EP1574587B1 - VERFAHREN ZUR THERMOMECHANISCHEN BEHANDLUNG FÜR EINE MIT NbC DOTIERTE Fe-Mn-Si-FORMGEDÄCHTNISLEGIERUNG - Google Patents

VERFAHREN ZUR THERMOMECHANISCHEN BEHANDLUNG FÜR EINE MIT NbC DOTIERTE Fe-Mn-Si-FORMGEDÄCHTNISLEGIERUNG Download PDF

Info

Publication number
EP1574587B1
EP1574587B1 EP03780855A EP03780855A EP1574587B1 EP 1574587 B1 EP1574587 B1 EP 1574587B1 EP 03780855 A EP03780855 A EP 03780855A EP 03780855 A EP03780855 A EP 03780855A EP 1574587 B1 EP1574587 B1 EP 1574587B1
Authority
EP
European Patent Office
Prior art keywords
shape memory
weight
memory alloy
alloy
addition
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 - Lifetime
Application number
EP03780855A
Other languages
English (en)
French (fr)
Other versions
EP1574587A1 (de
EP1574587A4 (de
Inventor
T. c/o NAT. INSTITUTE FOR MAT. SCIENCE KIKUCHI
Satoshi Kajiwara
A. c/o NAT. INSTITUTE FOR MAT. SCIENCE BARUJ
K. c/o NAT. INSTITUTE FOR MAT. SCIENCE OGAWA
N. c/o NAT. INSTITUTE FOR MAT. SCIENCE SHINYA
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.)
National Institute for Materials Science
Original Assignee
National Institute for Materials Science
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 National Institute for Materials Science filed Critical National Institute for Materials Science
Publication of EP1574587A1 publication Critical patent/EP1574587A1/de
Publication of EP1574587A4 publication Critical patent/EP1574587A4/de
Application granted granted Critical
Publication of EP1574587B1 publication Critical patent/EP1574587B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C22/00—Alloys based on 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
    • C22C38/02—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/006—Resulting in heat recoverable alloys with a memory effect
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/01—Shape memory effect

