EP0225263B1 - Blech oder Band aus ferritischem rostfreien Stahl, insbesondere für Auspuffsysteme - Google Patents

Blech oder Band aus ferritischem rostfreien Stahl, insbesondere für Auspuffsysteme Download PDF

Info

Publication number
EP0225263B1
EP0225263B1 EP86420267A EP86420267A EP0225263B1 EP 0225263 B1 EP0225263 B1 EP 0225263B1 EP 86420267 A EP86420267 A EP 86420267A EP 86420267 A EP86420267 A EP 86420267A EP 0225263 B1 EP0225263 B1 EP 0225263B1
Authority
EP
European Patent Office
Prior art keywords
strip
sheet
resistance
oxidation
test
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
Application number
EP86420267A
Other languages
English (en)
French (fr)
Other versions
EP0225263A1 (de
Inventor
Pascal Gressin
Philippe Maitrepierre
Jean Decroix
Pierre Pedarre
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.)
Ugine Aciers de Chatillon et Guegnon
Original Assignee
Ugine Aciers de Chatillon et Guegnon
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 Ugine Aciers de Chatillon et Guegnon filed Critical Ugine Aciers de Chatillon et Guegnon
Priority to AT86420267T priority Critical patent/ATE42770T1/de
Publication of EP0225263A1 publication Critical patent/EP0225263A1/de
Application granted granted Critical
Publication of EP0225263B1 publication Critical patent/EP0225263B1/de
Expired legal-status Critical Current

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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium

