EP4168595A1 - Procédé d'utilisation d'effets de permutation dans le but d'augmenter la tension et/ou de limiter la perte de tension d'éléments de précharge en un alliage à mémoire de forme - Google Patents

Procédé d'utilisation d'effets de permutation dans le but d'augmenter la tension et/ou de limiter la perte de tension d'éléments de précharge en un alliage à mémoire de forme

Info

Publication number
EP4168595A1
EP4168595A1 EP21731933.4A EP21731933A EP4168595A1 EP 4168595 A1 EP4168595 A1 EP 4168595A1 EP 21731933 A EP21731933 A EP 21731933A EP 4168595 A1 EP4168595 A1 EP 4168595A1
Authority
EP
European Patent Office
Prior art keywords
temperature
prestressing element
heating
time
nanometric
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.)
Pending
Application number
EP21731933.4A
Other languages
German (de)
English (en)
Inventor
Johanna FRENCK
Philipp KROOSS
Thomas Niendorf
Bernhard Middendorf
Alexander Wetzel
Ekkehard Fehling
Malte VOLLMER
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.)
Universitaet Kassel
Original Assignee
Universitaet Kassel
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 Universitaet Kassel filed Critical Universitaet Kassel
Publication of EP4168595A1 publication Critical patent/EP4168595A1/fr
Pending 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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 by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16B—DEVICES FOR FASTENING OR SECURING CONSTRUCTIONAL ELEMENTS OR MACHINE PARTS TOGETHER, e.g. NAILS, BOLTS, CIRCLIPS, CLAMPS, CLIPS OR WEDGES; JOINTS OR JOINTING
    • F16B2200/00—Constructional details of connections not covered for in other groups of this subclass
    • F16B2200/77—Use of a shape-memory material

