EP3631020A1 - Alliage à mémoire de forme fe-mn-si - Google Patents

Alliage à mémoire de forme fe-mn-si

Info

Publication number
EP3631020A1
EP3631020A1 EP18711120.8A EP18711120A EP3631020A1 EP 3631020 A1 EP3631020 A1 EP 3631020A1 EP 18711120 A EP18711120 A EP 18711120A EP 3631020 A1 EP3631020 A1 EP 3631020A1
Authority
EP
European Patent Office
Prior art keywords
shape memory
memory alloy
annealing
temperature
alloy according
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Withdrawn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
EP18711120.8A
Other languages
German (de)
English (en)
Inventor
Lydia LILLPOPP
Sabine Will
Dirk PONGE
Yujiao Li
Minjie LAI
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.)
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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 ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP3631020A1 publication Critical patent/EP3631020A1/fr
Withdrawn legal-status Critical Current

Links

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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D8/0221—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 characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/0247—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 characterised by the heat treatment
    • C21D8/0263—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 characterised by the heat treatment following hot 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
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a shape memory alloy, in particular a shape memory alloy comprising a base alloy of iron, manganese, silicon and chromium and a method for producing the shape memory alloy according to the invention.
  • Shape memory alloys are alloys that can exist in two different crystal structures. After a previous plastic deformation, these alloys can be brought into their old form by exceeding the A s temperature, which is referred to as a disposable effect. There are also alloys that remember their shape at two different temperatures. Such then have a so-called. Two-way effect. Furthermore, shape memory alloys can show a pseudoelastic behavior characterized by a reversible stress-induced martensitic transformation.
  • the thermal, chemical and mechanical behavior is largely determined by the alloy composition and the microstructure.
  • Ni-Ti alloys So far, mostly nickel and titanium based shape memory alloys have been used. They show excellent properties with regard to reversibility, number of cycles and transformation temperatures. Due to the high price of the Ni-Ti alloys and the limited formability, the fields of application are limited and only come into question where, for example, smaller quantities of the material are required.
  • Iron-based shape memory alloys such as Fe-Mn-Si alloys, have a significantly lower price than Ni-Ti alloys, but have a low number of cycles and a strongly decreasing recovery with increasing pre-strains.
  • Another advantage of the iron-based alloys as opposed to Ni-Ti alloys is the residual stress that makes the iron-based alloys very interesting for civil engineering applications. From EP 1 123 983 an Fe-based alloy is known, which in addition to manganese, silicon and chromium has small amounts of the elements niobium and carbon.
  • the disclosed composition has a restoring tension of 160 MPa at most.
  • EP 1 574 587 discloses an Fe-based alloy system which is the same in terms of elements and has values for the maximum restoring stress of 320 MPa.
  • the present invention has the object to provide an iron-based shape memory alloy, which in addition to the improved restoring tension also has an over the prior art improved recovery.
  • the restoring tension for the alloy system of the invention is at least 500 MPa, more preferably at least 600 MPa.
  • the alloy according to the invention has a nearly constant restoring stress at a pre-strain of 1 to 10%.
  • the alloy composition according to the invention has excellent reversibility of the phase transformation.
  • the alloy according to the invention can in principle be obtained by methods known to the person skilled in the art.
  • this alloy can be obtained by alloying iron with scrap or with the corresponding pure metals.
  • a targeted and well-defined mixture of iron and scrap is used to obtain the alloy according to the invention.
  • the alloy according to the invention can be produced more cheaply than is possible using pure metals.
  • this scrap preferably has the following impurities in the stated maximum amounts.
  • the scrap used to produce the alloy according to the invention contains sulfur to at most 0, 1 wt .-%, preferably at most 0.05 wt .-%, particularly preferably at most 0.01 wt .-%.
  • the scrap used to produce the alloy according to the invention contains phosphorus at most 0.05% by weight, preferably at most 0.04% by weight, particularly preferably at most 0.03% by weight.
  • the scrap used to produce the alloy according to the invention contains copper at most 0.3% by weight, preferably at most 0.2% by weight, particularly preferably at most 0.15% by weight.
  • the scrap used to produce the alloy according to the invention contains molybdenum at most 0.2% by weight, preferably at most 0.15% by weight, particularly preferably at most 0.08% by weight.
  • the scrap used to produce the alloy according to the invention contains nitrogen at most 0.2% by weight, preferably at most 0.1% by weight, particularly preferably at most 0.05% by weight.
  • the scrap used to produce the alloy according to the invention contains nickel at most 0.8% by weight, preferably at most 0.65% by weight, particularly preferably at most 0.55% by weight.
  • the scrap used to produce the alloy according to the invention contains titanium to at most 0, 15 wt .-%, preferably at most 0, 1 wt .-%, particularly preferably at most 0.07 wt .-%.
  • the scrap used to produce the alloy according to the invention contains tin to at most 0, 1 wt .-%, preferably at most 0.075 wt .-%, particularly preferably at most 0.05 wt .-%.
  • the vanadium and carbon elements are present in the shape memory alloy in the form of vanadium carbide nanoparticles.
  • VC nanoparticles have a small atomic radius difference so that they fit very well into face-centered cubic lattices.
  • the VC nanoparticles in the shape memory alloy preferably have a volume in the range from 0.1 to 3% by volume, more preferably from 0.5 to 2.5% by volume, particularly preferably from 1.0 to 1.8% by volume. %, one. In combination with the size of the nanoparticles, the formation of stacking faults and martensite is optimally promoted.
  • the volume of the VC nanoparticles can be determined by methods known to those skilled in the art, for example by