Definitions

  • the present invention relates to a thermomechanical treatment method for a Fe-Mn-Si-based shape memory alloy with Nb, C addition. More particularly, the present invention relates to a thermomechanical treatment method for a Fe-Mn-Si-based shape memory alloy with Nb, C addition which exhibits a satisfactory shape memory effect without undergoing so-called training, providing improved performance.
  • the training means a process sequence of repeating the following treatment several times to improve shape memory effect.
  • the treatment consists of deforming an alloy by 2-3% at room temperature and then heating it to around 600°C higher than the reverse transformation temperature of the alloy.
  • EP-A-1 123 983 discloses a shape memory alloy of Fe-Mn-Si system containing at least Fe, Mn and Si, wherein the alloy contains niobium carbides in the structure and the alloy is subjected to a heat treatment for homogenization at a temperature ranging from 1000°C to 1300°C and subsequently an ageing at a temperature ranging from 400°C to 1000°C to precipitate niobium carbides.
  • US-A-5,032,195 discloses a Fe-based shape memory alloy which is hot-rolled in the thickness of 0.8 mm and 4 mm after homogenization, and the hot-rolled plate of 4 mm is annealed at room temperature several times and then cold-rolled into a plate having 0.8 mm in thickness and the cold-rolled plate is annealed at 600°C for 2 hours.
  • the object of the present invention is to fundamentally solve the aforementioned problems.
  • the inventors of this invention has earnestly studied aiming at developing and ensuring good shape memory properties for a shape memory alloy of specified components even with deformation at low temperatures. As a result, they found that the satisfactory shape memory properties can be sufficiently ensured even with deformation at room temperature so as to achieve the aforementioned object.
  • the excellentshape memory property of alloy can be developed just by applying a basic operation comprising deforming a Fe-Mn-Si-based shape memory alloy with Nb, C addition at room temperature and then subjecting the deformed alloy to aging heating treatment to precipitate NbC carbides.
  • a basic operation comprising deforming a Fe-Mn-Si-based shape memory alloy with Nb, C addition at room temperature and then subjecting the deformed alloy to aging heating treatment to precipitate NbC carbides.
  • the deformation prior to aging is carried out in a temperature range of from 500°C to 800°C in case of the prior applications. According to the present invention, however, the deformation prior to the aging treatment can be successfully carried out not at high temperature but at room temperature, by setting the deformation ratio in a specified range.
  • the technical meaning of the present invention must be clearly understood as compared to the prior art and the inventions of the prior applications on which the present invention is based because there are obvious difference therebetween. That is, according to the present invention, the remarkable improvement in shape memory property is achieved first time by a combination of specified alloy components, specified deformation ratio at room temperature, and setting of aging condition to a certain range. Amazingly by run-of-the-mill thermomechanical treatment comprising a deformation at room temperature and then aging, the shape recovery ratio equivalent to that of the sample subjected to the training can be obtained and, in addition, the shape recovery stress significantly larger than that of the sample subjected to the training can be obtained. With development of the present invention, it is expected that the use of shape memory alloys will be accelerated toward the practical use in a wide variety of fields. The invention is described in detail in conjunction with the drawings, in which
  • the reason why the deformation ratio at room temperature is specified to be from 5% to 40% comes from the fact that the deformation ratio lower than 5% does not effectively contribute to improvement in shape memory property while the deformation ratio over 40% makes a sample too hard so that it is extremely difficult to deform the sample after subjected to an aging treatment.
  • An alloy as to be subjected to the thermomechanical treatment method for a Fe-Mn-Si-based shape memory alloy with Nb, C addition of the present invention has the following chemical compositions, just as specified in the prior applications, 1) Mn: 15% to 40% by weight, Si: 3% to 15% by weight, Nb: 0.1% to 1.5% by weight, C: 0.01% to 0.2% by weight, and Fe and inevitable impurities: residual amount, wherein the atomic ratio Nb/C between Nb and C is 1 or more; 2)
  • the Fe-Mn-Si-based shape memory alloy with Nb, C addition has the following compositions Mn: 15% to 40% by weight, Si: 3% to 15% by weight, Cr: 1% to 20% by weight, Nb: 0.1% to 1.5% by weight, C: 0.01% to 0.2% by weight, and Fe and inevitable impurities: residual amount, wherein the atomic ratio Nb/C between Nb and C is 1 or more; 3)
  • the atomic ratio Nb/C between Nb and C in the alloy is preferably from 1.0 to 1.2.
  • the alloy as to be subjected to a thermomechanical treatment method for the Fe-Mn-Si-based shape memory alloy of the present invention is permitted to contain, as impurities, one or more of a group consisting of Cu of 3% by weight or less, Mo of 2% by weight or less, Al of 10% by weight or less, Co of 30% by weight or less, and N of 5000 ppm or less.
  • a Fe-28Mn-6Si-5Cr-0.53Nb-0.06C alloy (% by weight) with Nb, C addition of the present invention was prepared by melting. How the shape memory property is improved by rolling at room temperature and then subjecting it to an aging treatment in a temperature range of 400°C to 1000°C for a time period from 1 minute to 2 hours, is shown below.
  • FIG. 1 is a graph showing differences in shape recovery ratio among a case in which only aging was conducted (0% rolling) and cases in which aging was conducted after rolling by 10%, 20% and 30% at room temperature. In all of the cases, the aging treatment was conducted at 800°C for 10 minutes. For comparison, results of samples of the Fe-28Mn-6Si-5Cr alloy with no Nb, C addition prepared only by annealing and samples of the alloy prepared after subjected to the training five times are shown. The abscissa shows the initial strain (%) by tensile deformation at room temperature, and the ordinate shows the recovery ratio of strain when the sample is heated to 600°C. When heated to 400°C, approximately the same shape recovery ratio is also obtained. The samples used in tests were test pieces having a thickness of 0.6 mm, a width of 1 to 4 mm, and a length (gage length) of 15 mm.