Definitions

  • the invention relates to a method for increasing the tension or for limiting the tension loss in a prestressing element made of a shape memory alloy (hereinafter SMA), the prestressing element being fixed during the application of the method at the destination, i.e. on or in the component or structure.
  • SMA shape memory alloy
  • SMA are known as prestressing elements for structures or components.
  • SMA are metals that, as a result of a change in temperature and / or mechanical stress, change their crystal structure through a diffusion-free phase transition between a High-temperature phase (hereinafter austenite) and a low-temperature phase (hereinafter martensite) can change reversibly. They have the possibility to “remember” their original shape, which means that even after a large (pseudoplastic / pseudoelastic) mechanical deformation of a SMA, it can return to its original state.
  • austenite High-temperature phase
  • martensite low-temperature phase
  • the procedure here is that a prestressing element from a SMA stretched to a permanent pre-deformation is mechanically anchored on or in a building or component, and is activated in the fixed state, that is, the anchored prestressing element is heated to a certain characteristic temperature, which in or is above the activation temperature interval, heated, in which case the prestressing element strives to return to its initial state, and here and during the subsequent cooling, stresses are applied to the component or structure.
  • the pre-tensioning achieved in this way is determined by the tension interval at which a conversion to martensite takes place again at the operating temperature, ie at the temperature at which the component or structure to be fixed is usually used, and / or is limited by the strength of the material.
  • the tension may decrease over time or is no longer sufficient to ensure safe use of the component or structure.
  • the pretensioning element had to be replaced or that additional pretensioning elements had to be provided and pretensioned. This is associated with considerable effort and is correspondingly expensive.
  • composite pre-tensioning elements it has not previously been possible to re-tension to compensate for the pre-tensioning losses.
  • precipitate particles finely dispersed precipitates
  • the plastic deformation of the material is made more difficult by various mechanisms, such as coherent stress fields, the Kelly Fine mechanism or the Orowan mechanism.
  • Precipitation hardening often takes place by means of a heat treatment of a supersaturated mixed crystal (aging) in order to increase the driving force and diffusion speed to such an extent that nucleation and growth take place in the material.
  • the object on which the invention is based is to achieve an increase in strength and / or a decrease in transformation temperatures and thus ultimately also an increase in transformation stresses by relocating precipitated particles in the already fixed state at the destination.
  • the object on which the invention is based is to prevent a loss of preload during use in a simple and inexpensive manner certain level, by a precipitation-related change in the transformation temperatures and thus the occurring shape memory effects, to limit and / or to increase the mechanical stress generated by the prestressing element in a simple and inexpensive manner, that is, the mechanical stress in the prestressing element to z. B. the original or a higher voltage.
  • This enables the pretensioning element to be upgraded when the pretensioning element is installed and fixed. Since the pre-tensioning and the subsequent increase in the pre-tensioning can take place without relative movements between the component and the pre-tensioning element, there are no losses of the pre-tensioning force due to friction even with curved profiles of the pre-tensioning element's geometry.
  • the following work steps are provided according to a method for using outsourcing effects with the aim of increasing the stress and / or limiting the stress loss of prestressing elements from a SMA, the prestressing element being fixed in a component or structure: Prestressing element in the fixed state, starting from a first temperature T1 to a second temperature T2, which is above the first temperature T1, the second temperature T2 and the holding time HT2 at the second temperature T2 and / or the heating time AHT2 for heating the prestressing element the temperature T2 is such that it is nanometric
  • Precipitation particles form in the structure of the prestressing element and / or existing precipitate particles enlarge;
  • T1 and T3 can correspond to the operating temperature, for example the room temperature or the ambient temperature.
  • Precipitation particles consist of alloying elements, for example aluminum, nickel, titanium, which are previously randomly distributed in the matrix.
  • the precipitated particles increase the yield strength and the strength of the prestressing element, change the coefficient of thermal expansion and at the same time lower the transformation temperatures. This allows higher pre-stresses to be generated.
  • the precipitation particles are characterized in that
  • the heating time AT2 for heating the prestressing element on the temperature T2 and / or the holding time HT2 at the second temperature T2 is such that nanometric precipitation particles form in the structure of the prestressing element and / or existing precipitation particles increase;
  • the precipitated particles increase the yield strength and the strength of the prestressing element, change the coefficient of thermal expansion and the modulus of elasticity and at the same time lower the transformation temperatures (Mf, Ms, As and Af).
  • the transformation temperatures Mf, Ms, As and Af.
  • the lowering of the transformation temperatures leads to an increased stress level at which a renewed transformation into martensite takes place and to an increased stress level at which a transformation from martensite into austenite takes place. Both the increased strength and the changed
  • the coefficient of thermal expansion and the increased stress level of the transformation from austenite to martensite enable the pretension to be increased.
  • the increased stress level at which a transformation from martensite to austenite takes place, enables the formation of a stress plateau when the load is removed from the prestressing element, which can be used to limit the loss of prestressing.
  • a change in the modulus of elasticity in the relief path can also limit the loss of prestress.
  • the work steps according to claim 1 or claim 2 can be repeated (claim 3), whereby the temperatures, holding times, heating-up times and cooling-down times can differ from the previously used temperatures, holding times, heating-up times and cooling-down times, but don't have to.
  • the heating time AHT4 for heating the prestressing element to the fourth temperature T4 and / or the holding time HT4 different from or equal to the heating time AHT2 and / or the Holding time HT2, the heating time AHT4 for heating the prestressing element to temperature T4 and / or holding time HT4 at fourth temperature T4 is such that nanometric precipitation particles form in the structure of the prestressing element and / or existing nanometric precipitation particles grow;