  • the shape memory alloy has an austenitic basic structure with coherently and / or partially coherently integrated VC nanoparticles.
  • Coherent precipitates have lattice parameters that differ only slightly from the lattice of the present Fe-Mn-Si-Cr base alloy. As a result, the grid can pass into the grid of precipitation with virtually no major geometric distortion. The phase boundary is coherent. Because of the necessary adaptation of the lattice to the diverging lattice of the precipitate, however, the matrix is also clamped in a large area around the precipitate. Hardening by coherent precipitates is most effective because the hardness of the intermediate compound is superimposed on the strain of the matrix.
  • the lattice of partially coherent precipitates can no longer be completely matched to the lattice of the base alloy.
  • Some transition between matrix and excretion is e.g. achieved in that at the phase boundary in a regular sequence dislocations are formed. Again, the matrix is clamped around the excreta.
  • the VC nanoparticles therefore preferably have a size in the range from 2 to 50 nm, more preferably 10 to 50 nm, particularly preferably 20 to 45 nm.
  • the shape memory alloy has a phase transition temperature M s and A s in the range of 0 ° C to 450 ° C, more preferably in the range of 120 to 370 ° C.
  • the present invention relates to a method for producing a shape memory alloy comprising the steps of: i) melting and casting a pure element mixture or a mixture of iron and scrap consisting of (in% by weight):
  • the pure element mixture was an alloy consisting of an iron carrier based on Armco iron and defined alloying additions with specific degrees of purity of manganese 99.9%; Silicon 75%; Chromium 99.5%; Vanadium 71, 1% and low-sulfur coal ( ⁇ 10 ppm sulfur) used.
  • a mixture of iron and scrap is used in step i).
  • a targeted and defined mixture of iron and scrap is used in order to obtain the alloy according to the invention.
  • the scrap contains the components desired in the alloy and optionally impurities in the abovementioned maximum amounts.
  • the resulting ingot is hot rolled to a thickness in the range of 1 to 6 mm.
  • a roller end temperature in the range of 750 to 1040 ° C, preferably 750 to 900 ° C is set.
  • the method further comprises the steps of: iii) annealing and cooling in a first temperature and time window, and iv) annealing and cooling in a second temperature and time window, both temperature and time windows differing in temperature and duration.
  • step iii) is achieved according to the inventive method that the alloying elements dissolve in the matrix.
  • the alloying elements dissolve in the matrix.
  • Homogenticiansglühen no VC nanoparticles form, since the atoms are preferably present in solution under these conditions.
  • the annealing in step iii) takes place in a temperature range of 1100-1300 ° C for 200-480 minutes.
  • the sample is cooled in a defined manner after the annealing in step iii), so that the VC nanoparticles are precipitated in the correct size, quantity and distribution.
  • the annealing in step iii) takes place under protective atmosphere.
  • the annealing in step iv) therefore takes place in a temperature range of 700-1000 ° C. for 60-180 minutes.
  • the present invention also relates to a shape memory alloy produced by the method according to the invention.
  • the shape memory alloy thus prepared has a restoring tension of at least 500 MPa, more preferably 600 MPa.
  • the shape memory alloy thus prepared has a recovery of at least 75% at a pre-strain of 5%.
  • the present invention relates to the use of the shape memory alloy according to the invention as a connecting element and / or as a damping element.
  • Preferred fasteners are systems for securing, loosening, prestressing and assembly of machine elements, components and / or structural parts (constructions) and / or for fastening, for example screws, bolts, etc.
  • fasteners are fasteners and / or reinforcing elements, such. B. mats.
  • a particularly preferred connecting element is an anchoring device, such. B. a dowel.
  • FIG. 2 shows a diagram with results from tempered bending tests
  • FIG. 3 shows HRTEM images of precipitated VC nanoparticles that are coherently (c) or partially coherently (a, b) integrated.
  • Fig. 4 shows a nano-structural image of the alloy 2 according to the invention after the homogenization annealing, i. in the solution annealed condition, but without a Ausscheidungsglühung has taken place. There are no precipitates and stacking faults visible.
  • FIG. 5 shows a nanostructural absorption of the alloy 2 according to the invention after the homogenization annealing, ie in the solution-annealed condition, and after a precipitation annealing at 650 ° C. (sample 1).
  • First precipitates of VC with an average size of 6 nm can be seen and there are individual stacking faults.
  • 6 shows a nanostructural recording of the alloy 2 according to the invention after the homogenization annealing, ie in the solution-annealed state, and after a precipitation annealing at 700 ° C. (sample 2).
  • Fig. 7 shows a nano-structural image of the alloy 2 according to the invention after the homogenization annealing, i. in the solution-annealed condition, and after a precipitation anneal at 750 ° C (Sample 3).
  • Fig. 8 shows a nano-structural image of the alloy 2 according to the invention after the homogenization annealing, i. in the solution-annealed condition, and after a precipitation anneal at 850 ° C (Sample 5).
  • alloys consisting of 28 wt% Mn, 6 wt% Si, 5 wt% Cr, 0.76 wt% V, 0, 18 wt% C, and balance iron and unavoidable Melted impurities in an induction furnace and cast in a copper mold.
  • alloy 1 an element mixture was used that was alloyed with scrap.
  • Alloy 2 a pure element mixture consisting of an iron carrier based on Armco iron and defined alloy additions with specific degrees of purity of manganese was 99.9%; Silicon 75% (FeSi 75HP); Chromium 99.5%; Vanadium 71, 1% and low-sulfur coal ( ⁇ 10 ppm sulfur) used.
  • the shape memory properties were determined by tensile and flexural tests after different heat treatments. For this, the samples were each pre-formed in the range of 1 to 6% and after subsequent tempering their degree of recovery was determined. The results of the recovery are summarized in Fig. 2 versus an unannealed (no precipitation annealing) sample.
  • the rebounds of the specimens which are in the pure homogenization annealed state and have undergone an aging anneal at 650 ° C, are below 50% with a pre-strain level between 1 and 6%.
  • the precipitation-annealed specimens with annealing temperatures above 700 ° C are significantly more than 75% at the same pre-strain level with the rebounding.