  • the sample rolled by 10% has shape memory recovery ratios nearly equivalent to or slightly lower than those of the alloy with no Nb, C addition which was subjected to training five times. Practically the necessary initial strain is believed to be about 4%. A shape memory recovery ratio of about 90% shown at this strain strongly suggests that it is used as a practically applicable alloy. Training of at least five times is necessary for obtaining the same shape recovery ratio as this sample, with a conventional Fe-Mn-Si-based shape memory alloy with no Nb, C addition. As is understood from this, the present invention exhibits shape memory properties with a simple method.
  • the sample with a higher rolling ratio of 20% has shape memory recovery ratios nearly equivalent to or slightly higher than those of the case without rolling (only aged). However, the sample with a further higher rolling ratio of 30% has shape memory recovery ratios lower than those of the case which was only aged in a range with large initial strain.
  • Fig. 2 is a graph showing the degrees of improvement in shape recovery stress of these samples, in comparison with the case in which only aging was conducted (0% rolling) and a case in which the aging was conducted after rolling by 10%.
  • the recovery stress when recovered strain on the abscissa is zero means the stress generated when a sample is tensile-deformed at room temperature, then, heated to the reverse transformation temperature or more in a state that the both ends of the sample are fixed without any recovery, and returned to room temperature again.
  • the recovery stress at recovered strain of 2% for example, means the stress generated in case that the both ends of the sample are fixed after a recovery of strain by 2%. Tests were conducted with the initial strain given at room temperature of from 4% to 6%.
  • the test pieces used were the same as those used for obtaining the results shown in Fig. 1 .
  • the recovered strain on the abscissa in Fig. 2 is explained, taking a case where a shape memory alloy is used as a coupling for examples. It is equivalent to the ratio (%) of clearance between the pipes and the coupling part (shape memory alloy) to the diameter.
  • Remarkable increase in shape recovery stress is observed in a range of high rolling ratio: a shape recovery stress of 310MPa is obtained at the recovered strain of 0% when the rolling ratio is from 20% to 30% at room temperature and a shape recovery stress of 200 MPa is obtained even at the recovered strain of 2% for the same rolling ratio. It is also found that the same shape recovery stress as the case subjected to training is obtained even in a case that the rolling ratio is 10%.
  • Fig. 2 shows shape recovery stresss of the sample with no Nb, C addition and the sample subjected to the training five times. It is seem from this figure that the recovery stresses of these samples are much smaller than those of the present invention.
  • the present invention was made by finding that the deformation treatment prior to the aging treatment to a Fe-Mn-Si-based shape memory alloy having specified components with Nb, C addition can be successfully carried out at room temperature if the deformation ratio is in a specified range.
  • the technical meaning of the present invention must be clearly understood because there are obvious advantages as compared to a conventional one which requires the training accompanied by troublesome operation and the inventions of the prior applications which still require high-temperature deformation in a range of from 500°C to 800°C.
  • the remarkable improvement in shape memory property is achieved first time by a combination of specified alloy components, specified deformation ratio at room temperature, and setting of aging condition to a certain range.
  • the shape recovery ratio equivalent to that of the sample subjected to the training can be obtained and, in addition, the shape recovery stress significantly larger than that of the sample subjected to the training can be obtained.
  • the meaning of the present invention is significant.
  • the shape memory alloy according to the present invention can be used as tightening materials for various applications, for example, for tightening water pipes, tightening oil pipes, etc., which will produce great economic effects.
  • the present invention provides a thermomechanical treatment means for a Fe-Mn-Si-based shape memory alloy having specified components with Nb, C addition with simple processing treatment prior to aging.
  • the deformation treatment prior to aging is carried out in a temperature range of from 500°C to 800°C. According to the present invention, however, the deformation treatment prior to the aging treatment can be successfully carried out not at high temperature but at room temperature, if the deformation ratio in a specified range.
  • the technical meaning of the present invention must be clearly understood as compared to the prior art and the inventions of the prior applications because there are obvious difference therebetween. That is, according to the present invention, the remarkable improvement in shape memory property is achieved first time by a combination of specified alloy components, specified processing ratio at room temperature, and setting of aging condition into a certain range.
  • the technical meaning of the present invention must be clearly understood as compared to the prior art and the inventions of the prior applications because there are obvious difference therebetween. That is, according to the present invention, the remarkable improvement in shape memory property is achieved first time by a combination of specified alloy components, specified deformation ratio at room temperature, and setting of aging condition to a certain range. Amazingly by run-of-the-mill thermomechanical treatment comprising a deformation at room temperature and then aging, the shape recovery ratio equivalent to that of the sample subjected to the training can be obtained and, in addition, the shape recovery stress significantly larger than that of the sample subjected to the training can be obtained. With development of the present invention, it is expected that the use of shape memory alloys will be accelerated toward the practical use in a wide variety of fields.

