US20180119257A1 - Steel with High Wear Resistance, Hardness and Corrosion Resistance as well as Low Thermal Conductivity - Google Patents
Steel with High Wear Resistance, Hardness and Corrosion Resistance as well as Low Thermal Conductivity Download PDFInfo
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- US20180119257A1 US20180119257A1 US15/507,004 US201515507004A US2018119257A1 US 20180119257 A1 US20180119257 A1 US 20180119257A1 US 201515507004 A US201515507004 A US 201515507004A US 2018119257 A1 US2018119257 A1 US 2018119257A1
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- 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
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
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- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
- C21D1/32—Soft annealing, e.g. spheroidising
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- 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
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
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- 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
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
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- 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
-
- 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
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
Definitions
- the invention relates to a steel for applications which require high wear resistance, a high degree of hardness, good corrosion resistance and/or low thermal conductivity.
- a typical area of use here is machines for reproducing or recycling plastic products which are melted down to a melt, in order to return them to the processing cycle.
- the melt is extruded through a die plate which it exits in a plurality of single strands.
- the single strands solidify and are then reduced in size to individual pellet grains by means of suitable knives rotating close to the die plate.
- Both the knives used for reducing the plastics to small pieces and the die plates used for forming the single strands to be reduced to small pieces by the knives must have good corrosion resistance, due to the corrosive environment to which they are exposed in use, and are at the same time exposed to a high level of abrasive wear.
- the thermal conductivity of the steel, from which the die plate has been produced in each case should at the same time be low, so that not too much heat is withdrawn from the plastic melt coming into contact with the respective die plate and a premature solidification of the melt occurs, which would result in the holes of the plate becoming blocked.
- the die plate is a so-called “micro die plate” with hole diameters of less than 1 mm.
- a known steel provided for these purposes is known under the material number 1.2379 (AISI designation: D2). It contains, in addition to iron and unavoidable impurities, (in % wt.) 1.55% C, 12.00% Cr, 0.80% Mo and 0.90% V.
- Another steel which is also widely used in plastics recycling is standardised under the material number 1.3343 (AISI designation: M2). It contains, in addition to iron and unavoidable impurities, (in % wt.) 0.85-0.9% C, 0.25% Mn, 4.1% Cr, 5.0% Mo, 1.9% V and 6.4% W.
- the martensitic steel standardised under the material number 1.4110 (AISI designation: 440A), which, in addition to iron and unavoidable impurities, contains (in % wt.) 0.6-0.75% C, max. 1% Mn, max. 1% Si, max. 0.04% P, max. 0.03% S, 16-18% Cr, and max. 0.75% Mo should stand up to the highest wear demands. After a suitable heat treatment this steel attains a hardness of at least 60 HRC.
- the proportion of titanium carbide in the microstructure of the steel composed in this way is 30% wt., which corresponds to a percentage by volume of approximately 40% vol. TiC.
- the known steel produced by powder metallurgy after it has been annealed over two to four hours in a vacuum at 850° C. and subsequently quenched, in which it is exposed to a nitrogen atmosphere at a pressure of 1-4.5 bar, attains an annealed hardness of approximately 53 HRC, which can be increased to a maximum hardness of approximately 62 HRC by means of a subsequent precipitation hardening treatment, in which the steel is aged over six to eight hours at 480° C.
- the object of the invention was to create a steel which can be produced on an industrial scale applying conventional methods and which has an optimised profile in terms of its properties. Practice-oriented uses of such a steel should also be stated.
- a steel is available for applications which require high wear resistance, a high degree of hardness, good corrosion resistance and/or low thermal conductivity.
- the steel according to the invention obtains a hardness of at least 56 HRC in the hardened state and contains in its microstructure in total at least 30% wt. of hard phases which in addition to the TiC particles consist of carbide particles, oxide particles or nitride particles. At the same time, the content of TiC particles in the steel according to the invention is at least 20% wt.
- the hard phases are embedded in a matrix which consists (in % wt.) of
- the components of a steel according to the invention are set such that it meets the highest requirements put on steels which are used in the plastics processing industry.
- a steel according to the invention is particularly suitable for the production of components for reproducing and for recycling plastic products.