  • Cooling of the prestressing element to a temperature T7 which is in the range of the third temperature T3, the cooling time AKT7 being different from or the same as the cooling time AKT3, with further nanometric precipitation particles forming in the structure of the prestressing element during the cooling time AKT Z to the temperature T7 and / or existing precipitates enlarge.
  • a repetition of the work steps according to claim 6 can also be provided in this context, wherein a Temperature T6 new is higher than or equal to the previous temperature T6 ai t at each repetition.
  • a Temperature T6 new is higher than or equal to the previous temperature T6 ai t at each repetition.
  • the temperature for example T2 or T4 or T6
  • the temperature is selected so that an at least partial reconversion of the martensitic structure into austenitic structure takes place in the pre-stretched state of the prestressing element in the initial state.
  • the nanometric waste particles have a size of 1 to 500 nanometers, but preferably a size of 1 to 25 nanometers, the nanometric waste particles advantageously acting as the source of the coherent or at least partially coherent stress fields. These are embedded in the SMA matrix, which is ultimately the reason for the increase in voltage, as already mentioned.
  • an SMA based on an iron and / or copper alloy with possibly nickel and / or aluminum components has the advantage that the temperatures for the formation of the precipitated particles can be kept relatively low, in particular in the range up to approx. 250 ° C, which is a temperature that concrete, for example, is able to withstand structurally with integrity.
  • the temperature T2, T4 or T6 for heating the prestressing element can be between 50 ° C and 700 ° C, depending on the application, but advantageously between 50 ° C and 250 ° C for use in buildings.
  • the heating time and also the holding time in the respective work steps are highly variable, which is essentially due to the wide range in which the temperature T2, T4 or T6 is, namely in the maximum range from 50 ° C to 700 ° C.
  • the temperatures T1, T3, T5 and T7 are the respective operating temperatures and are in the range from -196 ° C to 500 ° C, but ideally in the range from -50 ° C to 80 ° C.
  • FIG. 1 shows the pre-stretching process of an SMA pre-stressing element on the basis of an exemplary stress-strain diagram in the temperature range T ⁇ At;
  • Fig. 2 shows an exemplary stress-temperature diagram in which an SMA prestressing element which has been pre-stretched according to Fig. 1 is activated, i.e. heated and then cooled;
  • FIG. 3 shows an exemplary stress-strain diagram of the relief of an SMA prestressing element, as it is shown after a treatment according to FIG. 2;
  • FIG. 4 shows an example of a voltage-temperature diagram in which, at the same temperature, one SMA prestressing element according to FIG. 2 with the same end temperature (T2) but two different hold times (HT2 and HT2 new) have been treated;
  • FIG. 5 shows an exemplary illustration according to FIG. 2, in which a series of heating and cooling cycles are shown, each with a different maximum temperature but the same holding times;
  • Prestressing element arises. During the deformation, a stress plateau is created that is characteristic of the phase transformation or the de-twinning of the martensite. According to the case of the phase transformation, this characteristic stress plateau arises from the transformation of an essentially austenitic structure, as is the case with 0% elongation and without application of a stress s, through the increase in stress into a martensitic structure. If the prestressing element is then relieved from an SMA, i.e. the tension on the prestressing element is reduced to zero, a certain amount of expansion remains, so there is no complete structural transformation to austenite, rather the SMA prestressing element remains at least partially martensitic.
  • the pre-stretched prestressing element as it appears after the treatment according to Fig. 1, is what is fixed at the destination, i.e. in or on the component or structure.
  • This biasing element is now, as can be seen from FIG. 2, activated by heating and subsequent cooling.
  • the prestressing element is heated to a temperature T2, the temperature T2 being approximately 300 ° C., for example.
  • the prestressing element then cools down from temperature T2 to temperature T3.
  • the (partially) martensitic structure is converted into an at least partially austenitic structure, which leads to a contraction of the
  • Biasing element leads.
  • thermal expansion takes place, which counteracts the contraction caused by the conversion.
  • AHT2 heating time
  • AHT3 cooling time
  • HT2 holding time
  • the voltage initially increases considerably due to the negative thermal expansion.
  • the stress in the example at 350 MPa
  • a given temperature here approx. 150 ° C
  • the location of this kink point can be significantly influenced by the precipitated particles, as these make possible plastic deformation more difficult and increase the transformation stresses.
  • the temperatures T1 and T3 are in the range of the ambient temperature and are around 25 ° C.
  • FIG. 3 shows a stress-strain diagram similar to FIG. 1, but, in contrast to FIG. 1, in the stress-strain diagram according to FIG. have taken place previously.
  • the activated pretensioning element is gradually relieved of load, with an almost constant tension being shown over a large area during the relief, which is attributable to the transformation from martensitic structure to austenitic structure during relief. This is in turn due to the increased transformation stresses from martensite to austenite and thus, according to the Clausius-Clapeyron relationship, to the lowering of the transformation temperatures due to the precipitated particles. It has been found that the stress can be maintained by such a stress plateau over a large expansion range despite, for example, shrinkage and creep processes of the component, for example the concrete surrounding the prestressing element.
  • the illustration shows a double activation according to FIG. 2, the prestressing element being heated to a temperature T2 (here 250 ° C.) in a first cycle, in order then to be cooled to temperature T3;
  • T2 temperature
  • T3new temperature T3new
  • T3new temperature T3new
  • the difference between the two cycles shown is that the holding time for the first cycle is one second (HT2), whereas the holding time for the second cycle is 30 minutes (HT2new).
  • the last cooling process ends at a temperature T7new * , whereby it can be seen that the stress s has increased by approx. 100 MPa after each cycle.
  • the holding times during the individual cycles were kept the same at 30 seconds in each case.
  • the time between the heating processes from an operating temperature, for example T1, T3, T5, T7, to a correspondingly higher temperature can be several years.
  • the representation according to FIG. 5 reflects the teaching according to claim 3 and the teaching according to claims 6 and 7 again.