Landscapes

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

Claims (4)

  1. Thermomechanisches Behandlungsverfahren für eine Fe-Mn-Si-basierte Formgedächtnislegierung mit Nb- und C-Zugabe, wobei die Fe-Mn-Si-basierte Formgedächtnislegierung mit Nb- und C-Zugabe als Legierungskomponenten aufweist: Mn: 15 bis 40 Gew.-%, Si: 3 bis 15 Gew.-%, Nb: 0,1 bis 1,5 Gew.-%, C: 0,01 bis 0,2 Gew.-%, optional Cr: 1 bis 20 Gew.-% und/oder Ni: 0,1 bis 20 Gew.-% und als Rest Eisen und unvermeidliche Verunreinigungen, wobei das Atomverhältnis Nb/C zwischen Nb und C mindestens 1 beträgt,
    dadurch gekennzeichnet, daß das Verfahren die Schritte aufweist:
    Verformen der Fe-Mn-Si-basierten Formgedächtnislegierung mit Nb- und C-Zugabe durch ein Formänderungsverhältnis von 5 % bis 40 % bei Raumtemperatur, und
    Unterziehen der verformten Legierung einer Wärmealterungsbehandlung, um NbC-Carbide auszuscheiden.
  2. Thermomechanisches Behandlungsverfahren für eine Fe-Mn-Si-basierte Formgedächtnislegierung mit Nb- und C-Zugabe nach Anspruch 1, wobei das Atomverhältnis zwischen Nb und C in einem Bereich von 1,0 bis 1,2 festgelegt ist.
  3. Thermomechanisches Behandlungsverfahren für eine Fe-Mn-Si-basierte Formgedächtnislegierung mit Nb- und C-Zugabe nach Anspruch 1 oder 2, wobei die Fe-Mn-Si-basierte Formgedächtnislegierung mit Nb- und C-Zugabe als Verunreinigungen enthält: Cu: höchstens 3 Gew.-%, Mo: höchstens 2 Gew.-%, Al: höchstens 10 Gew.-%, Co: höchstens 30 Gew.-% und/oder N: höchstens 5000 ppm.
  4. Thermomechanisches Behandlungsverfahren für eine Fe-Mn-Si-basierte Formgedächtnislegierung mit Nb- und C-Zugabe nach einem der Ansprüche 1 bis 3, wobei die Bedingungen für die Wärmealterungsbehandlung ein Temperaturbereich von 400 °C bis 1000 °C und eine Zeitdauer von 1 Minute bis 2 Stunden sind.
EP03780855A 2002-12-18 2003-12-17 VERFAHREN ZUR THERMOMECHANISCHEN BEHANDLUNG FÜR EINE MIT NbC DOTIERTE Fe-Mn-Si-FORMGEDÄCHTNISLEGIERUNG Expired - Lifetime EP1574587B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2002367062A JP3950963B2 (ja) 2002-12-18 2002-12-18 ＮｂＣ添加Ｆｅ−Ｍｎ−Ｓｉ系形状記憶合金の加工熱処理法
JP2002367062 2002-12-18
PCT/JP2003/016189 WO2004055222A1 (ja) 2002-12-18 2003-12-17 ＮｂＣ添加Ｆｅ−Ｍｎ−Ｓｉ系形状記憶合金の加工熱処理方法

Publications (3)

Publication Number Publication Date
EP1574587A1 EP1574587A1 (de) 2005-09-14
EP1574587A4 EP1574587A4 (de) 2006-02-01
EP1574587B1 true EP1574587B1 (de) 2008-07-16

