ref document: DE

Representative=s name: LORENZ SEIDLER GOSSEL RECHTSANWAELTE PATENTANW, DE

Effective date: 20140402

Ref country code: DE

Ref legal event code: R082

Ref document number: 602004039295

Country of ref document: DE

Representative=s name: RECHTS- UND PATENTANWAELTE LORENZ SEIDLER GOSS, DE

Effective date: 20140402

Ref country code: DE

Ref legal event code: R081

Ref document number: 602004039295

Country of ref document: DE

Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION, JP

Free format text: FORMER OWNER: SUMITOMO METAL INDUSTRIES, LTD., OSAKA, JP

Effective date: 20140402

Ref country code: DE

Ref legal event code: R081

Ref document number: 602004039295

Country of ref document: DE

Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION, JP

Free format text: FORMER OWNER: SUMITOMO METAL INDUSTRIES, LTD., OSAKA, JP

Effective date: 20120912

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 13

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 14

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 15

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602004039295

Country of ref document: DE

Representative=s name: LORENZ SEIDLER GOSSEL RECHTSANWAELTE PATENTANW, DE

Ref country code: DE

Ref legal event code: R081

Ref document number: 602004039295

Country of ref document: DE

Owner name: NIPPON STEEL CORP., JP

Free format text: FORMER OWNER: NIPPON STEEL & SUMITOMO METAL CORPORATION, TOKYO, JP

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20200506

Year of fee payment: 17

Ref country code: FR

Payment date: 20200414

Year of fee payment: 17

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20200414

Year of fee payment: 17

Ref country code: GB

Payment date: 20200513

Year of fee payment: 17

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602004039295

Country of ref document: DE

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210520

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210520

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210531

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200520