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)
  • Heat Treatment Of Articles (AREA)

Abstract

La présente invention concerne un alliage à mémoire de forme présentant une tension de rappel améliorée par rapport à l'état de la technique, cet alliage à mémoire de forme présentant une composition constituée de (en % en poids) : 25-30 Mn, 4-8 Si, 3-7 Cr, 0,5-1 V, 0,05-0,5 % en poids, de préférence 0,1-0,5 % de C, le reste étant du fer et des impuretés inévitables.
EP18711120.8A 2017-06-01 2018-03-19 Alliage à mémoire de forme fe-mn-si Withdrawn EP3631020A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
PCT/EP2017/063322 WO2018219463A1 (fr) 2017-06-01 2017-06-01 Alliage à mémoire de forme fe-mn-si
PCT/EP2018/056876 WO2018219514A1 (fr) 2017-06-01 2018-03-19 Alliage à mémoire de forme fe-mn-si

Publications (1)

Publication Number Publication Date
EP3631020A1 true EP3631020A1 (fr) 2020-04-08

Family

ID=59152822

Family Applications (1)

Application Number Title Priority Date Filing Date
EP18711120.8A Withdrawn EP3631020A1 (fr) 2017-06-01 2018-03-19 Alliage à mémoire de forme fe-mn-si

Country Status (2)

Country Link
EP (1) EP3631020A1 (fr)
WO (2) WO2018219463A1 (fr)

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109457091B (zh) * 2018-10-15 2020-02-07 四川大学 一种制备粗晶铁锰硅基形状记忆合金的方法
DE102018129640A1 (de) * 2018-11-23 2020-05-28 Thyssenkrupp Ag Verfahren zum Vorspannen eines Bauwerks mit einer Spannvorrichtung und Verwendung einer solchen Spannvorrichtung zum Befestigen an einem Bauwerk
CN116219259B (zh) * 2023-03-10 2024-06-25 佛山市高明欧一电子制造有限公司 一种用于温控装置的记忆金属的制备方法

