EP2655684B1 - Method for reinforcing an alloy by plasma-nitriding - Google Patents
Method for reinforcing an alloy by plasma-nitriding Download PDFInfo
- Publication number
- EP2655684B1 EP2655684B1 EP11815535.7A EP11815535A EP2655684B1 EP 2655684 B1 EP2655684 B1 EP 2655684B1 EP 11815535 A EP11815535 A EP 11815535A EP 2655684 B1 EP2655684 B1 EP 2655684B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- manufacturing
- temperature
- nitride
- alloy
- ppm
- 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.)
- Not-in-force
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0068—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only nitrides
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/16—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on nitrides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
- C22C33/0228—Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/36—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases using ionised gases, e.g. ionitriding
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/36—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases using ionised gases, e.g. ionitriding
- C23C8/38—Treatment of ferrous surfaces
Definitions
- the present invention relates to a method of manufacturing a reinforced alloy. It relates more particularly to a process for manufacturing an alloy reinforced with nanoparticles of metal nitride.
- NDS nitride Dispersion Strenghtened
- the additional heat treatment of this nitriding process nevertheless has the disadvantage of producing dispersions with an average size of up to 300 nm. This large size of the dispersions tends to degrade the mechanical properties of the reinforced alloy.
- NDS alloy Another type of process used to make an NDS alloy involves powder metallurgy.
- a powder of a nitrogen donor compound such as Cr 2 N
- a powder for forming the metal matrix of a reinforced alloy is co-milled with a powder for forming the metal matrix of a reinforced alloy.
- the resulting powder mixture is subjected to a heat treatment to decompose the nitrogen donor so that the dinitrogen thus available forms a nitride with one of the elements of the metal matrix.
- an alloy reinforced by nitride dispersions is obtained.
- the heat treatment for producing nitrogen by decomposition of the nitrogen donor results in this powder metallurgy process being similar to a nitriding process.
- US 2007/295427 discloses a treated austenitic steel and the associated treatment method comprises an austenitic steel and a nonmetallic chemical element incorporated in a surface of the steel.
- the surface has a bilayer structure with a layer of compound above and an underlying diffusion layer, which protects the surface against embrittlement by hydrogen.
- One of the aims of the invention is therefore to provide a process for manufacturing an "NDS" alloy comprising nanoparticles of which at least 80% have an average size of less than 50 nm, such a method that may allow better control of the composition. and the amount of these nanoparticles within the alloy.
- the present invention thus relates to a method for manufacturing a reinforced alloy comprising a metal matrix in the volume of which nanoparticles are dispersed, of which at least 80% have an average size of 1 nm to 50 nm, the nanoparticles comprising at least one nitride selected from nitrides of at least one metal element M belonging to the group consisting of Ti, Zr, Hf, and Ta.
- the process of the invention does not involve the use of an intermediate nitride intended to form the metal nitride constituting all or part of the dispersed nanoparticles.
- the nitrogen intended to form the nitride is introduced into the base alloy in interstitial form, namely as nitrogen in solid solution. in the base alloy, and not in molecular form N 2 .
- the interstitial nitrogen then combines directly with all or part of this element, under the influence of the diffusion and / or precipitation temperature (generally under the influence of a temperature of between 500 ° C and 650 ° C) to form the nitride.
- the diffusion and precipitation step may therefore be totally or partially overlapping.
- step c) the nitride is precipitated by a germination-growth phenomenon in order to form the nanoparticles dispersed in the reinforced alloy.
- the passage through an intermediate nitride is therefore not necessary, unlike the processes of the state of the art that require a complementary heat treatment generally performed at a temperature of about 1200 ° C in order to dissociate a nitride such as Cr 2 N.
- Another advantage of the manufacturing method of the invention is that the temperature applied during its different stages can be chosen with great freedom.
- the plasma nitriding step a) is carried out at a temperature of 200 ° C. to 700 ° C., preferably 200 ° C. to 600 ° C., even more preferentially from 350 ° C. to 450 ° C.
- Step b) of diffusion of the interstitial nitrogen is carried out at a temperature of 350 ° C to 650 ° C, preferably 350 ° C to 500 ° C. Its duration is generally from 5 hours to 500 hours, preferably from 10 hours to 200 hours. It is generally inversely proportional to the temperature of the interstitial nitrogen diffusion step.
- the precipitation temperature can advantageously be chosen to control the size of the nitride of the metal element M at the expense of the precipitation of a metal element M 'such that Cr whose dissolution of the associated nitride Cr 2 N can only occur at a temperature of 1100 ° C.
- the nitride precipitation step c) is carried out at a temperature which is from 600 ° C. to 900 ° C., preferentially from 600 ° C to 800 ° C, even more preferably from 600 ° C to 700 ° C. Its duration is 10 minutes to 10 hours, preferably 30 minutes to 2 hours. It is generally inversely proportional to the temperature of the nitride precipitation step.
- this method makes it possible to obtain a reinforced alloy whose matrix comprises dispersed nanoparticles of smaller average size than those obtained by the processes of the state of the art mentioned above.
- the verb "to understand”, “to include”, “to incorporate”, “to include” and its conjugate forms are open terms and thus do not exclude the presence of element (s) and / or step (s). ) additional to the element (s) and / or initial stage (s) set out after these terms.
- these open terms also include a particular embodiment in which only the element (s) and / or initial stage (s), to the exclusion of all others, are targeted; in which case the term open also refers to the closed term “consist of", “constitute of” and its conjugated forms.
- the chemical composition of the base alloy, the reinforced alloy or the metal matrix and the nanoparticles it contains is expressed in the present description as a percentage by weight relative to the weight of the alloy considered. .
- Step a) of the manufacturing method of the invention consists of a plasma nitriding as known to those skilled in the art, described for example in the document “Techniques de l' Reference M 1227,” Nitriding, nitrocarburizing and derivatives ", Chapter 4".
- the reactive species can comprise neutral (atomic N) species, or even ionized or excited (such as for example N + or N 2 vibrationnally excited), the nitriding then being called ionic in the latter case.
- these species diffuse interstitial form in the base alloy to then form a nitride with the constituent atoms of this alloy.
- the plasma nitriding is performed on a base alloy incorporating 0.1% to 1% by weight of at least one metal element M selected from Ti, Zr, Hf, or Ta, preferably 0.5 % to 1% by weight of this element.
- the metal element M is titanium.
- the base alloy can be in the form of powder or part.
- It is selected from an austenitic, ferritic, ferritic-martensitic or nickel-based alloy.
- Plasma nitriding can be carried out using a gaseous medium comprising nitrogen (in the form of molecular nitrogen (N 2 ) and / or as a gaseous nitrogen compound such as, for example, NH 3 and / or N 2 H 2 ).
- the nitrogen is diluted in a chemically inert gas (vis-à-vis the other constituents of the gaseous medium), such as, for example, H 2 .
- the gaseous medium may further comprise a carbon species, such as for example CH 4 .