Definitions

  • the invention relates to the field of rolled products of stainless ferritic steel, and more particularly that of exhaust systems.
  • the Applicant has tried to improve the properties compromises obtained with sheets or strips of shades already known and more particularly with stainless ferritic grades stabilized with Nb and / or Zr, and this especially with regard to the creep resistance and to hot oxidation.
  • Ferritic stainless grades are superior to austenitic grades because of their coefficient of thermal expansion.
  • Patent application FR-A-2 463194 relates to ferritic steels with 1 to 20% Cr and Ti, Nb with 0.5 to 2% AI, in which a minimum AI content of 0.5% and preferably 0.75% is required to provide resistance to oxidation at elevated temperatures. Above 2%, AI has a detrimental effect on the weldability.
  • a ferritic stainless steel contains 0.08 to 0.5% AI and one or more of the elements B (2-50 ppm), Ti (0.005-0.4%), Nb (0.005-0.4%), V (0.005-0.4%) and Zr (0.005-0.4%), and AI results in structural changes at the various stages of sheet metal transformation with an increase in “ridging resistance” (resistance to the phenomenon of stringing or crumpling).
  • Zrest consumed by stabilization that is to say by trapping C and N in the form of nitrides and carbides, up to approximately 7 (C + N)%.
  • the free Zr is therefore limited to 0.2%, which makes it possible to avoid the drawbacks linked to the formation of eutectic compounds containing Fe 3 Zr in the case where there is more than 0.25% of free Zr, these compounds resulting in a degradation of the mechanical characteristics, in particular of the ductility and of the creep resistance, and a reduction in the corrosion resistance, as indicated essentially by document US-A-4010049.
  • the free Zr has no significant direct influence on the resistance to oxidation.
  • the free or non-combined Nb is between 0.25 and 0.55%.
  • the Nbtotal includes in addition to the free Nb an addition of 7 (C + N) -Zr, to compensate for the lack of stabilization by insufficient Zr, in the case where Zr is between 7 (C + N) - 0.1 and 7 (C + N).
  • the total content of AI assayed corresponds essentially to AI in solid solution.
  • Zr has more affinity than AI for oxygen and there is little residual oxygen in the metal, so that there can be only very little AI in the form of alumina.
  • the affinities of Zr and Nb for nitrogen and the greater affinity of AI for oxygen than for nitrogen means that aluminum nitride AIN does not form.
  • the result confirmed qualitatively by micrographic examinations, is that AI is in solid solution with the exception of a content at most equal to 0.003% and corresponding essentially to alumina.
  • 0.020 to 0.080% AI a surprising improvement in resistance to hot oxidation is obtained, linked to the role of aluminum in solid solution, whether it is continuous oxidation.
  • the AI content is limited to 0.080% so as to avoid, as has been the experience with 17% Cr stainless steels (type AISI 430), dross on the weld beads causing irregular oxidation and cracking conformation, therefore faster corrosion.
  • This dross effect is significant at the 0.1% AI level; but if one also wants to avoid or limit the inclusions of alumina linked to the presence of too much aluminum, these inclusions being sites of initiation of stings following the projections of salt water coming from salting or desalination of roads during winter, it is advisable to remain below 0.05% of AI as it is done in the preferential composition indicated below.
  • AI 0.020 to 0.045 and more preferably 0.025 to 0.040.
  • the sheet or strip according to the invention is in the annealed and optionally erected state, this annealed state typically corresponding to a treatment at 1000 ⁇ 10 ° C for 0.5 to 5 min.
  • the invention also relates to the method of manufacturing a sheet or strip of ferritic stainless steel, in which, as is known, the hot rolled strip is annealed with a thickness of between 2.5 and 5 mm between 800 and 1000 ° C. under slightly oxidizing conditions, then it is shot and pickled, then it is cold rolled to the delivery thickness typically between 0.6 and 3 mm, with or without annealing and intermediate pickling, and it is annealed at the end of the parade, then it is subjected to a finishing pass or so-called "skin-pass" hardening producing an elongation of less than 1%, with possibly a final stripping.
  • the hot rolled strip is annealed with a thickness of between 2.5 and 5 mm between 800 and 1000 ° C. under slightly oxidizing conditions, then it is shot and pickled, then it is cold rolled to the delivery thickness typically between 0.6 and 3 mm, with or without annealing and intermediate pickling, and it is annealed at the end of the parade, then
  • This process differs from the prior art in that the sheet or strip has the composition of the invention and in that the annealing, making it possible to obtain good hot creep results, is carried out between 980 and 1020 ° C. , and preferably between 990 and 1010 ° C for 0.5 to 5 min, or at a temperature and for a time giving an equivalent metallurgical state.
  • This final annealing is typically carried out following a rolling producing an elongation of at least 100% from the previous annealing.
  • Rectangular test specimens of 310 x 25 mm were cut from the sheets, and bent at 90 ° to 25 mm from one end. Then they were laid flat each on 2 supports of internal distance 254 mm and external distance 264 mm and they were subjected to continuous SAGTEST tests of creep under their own weight during 100 h at 850 ° C.
  • the sheets according to the invention with an uncombined Nb content of between 0.25 and 0.55%, and preferably with the intervals specified above, are thus indicated by their level of resistance to hot creep.
  • creep tests in tension at 800 ° C confirmed the SAGTEST tests.
  • the welds of the sheets according to the invention all exhibit very good ductility, unlike sheets with Nb + AI, and this even in the case of casting No. 445 where the Zr content is slightly less than 7 (C + N) .
  • the samples used come from 3 flows of 25 kg transformed according to the process indicated in connection with the test series N ° 1, the cold rolling being stopped at the thickness 1.5 mm and being followed by annealing under vacuum. from 1 h at 830 ° C.
  • the analyzes of the 3 castings, at 0.4% Nb and with increasing AI content, are shown in Table 7.
  • the samples are 20 x 30 mm plates cut out with a punch. in the annealed 1.5 mm sheets, then electrolytically polished in an aceto-perchloric bath (88-12) at room temperature for 5 min, then weighed in mg.
  • Each oxidation test relates to 3 test pieces of the same type, with an additional test piece for metallographic examinations.
  • the hot air oxidation tests have a unit duration of 50 h, the air renewal is ensured by "chimney effect" by means of a ⁇ 6 mm hole made in the lower part of the oven.
  • the oxides formed are removed by electrolytic pickling in a neutral medium, and it is the weight loss of the samples per unit area (in g / m 2 ) which makes it possible to assess "a contrario" the resistance to hot oxidation.
  • the results on the 3 test pieces of each test are well grouped in the case of continuous oxidation, and we have therefore given in this case only one result, average of the 3 individual results.
  • the AI contents are plotted on the graph in FIG. 4.
  • test pieces prepared as described above are subjected to cycles each comprising: rapid heating, holding for 10 min at the test temperature, then air cooling and maintaining at room temperature or close to total duration 10 min.
  • the duration of a test is 100 h during which 300 cycles are carried out giving an overall maintenance at the test temperature of 50 h.
  • test pieces from casting with Nb + Al No 101 and casting according to the invention N os 201 and 202, the analyzes of which appear in table 7.
  • the tests relate to both full-sheet test pieces and test pieces containing welds, the latter being carried out as indicated with regard to the series of tests No. 2, and the right side of these welds then occupying% of the width of the test pieces.
  • the sheets of the invention are therefore distinguished from sheets of Nb without Zr in that their welds without filler metal have better resistance to alternating or cyclic oxidation in this temperature range (850 to 950 ° C) important for exhaust manifolds.
  • the strips or sheets of the invention are used for any application in which an economic compromise of ductility (sheet metal and welds), heat resistance (creep, continuous or cyclic air oxidation) and resistance to corrosion.
  • Application to exhaust systems is particularly typical.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Catalysts (AREA)
  • Exhaust Gas Treatment By Means Of Catalyst (AREA)
  • Heat Treatment Of Steel (AREA)
  • Soft Magnetic Materials (AREA)
  • Treating Waste Gases (AREA)
  • Woven Fabrics (AREA)
  • Exhaust Silencers (AREA)