Family

ID=32588334

Family Applications (1)

Application Number Title Priority Date Filing Date
EP03780855A Expired - Lifetime EP1574587B1 (de) 2002-12-18 2003-12-17 VERFAHREN ZUR THERMOMECHANISCHEN BEHANDLUNG FÜR EINE MIT NbC DOTIERTE Fe-Mn-Si-FORMGEDÄCHTNISLEGIERUNG

Country Status (7)

Country Link
US (1) US20050236077A1 (de)
EP (1) EP1574587B1 (de)
JP (1) JP3950963B2 (de)
KR (1) KR20050083601A (de)
CN (1) CN100342039C (de)
DE (1) DE60322260D1 (de)
WO (1) WO2004055222A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102018119296A1 (de) * 2018-08-08 2020-02-13 Thyssenkrupp Ag Inline Vorrecken von Formgedächtnislegierungen, insbesondere Flachstahl

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8409372B1 (en) 2010-09-02 2013-04-02 The United States of America as Represented by the Administraton of National Aeronautics and Space Administration Thermomechanical methodology for stabilizing shape memory alloy (SMA) response
DE102013102353A1 (de) * 2013-03-08 2014-09-11 Thyssenkrupp Steel Europe Ag Temperaturgesteuertes Umlenkmittel
WO2014146733A1 (de) 2013-03-22 2014-09-25 Thyssenkrupp Steel Europe Ag Eisenbasierte formgedächtnislegierung
CN104328323A (zh) * 2014-10-24 2015-02-04 王健英 一种锰铁合金材料及制备方法
EP3511435B1 (de) * 2016-09-06 2021-04-07 Tohoku University Fe-basiertes formgedächtnislegierungsmaterial und verfahren zur herstellung davon
CN107012411A (zh) * 2017-03-08 2017-08-04 宁波高新区远创科技有限公司 一种土壤接地网用合金材料的制备方法
WO2018219463A1 (de) 2017-06-01 2018-12-06 Thyssenkrupp Steel Europe Ag Fe-Mn-Si FORMGEDÄCHTNISLEGIERUNG
WO2020108754A1 (de) 2018-11-29 2020-06-04 Thyssenkrupp Steel Europe Ag Flachprodukt aus einem eisenbasierten formgedächtniswerkstoff

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62112720A (ja) * 1985-11-09 1987-05-23 Nippon Steel Corp Ｆｅ−Ｍｎ−Ｓｉ系形状記憶合金の特性向上方法
US5032195A (en) * 1989-03-02 1991-07-16 Korea Institute Of Science And Technology FE-base shape memory alloy
JPH0382741A (ja) * 1989-08-25 1991-04-08 Nisshin Steel Co Ltd 耐応力腐食割れ性に優れた形状記憶ステンレス鋼およびその形状記憶方法
FR2654748B1 (fr) * 1989-11-22 1992-03-20 Ugine Aciers Alliage inoxydable a memoire de forme et procede d'elaboration d'un tel alliage.
JP3542754B2 (ja) * 2000-02-09 2004-07-14 独立行政法人物質・材料研究機構 形状記憶合金
JP2003277827A (ja) * 2002-03-20 2003-10-02 National Institute For Materials Science ＮｂＣ添加Ｆｅ−Ｍｎ−Ｓｉ系形状記憶合金の加工熱処理方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102018119296A1 (de) * 2018-08-08 2020-02-13 Thyssenkrupp Ag Inline Vorrecken von Formgedächtnislegierungen, insbesondere Flachstahl

Also Published As

Publication number Publication date
CN1692163A (zh) 2005-11-02
JP3950963B2 (ja) 2007-08-01
CN100342039C (zh) 2007-10-10
JP2004197161A (ja) 2004-07-15
DE60322260D1 (de) 2008-08-28
US20050236077A1 (en) 2005-10-27
EP1574587A1 (de) 2005-09-14
WO2004055222A1 (ja) 2004-07-01
KR20050083601A (ko) 2005-08-26
EP1574587A4 (de) 2006-02-01