- the gaseous medium may for example comprise 20% to 30% by volume of N 2 and / or of gaseous nitrogen compound, optionally supplemented with 5% to 20% by volume of the carbon species (for example CH 4 ), the rest being constituted by the chemically inert gas (for example H 2 ).
- the pressure of the gaseous medium is generally less than atmospheric pressure, for example from 1 mbar to 100 mbar, preferably from 1 mbar to 10 mbar, still more preferably from 1.5 mbar to 5 mbar.
- Plasma nitriding is generally carried out for a period of 5 hours to 300 hours, preferably from 10 hours to 200 hours, even more preferably from 24 hours to 100 hours.
- the base alloy comprises 1000 ppm to 2000 ppm by weight of nitrogen in interstitial form, which allows the preferential formation of a nitride of the metal element M at the expense of other nitrides such as Cr 2 N.
- the reinforced alloy obtained comprises a metal matrix in which nanoparticles composed entirely or partially of at least one metal nitride are dispersed.
- the metal matrix of the reinforced alloy has the chemical composition of the base alloy.
- the manufacturing method of the invention also makes it possible to preserve the structure of the base alloy (austenitic, ferritic or ferritic-martensitic structure) in the reinforced alloy.
- the nanoparticles are dispersed in all or part of the volume of the reinforced alloy. They represent most often 0.5% to 2% (typically 1%) of the volume of the reinforced alloy.
- the nanoparticles are dispersed in the reinforced alloy to a depth that may be between 30 ⁇ m and 1 mm, preferably between 50 ⁇ m and 500 ⁇ m, more preferably between 50 ⁇ m and 100 ⁇ m.
- At least 80% of the nanoparticles have an average size of 1 nm to 50 nm, preferably at least 90% a average size of 1 nm to 10 nm, even more preferably at least 95% an average size of 0.5 nm to 5 nm.
- the average size of the nanoparticles can be modulated by varying parameters such as the plasma nitriding temperature, the diffusion temperature, and / or the pressure of the gaseous medium.
- the term "average size" means the mean value of the diameter of the nanoparticles when they are substantially spherical, or the average value of their main dimensions when they are not substantially spherical.
- the quantity of nanoparticles (at least 80%) having a determined average size can be easily counted using a technique known to those skilled in the art such as Transmission Electron Microscopy (TEM).
- TEM Transmission Electron Microscopy
- the nanoparticles generally have a composition such that they comprise in atomic percentage of 30% to 70% of nitrogen, combined in the form of nitride with at least one metal element M. This quantity is conditioned by the quantity of interstitial nitrogen introduced into the base alloy, knowing that generally all of the interstitial nitrogen combines with the metal element M.
- the carbon element When the carbon element is additionally present in the gaseous medium in the form of carbon species, all or part of this element can be combined directly with the metal element M and optionally with nitrogen during the plasma nitriding. We then obtain nanoparticles in which the nitride is wholly or partly in the form of carbonitride of the metal element M.
- the nitride or carbonitride of the metal element M formed does not necessarily have a defined stoichiometry.
- These species are most often represented by the formula M (N) or M (C, N), or alternatively the formula M x C y N z in which the indices "x", "y” and “z” indicate respectively the relative atomic proportion of the elements M, C and N within the nitride or carbonitride formed.
- the nitride of a metal element M may, however, comprise one or more nitrides of defined stoichiometry which may optionally coexist within the nanoparticles.
- titanium nitride may be present in a nanoparticle in the form TiN and / or Ti 3 N 4 .
- the nitride present in the nanoparticles thus belongs to the group consisting of TiN, Ti 3 N 4 , ZrN, HfN and TaN.
- nanoparticles may also include other species that were initially present in the powders or that formed during the manufacturing process of the invention.
- the manufacturing method of the invention may comprise a consolidation step by hot spinning carried out during (optionally instead) or after step c) precipitation of the nitride, preferably at a temperature of less than or equal to 850 ° C, preferably at a temperature of 600 ° C to 850 ° C.
- This hot-spinning step is preferably carried out when the base alloy is in the form of a powder.
- the Figure 1 represents a MET plate of a reinforced alloy obtained by the manufacturing method of the invention.
- a ferritic powder composed of Fe-18Cr-1W-0.8Ti base alloy is nitrided using the manufacturing method of the invention.
- This powder has a particle size such that the average size of its grains is 100 microns.
- Consolidation is then carried out by hot spinning at 850 ° C for 1 hour, during which the titanium nitride precipitates.
- a sample taken from the core of the obtained reinforced alloy is examined by TEM.
- the picture obtained represented on the Figure 1 shows the presence of numerous particles comprising titanium nitride of average size between 2 nm and 8 nm.
Description
La présente invention concerne un procédé de fabrication d'un alliage renforcé. Elle concerne plus particulièrement un procédé de fabrication d'un alliage renforcé par des nanoparticules de nitrure métallique.The present invention relates to a method of manufacturing a reinforced alloy. It relates more particularly to a process for manufacturing an alloy reinforced with nanoparticles of metal nitride.
Les alliages renforcés par des particules de nitrure (dits alliages « NDS » pour « Nitride Dispersion Strenghtened ») présentent des propriétés mécaniques améliorées par rapport aux alliages maître, notamment une meilleure résistance mécanique en traction, en fluage, en compression ou en fatigue.The alloys reinforced with nitride particles (so-called "NDS" alloys for "Nitride Dispersion Strenghtened") have improved mechanical properties compared to master alloys, including better tensile strength, creep, compression or fatigue.
Ces propriétés peuvent encore être améliorées en diminuant la taille des particules dispersées.These properties can be further improved by decreasing the size of the dispersed particles.
De nombreuses études visent ainsi à mettre au point un procédé de fabrication d'un alliage NDS avec des particules de taille réduite.Many studies aim to develop a process for manufacturing an NDS alloy with small particles.
Parmi ces procédés, la nitruration gazeuse est couramment employée. Le document «
Le traitement thermique complémentaire de ce procédé de nitruration a néanmoins pour inconvénient de produire des dispersions d'une taille moyenne pouvant atteindre 300 nm. Cette taille importante des dispersions a tendance à dégrader les propriétés mécaniques de l'alliage renforcé.The additional heat treatment of this nitriding process nevertheless has the disadvantage of producing dispersions with an average size of up to 300 nm. This large size of the dispersions tends to degrade the mechanical properties of the reinforced alloy.
Un autre type de procédé utilisé pour fabriquer un alliage NDS fait intervenir la métallurgie des poudres. Dans le document
Le traitement thermique destiné à produire du diazote par décomposition du donneur d'azote fait que ce procédé de métallurgie des poudres peut s'apparenter à un procédé de nitruration.The heat treatment for producing nitrogen by decomposition of the nitrogen donor results in this powder metallurgy process being similar to a nitriding process.
La nécessité de disposer d'un nitrure intermédiaire tel que Cr2N avant de former le nitrure métallique final, a donc là encore un effet défavorable sur la taille des nanoparticules dispersées qui est tout au mieux de l'ordre du micromètre.The need to have an intermediate nitride such as Cr 2 N before forming the final metal nitride, therefore again has an adverse effect on the size of the nanoparticles dispersed which is at best of the order of a micrometer.