Claims (7)

1. Blech oder Band aus ferritischem rostfreiem Stahl, insbesondere für die Herstellung von Auspuffsystemen, gekennzeichnet durch folgende Zusammensetzung (in Gew.-%):
(C+N) < 0,060; Si < 0,9; Mn < 1;
Cr = 15 bis 19; Mo < 1; Ni < 0,5; Ti < 0,1; Cu < 0,4;
S < 0,02; P < 0,045; Zr = 0,10 bis 0,50 mit Zr von 7 (C+N) - 0,1 bis 7 (C+N) + 0,2; Nb = von 0,25 bis 0,55, wenn Zr ≥ 7 (C+N), und von 0,25 + 7 (C+N) - Zr bis 0,55 + 7 (C+N) - Zr, wenn Zr < 7 (C+N);
AI = 0,020 bis 0,080; Verunreinigungen und Fe: Rest, und das Vorliegen von AI als feste Lösung mit der Ausnahme eines Gehaltes von höchstens 0,003%.
2. Blech oder Band nach Anspruch 1, gekennzeichnet durch folgende Zusammensetzung (in Gew.-%) :
(C+N) < 0,040; Si < 0,8; Cr = 16 bis 18; Mo < 0,3; Ni < 0,3; Ti < 0,05;
S < 0,01; Zr = 0,10 bis 0,40 mit Zr von 7 (C+N) bis 7 (C+N) + 0,15;
Nb = 0,30 bis 0,52; AI = 0,020 bis 0,045.
3. Blech oder Band nach Anspruch 2, gekennzeichnet durch folgende Zusammensetzung (in Gew.-%) :
Nb = 0,33 bis 0,50 und
AI = 0,025 bis 0,040.
4. Blech oder Band nach einem der Ansprüche 1-3, dadurch gekennzeichnet, dass es 0,5 bis 5 min bei 1000 ± 10° Cgeglüht und dressiertwird.
5. Verfahren zur Herstellung eines Blechs oder Bands mit einer Zusammensetzung gemäss einem der Ansprüche 1-3, wobei das warmgewalzte Band mit einer Dicke von 2,5 bis 5 mm bei einer Temperatur von 800 bis 1000° C unter wenig oxydierenden Bedingungen geglüht, dann granuliert und abgebeizt wird, bis zu einer Lieferungsdicke von 0,6 bis 3 mm kaltgewalzt wird, mit gegebenenfalls dazwischengeschalteten Glühungen und Abbeizungen, im Vorbeilaufen endgeglüht und einer Endbearbeitung und einem Nachwalzen oder Dressierstich («skin-pass») unterworfen wird, wodurch eine Verlängerung unter 1 % entsteht, dadurch gekennzeichnet, dass das Endglühen bei einer Temperatur von 980 bis 1020° C durchgeführt wird.
6. Verfahren nach Anspruch 5, dadurch gekennzeichnet, dass das Endglühen bei einer Temperatur von 990 bis 1010° C während 0,5 bis 5 min durchgeführt wird.
EP86420267A 1985-11-05 1986-10-29 Blech oder Band aus ferritischem rostfreien Stahl, insbesondere für Auspuffsysteme Expired EP0225263B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT86420267T ATE42770T1 (de) 1985-11-05 1986-10-29 Blech oder band aus ferritischem rostfreien stahl, insbesondere fuer auspuffsysteme.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR8516781A FR2589482B1 (fr) 1985-11-05 1985-11-05 Tole ou bande en acier ferritique inoxydable, en particulier pour systemes d'echappement
FR8516781 1985-11-05