Similar Documents

Publication Publication Date Title
US4036669A (en) Mechanical preconditioning method
US4533411A (en) Method of processing nickel-titanium-base shape-memory alloys and structure
EP1574587B1 (de) VERFAHREN ZUR THERMOMECHANISCHEN BEHANDLUNG FÜR EINE MIT NbC DOTIERTE Fe-Mn-Si-FORMGEDÄCHTNISLEGIERUNG
JPH01279736A (ja) β型チタン合金材の熱処理方法
US3802930A (en) Alloys
US4025367A (en) Process for treating copper alloys to improve thermal stability
EP1348772B1 (de) Verfahren zur Herstellung und thermischen Behandlung von Formgedächtnis- Fe-Mn-Si-Legierung mit NbC
JPH10204592A (ja) ステンレス鋼ワイヤーと、その製造方法
JP3970645B2 (ja) 鉄基形状記憶合金の製造方法
JPS60234920A (ja) 超高張力マルエ−ジング冷延鋼板の製造方法
USRE28964E (en) Ultrahigh strength steels
JPS62112720A (ja) Ｆｅ−Ｍｎ−Ｓｉ系形状記憶合金の特性向上方法
JPH0128252B2 (de)
US4395295A (en) Process for treating copper-aluminum-silicon alloys to improve fatigue strength
EP0090115A2 (de) Kaltbearbeitete ferritische Legierungen und Bauteile
JPS60251227A (ja) 低熱膨張Ｆｅ−Ｎｉ系鋼板の製造方法
JPS62199757A (ja) 形状記憶合金材の製造方法
JPH0238547A (ja) Ｔｉ−Ｎｉ系形状記憶合金の製造方法
US6136102A (en) Maraging steel
JPH07258729A (ja) マルテンサイト系析出硬化型ステンレス鋼の製造方法
JP2528358B2 (ja) 形状回復特性に優れた鉄基形状記憶合金の製造方法
EP0460695B1 (de) Pseudoelastische Ti-Ni-C-Formgedächtnislegierung mit einer höheren Elastizitätsgrenze
JPH0770705A (ja) 熱膨張特性に優れたオーステナイトステンレス鋼
JPS63241150A (ja) チタン合金の熱処理方法
US3989551A (en) Method of making a heat-recoverable article

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: 20050105

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/34 20000101ALI20051207BHEP

Ipc: C22C 38/00 19740701ALI20051207BHEP

Ipc: C21D 8/00 19800101AFI20040707BHEP

Ipc: C22F 1/00 19680901ALI20051207BHEP

Ipc: C22C 38/48 20000101ALI20051207BHEP

A4 Supplementary search report drawn up and despatched

Effective date: 20051216

RBV Designated contracting states (corrected)

Designated state(s): DE FR GB

17Q First examination report despatched

Effective date: 20060419

RIN1 Information on inventor provided before grant (corrected)

Inventor name: KAJIWARA, SATOSHI

Inventor name: KIKUCHI, T.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

Inventor name: BARUJ, A.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

Inventor name: SHINYA, N.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

Inventor name: OGAWA, K.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

RIN1 Information on inventor provided before grant (corrected)

Inventor name: OGAWA, K.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

Inventor name: KAJIWARA, SATOSHI

Inventor name: SHINYA, N.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

Inventor name: BARUJ, A.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

Inventor name: KIKUCHI, T.,C/O NAT. INSTITUTE FOR MAT. SCIENCE

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

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 60322260

Country of ref document: DE

Date of ref document: 20080828

Kind code of ref document: P

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: 20090417

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

Ref country code: FR

Payment date: 20110107

Year of fee payment: 8

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

Ref country code: GB

Payment date: 20101217

Year of fee payment: 8

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

Ref country code: DE

Payment date: 20110131

Year of fee payment: 8

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

Effective date: 20111217

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20120831

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 60322260

Country of ref document: DE

Effective date: 20120703

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

Ref country code: DE

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

Effective date: 20120703

Ref country code: GB

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

Effective date: 20111217

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: 20120102