Les procédés de l'état de la technique précités ont donc notamment pour inconvénient qu'ils ne permettent pas de fabriquer un alliage renforcé dans lequel les nanoparticules ont pour l'essentiel une taille moyenne réduite, typiquement inférieure à 50nm.The processes of the state of the art cited above therefore have the disadvantage that they do not make it possible to manufacture a reinforced alloy in which the nanoparticles have essentially a reduced average size, typically less than 50 nm.
De plus, la nécessité de passer par un nitrure intermédiaire fait que ces procédés sont sujets à des réactions parasites qui rendent difficile le contrôle de la composition et de la quantité des particules qui sont présentes dans l'alliage renforcé obtenu.In addition, the need to pass through an intermediate nitride means that these processes are subject to parasitic reactions that make it difficult to control the composition and the amount of particles that are present in the obtained reinforced alloy.
Un des buts de l'invention est donc de réaliser un procédé de fabrication d'un alliage « NDS » comprenant des nanoparticules dont au moins 80% présentent une taille moyenne inférieure à 50 nm, un tel procédé pouvant permettre un meilleur contrôle de la composition et de la quantité de ces nanoparticules au sein de l'alliage.One of the aims of the invention is therefore to provide a process for manufacturing an "NDS" alloy comprising nanoparticles of which at least 80% have an average size of less than 50 nm, such a method that may allow better control of the composition. and the amount of these nanoparticles within the alloy.
La présente invention concerne ainsi un procédé de fabrication d'un alliage renforcé comportant une matrice métallique dans le volume de laquelle sont dispersées des nanoparticules, dont au moins 80% présentent une taille moyenne de 1 nm à 50 nm, les nanoparticules comprenant au moins un nitrure choisi parmi les nitrures d'au moins un élément métallique M appartenant au groupe consistant en Ti, Zr, Hf, et Ta.The present invention thus relates to a method for manufacturing a reinforced alloy comprising a metal matrix in the volume of which nanoparticles are dispersed, of which at least 80% have an average size of 1 nm to 50 nm, the nanoparticles comprising at least one nitride selected from nitrides of at least one metal element M belonging to the group consisting of Ti, Zr, Hf, and Ta.
Ce procédé comprend les étapes successives suivantes :
- a) on réalise à une température de 200°C à 700°C une nitruration par plasma d'un alliage de base afin d'y insérer de l'azote interstitiel, l'alliage de base incorporant 0,1% à 1% en poids de l'élément métallique M et étant choisi parmi un alliage austénitique, ferritique, ferritique-martensitique ou à base nickel ;
- b) on diffuse à une température de 350°C à 650°C l'azote interstitiel au sein de l'alliage de base ; et
- c) on précipite le nitrure à une température de 600°C à 900°C pendant une durée de 10 minutes à 10 heures, afin de former les nanoparticules dispersées dans l'alliage renforcé.
- a) a plasma nitriding of a base alloy is carried out at a temperature of 200 ° C. to 700 ° C. in order to insert interstitial nitrogen, the base alloy incorporating 0.1% to 1% by weight; weight of the metal element M and being chosen from an austenitic, ferritic, ferritic-martensitic or nickel-based alloy;
- b) diffusing at 350 ° C to 650 ° C the interstitial nitrogen within the base alloy; and
- c) the nitride is precipitated at a temperature of 600 ° C to 900 ° C for a period of 10 minutes to 10 hours, in order to to form the nanoparticles dispersed in the reinforced alloy.
Avantageusement, le procédé de l'invention ne comporte pas la mise en oeuvre d'un nitrure intermédiaire destiné à former le nitrure métallique constituant tout ou partie des nanoparticules dispersées.Advantageously, the process of the invention does not involve the use of an intermediate nitride intended to form the metal nitride constituting all or part of the dispersed nanoparticles.
Ceci est rendu possible grâce au procédé de fabrication de l'invention qui comprend des étapes séparées.This is made possible by the manufacturing method of the invention which comprises separate steps.
Ainsi, lors de l'étape de nitruration par plasma suivie de l'étape de diffusion, l'azote destiné à former le nitrure est introduit dans l'alliage de base sous forme interstitielle, à savoir en, tant qu'azote en solution solide dans l'alliage de base, et non sous forme moléculaire N2.Thus, during the plasma nitriding step followed by the diffusion step, the nitrogen intended to form the nitride is introduced into the base alloy in interstitial form, namely as nitrogen in solid solution. in the base alloy, and not in molecular form N 2 .
De par son affinité chimique préférentielle avec l'élément métallique M, l'azote interstitiel se combine alors directement avec tout ou partie de cet élément, sous l'influence de la température de diffusion et/ou de précipitation (généralement sous l'influence d'une température comprise entre 500 °C et 650 °C), afin de former le nitrure. Le cas échéant, notamment pour une température dans une plage commune comprise entre 600 °C et 650 °C, l'étape de diffusion et de précipitation peuvent donc se recouvrir en tout ou partie.By its preferential chemical affinity with the metallic element M, the interstitial nitrogen then combines directly with all or part of this element, under the influence of the diffusion and / or precipitation temperature (generally under the influence of a temperature of between 500 ° C and 650 ° C) to form the nitride. Where appropriate, especially for a temperature in a common range of between 600 ° C. and 650 ° C., the diffusion and precipitation step may therefore be totally or partially overlapping.
Au cours de l'étape c), on précipite le nitrure par un phénomène de germination-croissance afin de former les nanoparticules dispersées dans l'alliage renforcé.During step c), the nitride is precipitated by a germination-growth phenomenon in order to form the nanoparticles dispersed in the reinforced alloy.
Dans le cadre de l'invention, le passage par un nitrure intermédiaire n'est donc pas nécessaire, contrairement aux procédés de l'état de la technique qui nécessitent un traitement thermique complémentaire généralement pratiqué à une température d'environ 1200°C afin de dissocier un nitrure tel que Cr2N.In the context of the invention, the passage through an intermediate nitride is therefore not necessary, unlike the processes of the state of the art that require a complementary heat treatment generally performed at a temperature of about 1200 ° C in order to dissociate a nitride such as Cr 2 N.
Un autre avantage du procédé de fabrication de l'invention est que la température appliquée lors de ses différentes étapes peut être choisie avec une grande liberté.Another advantage of the manufacturing method of the invention is that the temperature applied during its different stages can be chosen with great freedom.
Ainsi, l'étape a) de nitruration plasma est réalisée à une température de 200°C à 700°C, préférentiellement 200°C à 600°C, encore plus préférentiellement de 350°C à 450°C.Thus, the plasma nitriding step a) is carried out at a temperature of 200 ° C. to 700 ° C., preferably 200 ° C. to 600 ° C., even more preferentially from 350 ° C. to 450 ° C.