Publications (2)

Publication Number Publication Date
EP0225263A1 EP0225263A1 (de) 1987-06-10
EP0225263B1 true EP0225263B1 (de) 1989-05-03

Family

ID=9324764

Family Applications (1)

Application Number Title Priority Date Filing Date
EP86420267A Expired EP0225263B1 (de) 1985-11-05 1986-10-29 Blech oder Band aus ferritischem rostfreien Stahl, insbesondere für Auspuffsysteme

Country Status (14)

Country Link
US (1) US4726853A (de)
EP (1) EP0225263B1 (de)
JP (1) JPS62112757A (de)
AT (1) ATE42770T1 (de)
AU (1) AU585083B2 (de)
BR (1) BR8605431A (de)
CA (1) CA1285791C (de)
DE (1) DE3663150D1 (de)
DK (1) DK518886A (de)
ES (1) ES2008092B3 (de)
FR (1) FR2589482B1 (de)
NO (1) NO167307C (de)
PT (1) PT83679B (de)
ZA (1) ZA868359B (de)

Families Citing this family (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3706415A1 (de) * 1987-02-27 1988-09-08 Thyssen Edelstahlwerke Ag Halbfertigerzeugnis aus ferritischem stahl und seine verwendung
US4834808A (en) * 1987-09-08 1989-05-30 Allegheny Ludlum Corporation Producing a weldable, ferritic stainless steel strip
DE68919606T2 (de) * 1988-09-05 1995-04-06 Hitachi Metals Ltd Hitzebeständige Gussstähle.
US4942922A (en) * 1988-10-18 1990-07-24 Crucible Materials Corporation Welded corrosion-resistant ferritic stainless steel tubing having high resistance to hydrogen embrittlement and a cathodically protected heat exchanger containing the same
US5288343A (en) * 1989-03-17 1994-02-22 Kawasaki Steel Corporation Stainless steel sheet for exterior building constituent
CA2012417C (en) * 1989-03-17 1998-07-21 Noboru Kinoshita Stainless steel sheet for exterior building constituent and method of making the same
DE3911104C1 (de) * 1989-04-06 1990-11-29 Krupp Stahl Ag, 4630 Bochum, De
US5110544A (en) * 1989-11-29 1992-05-05 Nippon Steel Corporation Stainless steel exhibiting excellent anticorrosion property for use in engine exhaust systems
JPH0747799B2 (ja) * 1989-11-29 1995-05-24 新日本製鐵株式会社 耐食性の優れたエンジン排ガス系材料用ステンレス鋼
US5302214A (en) * 1990-03-24 1994-04-12 Nisshin Steel Co., Ltd. Heat resisting ferritic stainless steel excellent in low temperature toughness, weldability and heat resistance
JP2696584B2 (ja) * 1990-03-24 1998-01-14 日新製鋼株式会社 低温靭性，溶接性および耐熱性に優れたフエライト系耐熱用ステンレス鋼
JP2562740B2 (ja) * 1990-10-15 1996-12-11 日新製鋼株式会社 耐粒界腐食性，造管性および高温強度に優れたフエライト系ステンレス鋼
DE69330590T2 (de) * 1992-04-09 2002-06-13 Nippon Steel Corp., Tokio/Tokyo Ferritischer rostfreier stahl mit exzellentem hochtemperatur widerstand und hochtemperaturwiderstand gegen salzangriff
JPH06220545A (ja) * 1993-01-28 1994-08-09 Nippon Steel Corp 靱性の優れたＣｒ系ステンレス鋼薄帯の製造方法
DE69332505T2 (de) * 1993-04-27 2003-10-02 Nisshin Steel Co., Ltd. Rostfreier ferritischer stahl mit hervorragenden hochtemperaturkorrosionseigenschaften und zunderadhesion
KR100240742B1 (ko) * 1994-04-21 2000-01-15 에모또 간지 자동차 배기재료용 열연페라이트강
ATE193957T1 (de) * 1994-10-11 2000-06-15 Crs Holdings Inc Korrosionsfestes magnetmaterial
SE504295C2 (sv) * 1995-04-21 1996-12-23 Avesta Sheffield Ab Förfarande för kallvalsning-glödgning-kallsträckning av ett varmvalsat rostfritt stålband
FR2798394B1 (fr) * 1999-09-09 2001-10-26 Ugine Sa Acier ferritique a 14% de chrome stabilise au niobium et son utilisation dans le domaine de l'automobile
EP1219719B1 (de) * 2000-12-25 2004-09-29 Nisshin Steel Co., Ltd. Ferritisches rostfreies Stahlblech mit einer guten Verarbeitbarkeit und Verfahren zu dessen Herstellung
CA2383808C (en) * 2001-09-27 2009-10-27 Hitachi Metals, Ltd. Steel for separators of solid-oxide type fuel cells
WO2005014873A1 (ja) * 2003-08-06 2005-02-17 Nisshin Steel Co., Ltd. ステンレス鋼の加工硬化材
KR20060089136A (ko) * 2005-02-03 2006-08-08 닛신 세이코 가부시키가이샤 Ｃｐｕ 소켓 프레임용 또는 ｃｐｕ 고정 커버용 고강성스테인레스강판
EP1818421A1 (de) * 2006-02-08 2007-08-15 UGINE &amp; ALZ FRANCE Ferritischer, Niobium-stabilisierter 19% Chrom-Edelstahl
SI3670692T1 (sl) 2018-12-21 2022-11-30 Outokumpu Oyj, Feritno nerjavno jeklo
CN116145030B (zh) * 2022-12-23 2023-12-15 鞍钢股份有限公司 三代核电站关键设备支撑用铁素体不锈钢钢板及制造方法