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
JP3970645B2 (ja) * 2002-03-15 2007-09-05 淡路マテリア株式会社 鉄基形状記憶合金の製造方法
JP2004002981A (ja) * 2002-03-27 2004-01-08 Kurimoto Ltd 鉄系形状記憶合金管およびその製造方法
JP2004115864A (ja) * 2002-09-26 2004-04-15 Hiroshi Kubo 鉄基形状記憶合金
JP3950963B2 (ja) 2002-12-18 2007-08-01 独立行政法人物質・材料研究機構 ＮｂＣ添加Ｆｅ−Ｍｎ−Ｓｉ系形状記憶合金の加工熱処理法
EP2141251B1 (fr) 2008-06-25 2016-12-28 EMPA Dübendorf Alliages à mémoire de forme à base de fer, de manganèse et de silicium
DE102012113053A1 (de) * 2012-12-21 2014-06-26 Thyssenkrupp Steel Europe Ag Verbindungsmittel mit Formgedächtnis

Also Published As

Publication number Publication date
WO2018219514A1 (fr) 2018-12-06
WO2018219463A1 (fr) 2018-12-06

Similar Documents

Publication Publication Date Title
DE60316212T2 (de) Nickelbasislegierung, heissbeständige Feder aus dieser Legierung und Verfahren zur Herstellung dieser Feder
DE102020106433A1 (de) Nickel-Legierung mit guter Korrosionsbeständigkeit und hoher Zugfestigkeit sowie Verfahren zur Herstellung von Halbzeugen
DE60302108T2 (de) Ausscheidungsgehärtete Kobalt-Nickel-Legierung mit guter Wärmebeständigkeit sowie zugehörige Herstellungsmethode
DE3331654A1 (de) Kupfer-beryllium-legierung und ihre herstellung
DE60205419T2 (de) Niedrig legierter und hitzebeständiger Stahl, Verfahren zur Wärmebehandlung und Turbinenrotor
DE3130914A1 (de) Stahl fuer fahrzeugaufhaengefedern mit hoher bestaendigkeit gegen zunehmendes durchbiegen bzw. durchhaengen
EP3196324B1 (fr) Alliage en aluminium durcissable a base de al-mg-si
EP3631020A1 (fr) Alliage à mémoire de forme fe-mn-si
DE60016286T2 (de) Niedrig legierter und hitzebeständiger Stahl, Verfahren zur Wärmebehandlung und Turbinenrotor
DE60219693T2 (de) Ausscheidungshärtbarer austenitischer stahl
DE69128293T2 (de) Rostfreier Stahl
WO2016020519A1 (fr) Produits semi-finis à haute résistance et en même temps durs, et composants en acier fortement allié, leur procédé de fabrication et utilisation
WO2020064127A1 (fr) Alliage à mémoire de forme, produit plat en acier préparé à partir de celui-ci doté de caractéristiques pseudoélastiques et procédé pour la préparation d'un tel produit plat en acier
DE2649529A1 (de) Umformbare legierung auf kobalt- nickel-chrom-basis und verfahren zu seiner herstellung
EP0035069B1 (fr) Alliage à mémoire de forme à base de Cu-Al ou de Cu-Al-Ni et procédé pour la stabilisation de l'effet de réversibilité
EP1255873B9 (fr) Acier a ressorts de type acier vieilli thermiquement
DE69110707T2 (de) Hochfester rostfreier Stahl.
EP3872206B1 (fr) Procédé de fabrication d'un produit plan en acier laminé à froid, traité ultérieurement et produit plan en acier laminé à froid, traité ultérieurement
DE1233609B (de) Verfahren zur Waermebehandlung einer aushaertbaren Nickel-Chrom-Legierung
WO2020108754A1 (fr) Produit plat constitué d'un matériau à mémoire de forme à base de fer
DE1558676C3 (fr)
DE2209085A1 (de) Alterungsgehärteter martensitischer Nickelstahl
DE69519677T2 (de) Verwendung nichtmagnetischen, rostfreien stahls
DE2636553A1 (de) Nicht-alternder superweichstahl mit einer ausgezeichneten verarbeitbarkeit
DE69216334T2 (de) Superlegierung mit niedrigem Ausdehnungskoeffizient

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: UNKNOWN

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

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

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

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

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20200102

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

RIN1 Information on inventor provided before grant (corrected)

Inventor name: LI, YUJIAO

Inventor name: WILL, SABINE

Inventor name: LAI, MINJIE

Inventor name: LILLPOPP, LYDIA

Inventor name: PONGE, DIRK

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20210920

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

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20220201