L'étape b) de diffusion de l'azote interstitiel est quant à elle réalisée à une température de 350°C à 650°C, préférentiellement de 350°C à 500°C. Sa durée est généralement de 5 heures à 500 heures, préférentiellement de 10 heures à 200 heures. Elle est généralement inversement proportionnelle à la température de l'étape de diffusion de l'azote interstitiel.Step b) of diffusion of the interstitial nitrogen is carried out at a temperature of 350 ° C to 650 ° C, preferably 350 ° C to 500 ° C. Its duration is generally from 5 hours to 500 hours, preferably from 10 hours to 200 hours. It is generally inversely proportional to the temperature of the interstitial nitrogen diffusion step.
Une fois l'azote diffusé sous forme interstitielle dans l'alliage de base, la température de précipitation peut avantageusement être choisie pour contrôler la taille du nitrure de l'élément métallique M au détriment de la précipitation d'un élément métallique M' tel que Cr dont la dissolution du nitrure associé Cr2N ne peut s'opérer qu'à une température voisine de 1100°C.Once the nitrogen diffuses interstitial form in the base alloy, the precipitation temperature can advantageously be chosen to control the size of the nitride of the metal element M at the expense of the precipitation of a metal element M 'such that Cr whose dissolution of the associated nitride Cr 2 N can only occur at a temperature of 1100 ° C.
Après combinaison directe de l'azote interstitiel avec tout ou partie de l'élément métallique M afin de former le nitrure, l'étape c) de précipitation du nitrure est réalisée à une température qui est de 600°C à 900°C, préférentiellement de 600°C à 800°C, encore plus préférentiellement de 600°C à 700°C. Sa durée est de 10 minutes à 10 heures, préférentiellement de 30 minutes à 2 heures. Elle est généralement inversement proportionnelle à la température de l'étape de précipitation du nitrure.After direct combination of the interstitial nitrogen with all or part of the metal element M in order to form the nitride, the nitride precipitation step c) is carried out at a temperature which is from 600 ° C. to 900 ° C., preferentially from 600 ° C to 800 ° C, even more preferably from 600 ° C to 700 ° C. Its duration is 10 minutes to 10 hours, preferably 30 minutes to 2 hours. It is generally inversely proportional to the temperature of the nitride precipitation step.
Un tel choix de température n'est pas accessible aux procédés de l'état de la technique car la réactivité du milieu de nitruration leur impose une température de mise en oeuvre qui est plus élevée et/ou de choix plus restreint.Such a choice of temperature is not accessible to the processes of the state of the art because the reactivity of the nitriding medium imposes on them a processing temperature which is higher and / or of more limited choice.
L'absence de nitrure intermédiaire et/ou la liberté de choix dans la température de mise en oeuvre du procédé de l'invention font que ce procédé permet d'obtenir un alliage renforcé dont la matrice comprend des nanoparticules dispersées de taille moyenne plus réduite que celles obtenues par les procédés de l'état de la technique précités.The absence of intermediate nitride and / or the freedom of choice in the temperature of implementation of the process of According to the invention, this method makes it possible to obtain a reinforced alloy whose matrix comprises dispersed nanoparticles of smaller average size than those obtained by the processes of the state of the art mentioned above.
Dans la présente description, le verbe « comprendre », « comporter », « incorporer », « inclure » et ses formes conjuguées sont des termes ouverts et n'excluent donc pas la présence d'élément(s) et/ou étape(s) additionnels s'ajoutant aux élément(s) et/ou étape(s) initiaux énoncés après ces termes. Toutefois, ces termes ouverts visent en outre un mode de réalisation particulier dans lequel seul(s) le (s) élément(s) et/ou étape(s) initiaux, à l'exclusion de tout autre, sont visés ; auquel cas le terme ouvert vise en outre le terme fermé « consister en », « constituer de » et ses formes conjuguées.In the present description, the verb "to understand", "to include", "to incorporate", "to include" and its conjugate forms are open terms and thus do not exclude the presence of element (s) and / or step (s). ) additional to the element (s) and / or initial stage (s) set out after these terms. However, these open terms also include a particular embodiment in which only the element (s) and / or initial stage (s), to the exclusion of all others, are targeted; in which case the term open also refers to the closed term "consist of", "constitute of" and its conjugated forms.
L'usage de l'article indéfini « un » ou « une » pour un élément ou une étape n'exclut pas, sauf mention contraire, la présence d'une pluralité d'éléments ou étapes.The use of the undefined article "a" or "an" for an element or a step does not exclude, unless otherwise stated, the presence of a plurality of elements or steps.
Sauf indication contraire, la composition chimique de l'alliage de base, de l'alliage renforcé ou de la matrice métallique et des nanoparticules qu'il contient est exprimée dans la présente description en pourcentage en poids par rapport au poids de l'alliage considéré.Unless otherwise indicated, the chemical composition of the base alloy, the reinforced alloy or the metal matrix and the nanoparticles it contains is expressed in the present description as a percentage by weight relative to the weight of the alloy considered. .
L'étape a) du procédé de fabrication de l'invention consiste en une nitruration par plasma telle qu'elle est connue de l'homme du métier, décrite par exemple dans le document « Techniques de l'ingénieur, référence M 1227, "Nitruration, nitrocarburation et dérivés", chapitre 4 ».Step a) of the manufacturing method of the invention consists of a plasma nitriding as known to those skilled in the art, described for example in the document "Techniques de l'ingénieur, reference M 1227," Nitriding, nitrocarburizing and derivatives ", Chapter 4".
Elle comprend principalement la formation d'un plasma en imposant une différence de potentiel entre une anode et une cathode dans un milieu gazeux comprenant de l'azote, de telle sorte que des espèces réactives sont produites. Les espèces réactives peuvent comprendre des espèces neutres (N atomique), voire ionisées ou excitées (telles que par exemple N+ ou N2 vibrationnellement excité), la nitruration étant alors dite ionique dans ce dernier cas. A l'aide de traitements thermiques appropriés, ces espèces diffusent sous forme interstitielle dans l'alliage de base pour former ensuite un nitrure avec les atomes constitutifs de cet alliage.It mainly comprises the formation of a plasma by imposing a potential difference between an anode and a cathode in a gaseous medium comprising nitrogen, so that reactive species are produced. The reactive species can comprise neutral (atomic N) species, or even ionized or excited (such as for example N + or N 2 vibrationnally excited), the nitriding then being called ionic in the latter case. Using appropriate heat treatments, these species diffuse interstitial form in the base alloy to then form a nitride with the constituent atoms of this alloy.
Selon l'invention, la nitruration par plasma est réalisée sur un alliage de base incorporant 0,1% à 1% en poids d'au moins un élément métallique M choisi parmi Ti, Zr, Hf, ou Ta, de préférence 0,5% à 1% en poids de cet élément.According to the invention, the plasma nitriding is performed on a base alloy incorporating 0.1% to 1% by weight of at least one metal element M selected from Ti, Zr, Hf, or Ta, preferably 0.5 % to 1% by weight of this element.
Préférentiellement, l'élément métallique M est le titane.Preferably, the metal element M is titanium.
L'alliage de base peut se présenter sous forme de poudre ou de pièce.The base alloy can be in the form of powder or part.