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4010049A (en) * 1975-10-06 1977-03-01 Jones & Laughlin Steel Corporation Columbium-stabilized high chromium ferritic stainless steels containing zirconium
DE2701329C2 (de) * 1977-01-14 1983-03-24 Thyssen Edelstahlwerke AG, 4000 Düsseldorf Korrosionsbeständiger ferritischer Chrom-Molybdän-Nickelstahl
US4261739A (en) * 1979-08-06 1981-04-14 Armco Inc. Ferritic steel alloy with improved high temperature properties

Also Published As

Publication number Publication date
DK518886D0 (da) 1986-10-30
JPS62112757A (ja) 1987-05-23
NO864394L (no) 1987-05-06
NO167307C (no) 1991-10-23
ZA868359B (en) 1987-06-24
PT83679A (fr) 1986-12-01
PT83679B (pt) 1989-06-30
US4726853A (en) 1988-02-23
ATE42770T1 (de) 1989-05-15
EP0225263A1 (de) 1987-06-10
DE3663150D1 (en) 1989-06-08
ES2008092B3 (es) 1989-07-16
NO864394D0 (no) 1986-11-04
NO167307B (no) 1991-07-15
FR2589482B1 (fr) 1987-11-27
BR8605431A (pt) 1987-08-11
CA1285791C (fr) 1991-07-09
AU6480286A (en) 1987-05-07
FR2589482A1 (fr) 1987-05-07
DK518886A (da) 1987-05-06
AU585083B2 (en) 1989-06-08