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

Abstract

L'invention concerne un procédé d'utilisation d'effets de permutation dans le but d'augmenter la tension et/ou de limiter la perte de tension d'éléments de précharge en un alliage à mémoire de forme, l'élément de précharge étant fixé à la destination, c'est-à-dire sur ou dans l'élément ou la structure, pendant le procédé.
EP21731933.4A 2020-06-17 2021-05-31 Procédé d'utilisation d'effets de permutation dans le but d'augmenter la tension et/ou de limiter la perte de tension d'éléments de précharge en un alliage à mémoire de forme Pending EP4168595A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102020115941.2A DE102020115941A1 (de) 2020-06-17 2020-06-17 Verfahren zur Nutzung von Auslagerungseffekten mit dem Ziel der Erhöhung der Spannung und/oder der Begrenzung des Spannungsverlustes von Vorspannelementen aus einer Formgedächtnislegierung
PCT/EP2021/064520 WO2021254768A1 (fr) 2020-06-17 2021-05-31 Procédé d'utilisation d'effets de permutation dans le but d'augmenter la tension et/ou de limiter la perte de tension d'éléments de précharge en un alliage à mémoire de forme

Publications (1)

Publication Number Publication Date
EP4168595A1 true EP4168595A1 (fr) 2023-04-26

Family

ID=76421942

Family Applications (1)

Application Number Title Priority Date Filing Date
EP21731933.4A Pending EP4168595A1 (fr) 2020-06-17 2021-05-31 Procédé d'utilisation d'effets de permutation dans le but d'augmenter la tension et/ou de limiter la perte de tension d'éléments de précharge en un alliage à mémoire de forme

Country Status (3)

Country Link
EP (1) EP4168595A1 (fr)
DE (1) DE102020115941A1 (fr)
WO (1) WO2021254768A1 (fr)

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102013223084A1 (de) 2012-11-27 2014-05-28 GM Global Technology Operations, LLC (n.d. Ges. d. Staates Delaware) Hohle superelastische formgedächtnislegierungspartikel
CH707301B1 (de) 2013-04-08 2014-06-13 Empa Verfahren zum Erstellen von vorgespannten Betonbauwerken mittels Profilen aus einer Formgedächtnis-Legierung sowie Bauwerk, hergestellt nach dem Verfahren.
WO2020064127A1 (fr) 2018-09-28 2020-04-02 Thyssenkrupp Steel Europe Ag 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
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

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Publication number Publication date
DE102020115941A1 (de) 2021-12-23
WO2021254768A1 (fr) 2021-12-23

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