Il est choisi parmi un alliage austénitique, ferritique, ferritique-martensitique ou à base nickel.It is selected from an austenitic, ferritic, ferritic-martensitic or nickel-based alloy.
La nitruration par plasma peut être réalisée à l'aide d'un milieu gazeux comprenant de l'azote (sous forme d'azote moléculaire (N2) et/ou en tant que composé azoté gazeux tel que par exemple NH3 et/ou N2H2). L'azote est dilué dans un gaz inerte chimiquement (vis-à-vis des autres constituants du milieu gazeux), tel que par exemple H2.Plasma nitriding can be carried out using a gaseous medium comprising nitrogen (in the form of molecular nitrogen (N 2 ) and / or as a gaseous nitrogen compound such as, for example, NH 3 and / or N 2 H 2 ). The nitrogen is diluted in a chemically inert gas (vis-à-vis the other constituents of the gaseous medium), such as, for example, H 2 .
Le milieu gazeux peut en outre comprendre une espèce carbonée, telle que par exemple CH4.The gaseous medium may further comprise a carbon species, such as for example CH 4 .
Le milieu gazeux peut par exemple comprendre 20% à 30% en volume de N2 et/ou de composé azoté gazeux, éventuellement additionné de 5% à 20% en volume de l'espèce carbonée (par exemple CH4), le reste étant constitué par le gaz inerte chimiquement (par exemple H2).The gaseous medium may for example comprise 20% to 30% by volume of N 2 and / or of gaseous nitrogen compound, optionally supplemented with 5% to 20% by volume of the carbon species (for example CH 4 ), the rest being constituted by the chemically inert gas (for example H 2 ).
La pression du milieu gazeux est généralement inférieure à la pression atmosphérique, par exemple de 1 mbar à 100 mbar, préférentiellement de 1 mbar à 10 mbar, encore plus préférentiellement de 1,5 mbar à 5 mbar.The pressure of the gaseous medium is generally less than atmospheric pressure, for example from 1 mbar to 100 mbar, preferably from 1 mbar to 10 mbar, still more preferably from 1.5 mbar to 5 mbar.
La nitruration plasma est généralement réalisée pendant une durée de 5 heures à 300 heures, préférentiellement de 10 heures à 200 heures, encore plus préférentiellement de 24 heures à 100 heures.Plasma nitriding is generally carried out for a period of 5 hours to 300 hours, preferably from 10 hours to 200 hours, even more preferably from 24 hours to 100 hours.
De préférence, après l'étape de diffusion de l'azote, l'alliage de base comprend 1000 ppm à 2000 ppm en poids d'azote sous forme interstitielle, ce qui permet la formation préférentielle d'un nitrure de l'élément métallique M au détriment d'autres nitrures tels que Cr2N.Preferably, after the nitrogen diffusion step, the base alloy comprises 1000 ppm to 2000 ppm by weight of nitrogen in interstitial form, which allows the preferential formation of a nitride of the metal element M at the expense of other nitrides such as Cr 2 N.
A l'issue du procédé de fabrication de l'invention, l'alliage renforcé obtenu comprend une matrice métallique dans laquelle sont dispersées des nanoparticules composées en tout ou partie d'au moins un nitrure métallique.At the end of the manufacturing process of the invention, the reinforced alloy obtained comprises a metal matrix in which nanoparticles composed entirely or partially of at least one metal nitride are dispersed.
La matrice métallique de l'alliage renforcé a la composition chimique de l'alliage de base.The metal matrix of the reinforced alloy has the chemical composition of the base alloy.
Le procédé de fabrication de l'invention permet également de préserver la structure de l'alliage de base (structure austénitique, ferritique ou ferritique-martensitique) dans l'alliage renforcé.The manufacturing method of the invention also makes it possible to preserve the structure of the base alloy (austenitic, ferritic or ferritic-martensitic structure) in the reinforced alloy.
Les nanoparticules sont dispersées dans tout ou partie du volume de l'alliage renforcé. Elles représentent le plus souvent 0,5% à 2% (typiquement 1%) du volume de l'alliage renforcé.The nanoparticles are dispersed in all or part of the volume of the reinforced alloy. They represent most often 0.5% to 2% (typically 1%) of the volume of the reinforced alloy.
Lorsque l'alliage de base se présente sous forme de pièce, les nanoparticules sont dispersées dans l'alliage renforcé sur une profondeur pouvant être comprise entre 30 µm et 1 mm, préférentiellement entre 50 µm et 500 µm, encore plus préférentiellement entre 50 µm et 100 µm.When the base alloy is in the form of a workpiece, the nanoparticles are dispersed in the reinforced alloy to a depth that may be between 30 μm and 1 mm, preferably between 50 μm and 500 μm, more preferably between 50 μm and 100 μm.
Au moins 80% des nanoparticules présentent une taille moyenne de 1 nm à 50 nm, préférentiellement au moins 90% une taille moyenne de 1 nm à 10 nm, encore plus préférentiellement au moins 95% une taille moyenne de 0,5 nm à 5 nm.At least 80% of the nanoparticles have an average size of 1 nm to 50 nm, preferably at least 90% a average size of 1 nm to 10 nm, even more preferably at least 95% an average size of 0.5 nm to 5 nm.
Afin d'obtenir une telle réduction de taille, la taille moyenne des nanoparticules peut être modulée en faisant varier des paramètres tels que la température de nitruration plasma, la température de diffusion, et/ou la pression du milieu gazeux.In order to obtain such a reduction in size, the average size of the nanoparticles can be modulated by varying parameters such as the plasma nitriding temperature, the diffusion temperature, and / or the pressure of the gaseous medium.
Elle peut également être réduite en diminuant la température et/ou la durée de l'étape c) de précipitation, qui sont par exemple de 850°C pendant 1 heure.It can also be reduced by decreasing the temperature and / or the duration of the precipitation step c), which are, for example, 850 ° C. for 1 hour.
Au sens de l'invention, on entend par « taille moyenne » la valeur moyenne du diamètre des nanoparticules lorsqu'elles sont substantiellement sphériques, ou la valeur moyenne de leurs dimensions principales lorsqu'elles ne sont pas substantiellement sphériques.For the purposes of the invention, the term "average size" means the mean value of the diameter of the nanoparticles when they are substantially spherical, or the average value of their main dimensions when they are not substantially spherical.
La quantité de nanoparticules (au moins 80%) présentant une taille moyenne déterminée peut être aisément dénombrée à l'aide d'une technique connue de l'homme du métier telle que la Microscopie Electronique en Transmission (MET).The quantity of nanoparticles (at least 80%) having a determined average size can be easily counted using a technique known to those skilled in the art such as Transmission Electron Microscopy (TEM).
Les nanoparticules ont généralement une composition telle qu'elles comprennent en pourcentage atomique de 30% à 70% d'azote, combiné sous forme de nitrure avec au moins un élément métallique M. Cette quantité est conditionnée par la quantité d'azote interstitiel introduite dans l'alliage de base, sachant que généralement la totalité de l'azote interstitiel se combine avec l'élément métallique M.The nanoparticles generally have a composition such that they comprise in atomic percentage of 30% to 70% of nitrogen, combined in the form of nitride with at least one metal element M. This quantity is conditioned by the quantity of interstitial nitrogen introduced into the base alloy, knowing that generally all of the interstitial nitrogen combines with the metal element M.