Similar Documents

Publication Publication Date Title
EP0225263B1 (de) Blech oder Band aus ferritischem rostfreien Stahl, insbesondere für Auspuffsysteme
KR101210113B1 (ko) 내침탄성 금속 재료
JP5177330B1 (ja) 耐浸炭性金属材料
KR101256268B1 (ko) 오스테나이트계 스테인리스강
JPWO2005078148A1 (ja) 浸炭性ガス雰囲気下で使用するための金属管
US20070187379A1 (en) Weld joint and weld material thereof
JP2003073763A (ja) 耐メタルダスティング性を有する金属材料
JP4088231B2 (ja) 耐食性に優れた原油油槽用溶接継手
EP1005946B1 (de) Schweisselektrode aus einer Nickelbasislegierung und diese Legierung
JP4442331B2 (ja) 耐浸炭性と耐コーキング性を有するステンレス鋼およびステンレス鋼管
JP2002235136A (ja) Ｎｉ基耐熱合金とその溶接継手
JP4513466B2 (ja) 溶接継手および溶接材料
JP5053652B2 (ja) 耐溶融金属脆化割れ性に優れたＺｎ−Ａｌ−Ｍｇ系めっき鋼板
EP0388283B1 (de) Rostfreier ferritischer Stahl und Verfahren zur Herstellung dieses Stahls
CH619491A5 (de)
JP7722299B2 (ja) フェライト系ステンレス冷延焼鈍鋼板、その素材となる冷延鋼板および前記冷延焼鈍鋼板の製造方法
FR2495189A1 (fr) Tole d&#39;acier de haute resistance et son procede de fabrication
JP4610272B2 (ja) 耐溶融金属脆化割れ性に優れたＺｎ−Ａｌ−Ｍｇ合金めっき鋼板の製造方法
JP3424088B2 (ja) 高張力鋼のｔｉｇ溶接方法及びｔｉｇ溶接用ソリッドワイヤ
EP0892076B1 (de) Nickelbasislegierung und Schweisselektrode aus einer Nickelbasislegierung
JP3352857B2 (ja) 極低温鋼用Ｎｉ基合金ＴＩＧ溶接ワイヤ
JP2002275590A (ja) 溶接部の加工性に優れた溶接用フェライト系ステンレス鋼
JPH01202395A (ja) ステンレス鋼ガスシールドアーク溶接用ワイヤ
EP3411509B1 (de) Zusammensetzung für einen stahl mit verbesserten antikokungs-eigenschaften
JPS583942A (ja) 耐中間温度脆性にすぐれたＮｉ基合金

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

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE CH DE ES FR GB IT LI LU NL SE

17P Request for examination filed

Effective date: 19870622

17Q First examination report despatched

Effective date: 19880629

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE CH DE ES FR GB IT LI LU NL SE

REF Corresponds to:

Ref document number: 42770

Country of ref document: AT

Date of ref document: 19890515

Kind code of ref document: T

ITF It: translation for a ep patent filed
GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)
REF Corresponds to:

Ref document number: 3663150

Country of ref document: DE

Date of ref document: 19890608

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

Ref country code: FR

Payment date: 19920928

Year of fee payment: 7

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

Ref country code: ES

Payment date: 19921015

Year of fee payment: 7

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

Ref country code: AT

Payment date: 19921028

Year of fee payment: 7

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

Ref country code: NL

Payment date: 19921031

Year of fee payment: 7

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

Ref country code: GB

Payment date: 19930825

Year of fee payment: 8

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

Ref country code: SE

Payment date: 19930922

Year of fee payment: 8

Ref country code: DE

Payment date: 19930922

Year of fee payment: 8

Ref country code: CH

Payment date: 19930922

Year of fee payment: 8

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

Ref country code: LU

Payment date: 19931015

Year of fee payment: 8

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

Ref country code: BE

Payment date: 19931022

Year of fee payment: 8

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

Ref country code: AT

Effective date: 19931029

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

Ref country code: ES

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 19931030

ITTA It: last paid annual fee
EPTA Lu: last paid annual fee
PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Effective date: 19940501

NLV4 Nl: lapsed or anulled due to non-payment of the annual fee
PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Effective date: 19940630

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

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

Ref country code: LU

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

Effective date: 19941029

Ref country code: GB

Effective date: 19941029

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

Ref country code: SE

Effective date: 19941030

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

Ref country code: LI

Effective date: 19941031

Ref country code: CH

Effective date: 19941031

Ref country code: BE

Effective date: 19941031

EAL Se: european patent in force in sweden

Ref document number: 86420267.6

BERE Be: lapsed

Owner name: S.A. UGINE GUEUGNON

Effective date: 19941031

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

Effective date: 19941029

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

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

Ref country code: DE

Effective date: 19950701

EUG Se: european patent has lapsed

Ref document number: 86420267.6

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 19990601

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;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED.

Effective date: 20051029