Lorsque l'élément carbone est en outre présent dans le milieu gazeux sous forme d'espèce carbonée, tout ou partie de cet élément peut se combiner directement avec l'élément métallique M et éventuellement l'azote au cours de la nitruration par plasma. On obtient alors des nanoparticules dans lesquelles le nitrure se présente en tout ou partie sous forme de carbonitrure de l'élément métallique M.When the carbon element is additionally present in the gaseous medium in the form of carbon species, all or part of this element can be combined directly with the metal element M and optionally with nitrogen during the plasma nitriding. We then obtain nanoparticles in which the nitride is wholly or partly in the form of carbonitride of the metal element M.
Comme cela est connu de l'homme du métier dans le domaine de la métallurgie, le nitrure ou le carbonitrure de l'élément métallique M formé ne présente pas forcément une stoechiométrie définie. Ces espèces sont le plus souvent représentées par la formule M(N) ou M(C,N), ou à titre alternatif la formule MxCyNz dans lequel les indices « x », « y » et « z » indiquent respectivement la proportion atomique relative des éléments M, C et N au sein du nitrure ou carbonitrure formé.As is known to those skilled in the field of metallurgy, the nitride or carbonitride of the metal element M formed does not necessarily have a defined stoichiometry. These species are most often represented by the formula M (N) or M (C, N), or alternatively the formula M x C y N z in which the indices "x", "y" and "z" indicate respectively the relative atomic proportion of the elements M, C and N within the nitride or carbonitride formed.
Le nitrure d'un élément métallique M peut toutefois comprendre un ou plusieurs nitrures de stoechiométrie définie qui peuvent le cas échéant coexister au sein des nanoparticules. Par exemple, le nitrure de titane peut être présent dans une nanoparticule sous la forme TiN et/ou Ti3N4.The nitride of a metal element M may, however, comprise one or more nitrides of defined stoichiometry which may optionally coexist within the nanoparticles. For example, titanium nitride may be present in a nanoparticle in the form TiN and / or Ti 3 N 4 .
De préférence, le nitrure présent dans les nanoparticules appartient ainsi au groupe constitué de TiN, Ti3N4, ZrN, HfN et TaN.Preferably, the nitride present in the nanoparticles thus belongs to the group consisting of TiN, Ti 3 N 4 , ZrN, HfN and TaN.
Bien entendu, les nanoparticules peuvent également comprendre d'autres espèces qui étaient initialement présentes dans les poudres ou qui se sont formées au cours du procédé de fabrication de l'invention.Of course, the nanoparticles may also include other species that were initially present in the powders or that formed during the manufacturing process of the invention.
L'alliage renforcé peut en outre comprendre en poids au moins un des éléments suivants (parfois en tant qu'impureté inévitable de fabrication) :
- de 10 à 120ppm de silicium ;
- de 10 à 100ppm de soufre ;
- moins de 20ppm de chlore ;
- de 2 à 10ppm de phosphore ;
- de 0,1 à 10ppm de bore ;
- de 0,1 à 10ppm de calcium ;
- moins de 0,1ppm de chacun des éléments suivants : lithium, fluor, métaux lourds, Sn, As, Sb.
- from 10 to 120 ppm of silicon;
- from 10 to 100 ppm sulfur;
- less than 20ppm of chlorine;
- from 2 to 10 ppm of phosphorus;
- 0.1 to 10 ppm boron;
- from 0.1 to 10 ppm of calcium;
- less than 0.1 ppm of each of the following: lithium, fluorine, heavy metals, Sn, As, Sb.
Le procédé de fabrication de l'invention peut comprendre une étape de consolidation par filage à chaud réalisée au cours (éventuellement à la place) ou après l'étape c) de précipitation du nitrure, de préférence à une température inférieure ou égale à 850°C, préférentiellement à une température de 600°C à 850°C. Cette étape de filage à chaud est de préférence mise en oeuvre lorsque l'alliage de base se présente sous forme de poudre.The manufacturing method of the invention may comprise a consolidation step by hot spinning carried out during (optionally instead) or after step c) precipitation of the nitride, preferably at a temperature of less than or equal to 850 ° C, preferably at a temperature of 600 ° C to 850 ° C. This hot-spinning step is preferably carried out when the base alloy is in the form of a powder.
D'autres objets, caractéristiques et avantages de l'invention vont maintenant être précisées dans la description qui suit d'un mode de réalisation particulier de l'invention, donné à titre illustratif et non limitatif, en référence à la
La
Une poudre ferritique composée d'un alliage de base Fe-18Cr-1W-0,8Ti est nitrurée à l'aide du procédé de fabrication de l'invention.A ferritic powder composed of Fe-18Cr-1W-0.8Ti base alloy is nitrided using the manufacturing method of the invention.
Cette poudre a une granulométrie telle que la taille moyenne de ses grains est de 100 µm.This powder has a particle size such that the average size of its grains is 100 microns.
Les conditions de mise en oeuvre du procédé sont les suivantes :
- brassage de la poudre ;
- milieu gazeux constitué en volume de 71% H2, 23% N2 et 6% CH4 ;
- pression du milieu gazeux de 2,5 mbar ;
- cycle de 15 heures de nitruration plasma réalisé à 380°C, suivi par un traitement thermique de diffusion réalisé à une température de 400°C pendant 200 heures.
- brewing the powder;
- a gaseous medium consisting in volume of 71% H 2 , 23% N 2 and 6% CH 4 ;
- pressure of the gaseous medium of 2.5 mbar;
- 15 hour cycle of plasma nitriding performed at 380 ° C., followed by a diffusion heat treatment carried out at a temperature of 400 ° C. for 200 hours.
Une analyse par MET de la poudre obtenue montre l'absence de précipitation de nitrure.TEM analysis of the powder obtained shows the absence of nitride precipitation.
Une consolidation est ensuite réalisée à l'aide d'un filage à chaud à 850°C pendant 1 heure, au cours duquel le nitrure de titane précipite.Consolidation is then carried out by hot spinning at 850 ° C for 1 hour, during which the titanium nitride precipitates.
Un échantillon prélevé au coeur de l'alliage renforcé obtenu est examiné par MET. Le cliché obtenu représenté sur la
Claims (23)
- Manufacturing method of a strengthened alloy comprising a metal matrix in the volume of which nanoparticles are dispersed, of which at least 80% have an average size of 1 nm to 50 nm, said nanoparticles comprising at least one nitride chosen from the nitrides of at least one metal element M belonging to the group consisting of Ti, Zr, Hf and Ta,
the method comprising the following successive steps:a) performing plasma nitriding of a base alloy at a temperature of 200°C to 700°C in order to insert interstitial nitrogen therein, said base alloy incorporating 0.1 % to 1% by weight of the metal element M and being chosen from an austenitic, ferritic, ferritic-martensitic or nickel-based alloy;b) diffusing the interstitial nitrogen in said base alloy at a temperature of 350°C to 650°C; andc) precipitating the nitride at a temperature of 600°C to 900°C for a period of 10 minutes to 10 hours, in order to form said nanoparticles dispersed in the strengthened alloy. - Manufacturing method according to claim 1, wherein plasma nitriding is performed according to step (a) at a temperature of 200°C to 600°C.
- Manufacturing method according to claim 1 or 2, wherein the interstitial nitrogen is diffused according to step (b) at a temperature of 350°C to 500°C.
- Manufacturing method according to any one of the preceding claims, wherein the nitride is precipitated according to step (c) at a temperature of 600°C to 800°C.
- Manufacturing method according to any one of the preceding claims, wherein:- plasma nitriding is performed according to step (a) at a temperature of 200°C to 600°C;- the interstitial nitrogen is diffused according to step (b) at a temperature of 350°C to 500°C; and- the nitride is precipitated according to step (c) at a temperature of 600°C to 800°C.
- Manufacturing method according to any one of claims 2 to 5, wherein plasma nitriding is performed according to step (a) at a temperature of 350°C to 450°C.
- Manufacturing method according to any one of the preceding claims, wherein the interstitial nitrogen is diffused according to step (b) for a duration from 5 hours to 500 hours.
- Manufacturing method according to any one of claims 4 to 7, wherein the nitride is precipitated according to step (c) at a temperature of 600°C to 700°C.
- Manufacturing method according to any one of the preceding claims, wherein said base alloy incorporates 0.5% to 1% by weight of the metal element M.
- Manufacturing method according to any one of the preceding claims, wherein the metal element M is titanium.
- Manufacturing method according to any one of the preceding claims, wherein the plasma nitriding is performed by means of a gaseous medium comprising nitrogen in the form of molecular nitrogen (N2) and/or as a gaseous nitrogenous compound.
- Manufacturing method according to claim 11, wherein the gaseous nitrogenous compound is NH3 and/or N2H2.
- Manufacturing method according to claim 11 or 12, wherein the gaseous medium comprises 20% to 30% by volume of N2 and/or of the gaseous nitrogenous compound, the remainder consisting of the chemically inert gas.
- Manufacturing method according to any one of the claims 11 to 13, wherein the gaseous medium also comprises a carbonaceous species.
- Manufacturing method according to claim 14, wherein the carbonaceous species is CH4.
- Manufacturing method according to claim 14 or 15, wherein the gaseous medium comprises 20% to 30% by volume of N2 and/or of the gaseous nitrogenous compound, with the carbonaceous species added to the extent of 5% to 20% by volume, the remainder consisting of the chemically inert gas.
- Manufacturing method according to any one of the preceding claims, wherein the nitride belongs to the group consisting of TiN, Ti3N4, ZrN, HfN and TaN.
- Manufacturing method according to any one of the preceding claims, wherein the nitride is wholly or partly in the form of carbonitride of the metal element M.
- Manufacturing method according to any one of the preceding claims, wherein at least 90% of said nanoparticles have an average size of 1 nm to 10 nm.
- Manufacturing method according to any one of the preceding claims, wherein the strengthened alloy also comprises by weight at least one of the following elements:- from 10 to 120 ppm of silicon;- from 10 to 100 ppm of sulfur;- less than 20 ppm of chlorine;- from 2 to 10 ppm of phosphorus;- from 0.1 to 10 ppm of boron;- from 0.1 to 10 ppm of calcium;- less than 0.1 ppm of each of the following elements: lithium, fluorine, heavy metals, Sn, As, Sb.
- Manufacturing method according to any one of the preceding claims, comprising a step of consolidation by hot extrusion performed during or after the step c) precipitating the nitride.
- Manufacturing method according to claim 21, wherein the hot extrusion step is performed at a temperature of less than or equal to 850°C.
- Manufacturing method according to any one of the preceding claims, wherein the nanoparticles represent 0.5% to 2% of the volume of the strengthened alloy.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR1061243A FR2969662B1 (en) | 2010-12-24 | 2010-12-24 | PROCESS FOR MANUFACTURING PLASMA NITRURATION REINFORCED ALLOY |
PCT/FR2011/053175 WO2012085489A1 (en) | 2010-12-24 | 2011-12-22 | Process for manufacturing a reinforced alloy by plasma nitriding |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2655684A1 EP2655684A1 (en) | 2013-10-30 |
EP2655684B1 true EP2655684B1 (en) | 2016-03-02 |
Family
ID=44194161
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP11815535.7A Not-in-force EP2655684B1 (en) | 2010-12-24 | 2011-12-22 | Method for reinforcing an alloy by plasma-nitriding |
Country Status (9)
Country | Link |
---|---|
US (1) | US8999228B2 (en) |
EP (1) | EP2655684B1 (en) |
JP (1) | JP5878932B2 (en) |
KR (1) | KR101506103B1 (en) |
CN (1) | CN103282537B (en) |
ES (1) | ES2572642T3 (en) |
FR (1) | FR2969662B1 (en) |
RU (1) | RU2569438C2 (en) |
WO (1) | WO2012085489A1 (en) |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR101673695B1 (en) * | 2014-11-12 | 2016-11-08 | 국민대학교산학협력단 | Austenitic steel matrix-nano particle composite and preparing method of the same |
CN107737932B (en) * | 2017-10-26 | 2019-08-06 | 西北工业大学 | A kind of integrated laser increasing material manufacturing method that titanium or titanium alloy constituency are strengthened |
CN108103432B (en) * | 2017-12-25 | 2020-01-17 | 哈尔滨汽轮机厂有限责任公司 | Nitriding method of nickel-based high-temperature alloy |
TWI675938B (en) * | 2019-01-25 | 2019-11-01 | 友鋮股份有限公司 | Three-stage surface modified stainless steel material and manufacturing method thereof |
AU2020228291A1 (en) * | 2019-02-26 | 2021-10-07 | Somnio Global Holdings, Llc | High nitrogen steel powder and methods of making the same |
CN111304483B (en) * | 2020-03-18 | 2021-07-06 | 深圳市联合蓝海科技开发有限公司 | Pure gold and preparation method and application thereof |
Family Cites Families (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4921531A (en) * | 1984-10-19 | 1990-05-01 | Martin Marietta Corporation | Process for forming fine ceramic powders |
GB2183676B (en) * | 1985-11-28 | 1989-11-22 | Atomic Energy Authority Uk | Production of nitride dispersion strengthened alloys |
JPS63227790A (en) * | 1987-03-16 | 1988-09-22 | N T T Gijutsu Iten Kk | High strength stainless steel and its production |
SE503520C2 (en) * | 1989-11-15 | 1996-07-01 | Sandvik Ab | Cut of pressed and sintered titanium-based carbonitride alloy and methods for its preparation |
RU2039126C1 (en) * | 1992-12-25 | 1995-07-09 | Российский научный центр "Курчатовский институт" | Method for hardening articles of metals and their alloys |
JPH08120394A (en) * | 1994-10-17 | 1996-05-14 | Sumitomo Metal Ind Ltd | Production of highly rigid material |
JP2002047528A (en) * | 2000-07-28 | 2002-02-15 | Sanyo Special Steel Co Ltd | Method for producing particle-dispersed type high strength ferritic steel |
US7410610B2 (en) * | 2002-06-14 | 2008-08-12 | General Electric Company | Method for producing a titanium metallic composition having titanium boride particles dispersed therein |
JP4461014B2 (en) * | 2002-07-29 | 2010-05-12 | コーニンクレッカ フィリップス エレクトロニクス エヌ ヴィ | Plasma nitriding of maraging steel, shaver cap and cutting device for electric shaver manufactured from such maraging steel, and electric shaver |
US7846272B2 (en) * | 2006-04-28 | 2010-12-07 | Gm Global Technology Operations, Inc. | Treated austenitic steel for vehicles |
JP2008255393A (en) * | 2007-04-03 | 2008-10-23 | Sanyo Special Steel Co Ltd | High rigidity material and its manufacturing method |
KR100869346B1 (en) * | 2007-06-12 | 2008-11-19 | 한국생산기술연구원 | Method and apparatus for plasma nitriding used high-density formed by low-energy electrode |
RU2360032C1 (en) * | 2007-12-10 | 2009-06-27 | Общество с ограниченной ответственностью "Специальные технологии" | Method of obtaining wear-resisting ultra-hard coatings |
-
2010
- 2010-12-24 FR FR1061243A patent/FR2969662B1/en not_active Expired - Fee Related
-
2011
- 2011-12-22 WO PCT/FR2011/053175 patent/WO2012085489A1/en active Application Filing
- 2011-12-22 KR KR1020137019553A patent/KR101506103B1/en active IP Right Grant
- 2011-12-22 US US13/997,558 patent/US8999228B2/en not_active Expired - Fee Related
- 2011-12-22 ES ES11815535.7T patent/ES2572642T3/en active Active
- 2011-12-22 RU RU2013132869/02A patent/RU2569438C2/en not_active IP Right Cessation
- 2011-12-22 JP JP2013545484A patent/JP5878932B2/en not_active Expired - Fee Related
- 2011-12-22 CN CN201180062477.7A patent/CN103282537B/en not_active Expired - Fee Related
- 2011-12-22 EP EP11815535.7A patent/EP2655684B1/en not_active Not-in-force
Also Published As
Publication number | Publication date |
---|---|
US20140086783A1 (en) | 2014-03-27 |
KR101506103B1 (en) | 2015-03-25 |
WO2012085489A1 (en) | 2012-06-28 |
RU2569438C2 (en) | 2015-11-27 |
ES2572642T3 (en) | 2016-06-01 |
FR2969662A1 (en) | 2012-06-29 |
JP2014507557A (en) | 2014-03-27 |
CN103282537B (en) | 2015-06-03 |
EP2655684A1 (en) | 2013-10-30 |
FR2969662B1 (en) | 2013-06-28 |
US8999228B2 (en) | 2015-04-07 |
KR20140005213A (en) | 2014-01-14 |
JP5878932B2 (en) | 2016-03-08 |
CN103282537A (en) | 2013-09-04 |
RU2013132869A (en) | 2015-01-27 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2655684B1 (en) | Method for reinforcing an alloy by plasma-nitriding | |
CA3001158C (en) | Steel, product created from said steel, and manufacturing method thereof | |
CA2984131A1 (en) | Steel, product made of said steel, and manufacturing method thereof | |
EP3056583B1 (en) | Method for manufacturing a part made of nitrided low-alloy steel | |
WO2022038484A1 (en) | Steel with high-grade mechanical characteristics and method for manufacturing same | |
EP3273303A1 (en) | Part for clock movement | |
EP3273304B1 (en) | Part for clock movement | |
FR2993575A1 (en) | CORRESPONDING ALLOY, PART, AND MANUFACTURING METHOD | |
CH715564B1 (en) | Composition of austenitic stainless steel powder without nickel and part produced by sintering of this powder. | |
EP3273305B1 (en) | Part for clock movement | |
FR2952650A1 (en) | PROCESS FOR PRODUCING AN ALLOY REINFORCED BY A DISPERSION OF NANOPARTICLES BASED ON NITRIDE | |
CH715726A1 (en) | Process for obtaining a functional component for a watch movement. | |
EP3935200B1 (en) | Austenitic stainless steel nickel-free powder composition and part manufactured by sintering by means of said powder | |
EP3963120B1 (en) | Case-hardened steel part for use in aeronautics | |
EP3252175B1 (en) | Molded steel alloy, corresponding part and manufacturing method | |
CH712718B1 (en) | Pivot pin for clockwork movement. | |
CH712719B1 (en) | Watch component for watch movement. | |
FR3003875A1 (en) | MARTENSIX OXIDE DISPERSION REINFORCED ALLOY HAVING IMPROVED RESISTANCE AND HIGH TEMPERATURE FLUID PROPERTIES, AND PROCESS FOR ITS MANUFACTURE | |
EP3885842B1 (en) | Non-magnetic timepiece component with improved wear resistance | |
WO2021110945A1 (en) | Method for hardening by nitriding | |
WO2023011980A1 (en) | Alloy with complex composition | |
CH717261A2 (en) | Non-magnetic watch component with wear resistance | |
WO2020249781A1 (en) | Titanium alloys with improved mechanical properties | |
CH712720A2 (en) | Pivot axis for watch movement. |
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: 20130703 |
|
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 |
|
DAX | Request for extension of the european patent (deleted) | ||
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
INTG | Intention to grant announced |
Effective date: 20151001 |
|
GRAJ | Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted |
Free format text: ORIGINAL CODE: EPIDOSDIGR1 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
INTG | Intention to grant announced |
Effective date: 20151123 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 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 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D Free format text: NOT ENGLISH |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 778116 Country of ref document: AT Kind code of ref document: T Effective date: 20160315 Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D Free format text: LANGUAGE OF EP DOCUMENT: FRENCH |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602011023713 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: RO Ref legal event code: EPE |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2572642 Country of ref document: ES Kind code of ref document: T3 Effective date: 20160601 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20160302 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 778116 Country of ref document: AT Kind code of ref document: T Effective date: 20160302 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160602 Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160603 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: PL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: AT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160702 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160704 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602011023713 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 6 |
|
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 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
26N | No opposition filed |
Effective date: 20161205 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160602 |
|
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: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161222 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161222 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 7 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20111222 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20160302 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20191216 Year of fee payment: 9 Ref country code: RO Payment date: 20191126 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20191230 Year of fee payment: 9 Ref country code: IT Payment date: 20191217 Year of fee payment: 9 Ref country code: BE Payment date: 20191218 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20200124 Year of fee payment: 9 Ref country code: GB Payment date: 20191220 Year of fee payment: 9 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R119 Ref document number: 602011023713 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RO Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201222 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20201222 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20201231 |
|
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: 20201231 Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201222 |
|
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: 20210701 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201222 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20220412 |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20201223 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20201231 |