- die plates in particular micro-pelletizing die plates, required for pelletizing melts formed from abrasive plastics can be produced from steel according to the invention, which themselves have optimum use properties even if their hole openings are micro-finely formed, in order to produce correspondingly fine-grained pellets.
- Knives for reducing plastic parts to small pieces can likewise be produced from steel according to the invention. Such knives are, as already explained above, also required when producing pellets from melted plastic strands as are produced by means of die plates of the type explained above in pelletizing installations.
- a steel according to the invention contains at least 20% wt. TiC which is embedded in a matrix which through precipitation formation contributes to the hardenability of the steel and which, at the same time, is chosen such that low thermal conductivity of less than 35 W/mK is guaranteed irrespective of the respective heat treatment state.
- the passive current density of the steel according to the invention is less than 5 ⁇ A/cm 2 , measured in oxygen-free 0.5 molar sulphuric acid with a potential change speed of 600 mV/h against a calomel reference electrode at 20° C. Therefore, steel according to the invention with a high degree of hardness and optimised wear resistance has a resistance to corrosion which is comparable to the resistance to corrosion of conventional austenitic stainless steels.
- the E-modulus of steels according to the invention determined by means of ultrasonic measurement subject to the sound-propagation velocity is at a temperature of 20° C. more than 270 GPa, in particular more than 300 GPa, so that the steel according to the invention or the components produced from it also reliably fulfil the highest requirements with regard to their strength.
- the thermal coefficient of expansion of steel according to the invention determined by means of a dilatometer lies in the temperature range important for applications for which steels according to the invention are provided of 20° C. to 600° C. at 7 ⁇ 10 ⁇ 6 /K to 12 ⁇ 10 ⁇ 6 /K.
- the steel according to the invention contains at least 20% wt. corresponding to approximately 30% vol. TiC, or at least 28% wt. TiC, in particular at least 30% wt. TiC.
- the TiC content should not exceed an upper limit of 45% wt. In this way, it can be ensured that steel according to the invention can be operationally reliably produced and processed further.
- An advantage of steel according to the invention here is that it can also be conventionally machined.
- the precipitations which are formed in the steel matrix of the steel according to the invention are intermetallic precipitations which, above all, the elements Ni, Al and Ti are involved in forming. These elements form Ni 3 Al and Ni 3 Ti or mixed forms. These intermetallic phases are present in the microstructure with grain sizes of the order of 10 nm and are not included in the total hard-phase content. Due to their small size they do not make a great contribution to resistance against abrasive wear compared to the coarse hard-phase particles, as are embedded according to the invention in the matrix of the steel according to the invention, but the intermetallic precipitations bring about an increase in the hardness and strength of the metal matrix and, in this way, also contribute to improvement in the performance characteristics.
- Chromium is present in contents of 9.0-15.0% wt. in the steel according to the invention, in order to guarantee the required corrosion resistance. Optimally, the Cr content amounts to 12.5-14.5% wt. for this purpose.
- Molybdenum is contained in contents of 5.0-9.0% wt. in the steel according to the invention, in order, on the one hand, to guarantee sufficient resistance to corrosion, in particular with regard to the hole corrosion, and, on the other hand, to support the formation of intermetallic phases, by means of which the hardness of the steel matrix, in which the hard phases are embedded, is increased.
- the Mo content of the steel according to the invention is 6.5-7.5% wt.
- Cobalt is contained in contents of 6.0-11.0% wt. in the steel according to the invention, in order, on the one hand, to increase the martensite start temperature and, on the other hand, to reduce the solubility of Mo in the metal matrix.
- the Mo contained in the steel matrix according to the invention can participate more strongly in the formation of intermetallic phases.
- the Co content of the steel according to the invention is 8.0-10.0% wt.
- Copper is contained in contents of 0.3-1.5% wt. in the steel according to the invention, in order to accelerate the precipitation hardening.
- the Cu content of the steel according to the invention is 0.5-1.0% wt.
- Nickel is contained in contents of 3.0-7.0% wt. in the steel according to the invention. Nickel is required in a sufficient amount in the steel matrix in order to stabilise the austenitic phase during a solution annealing operation which is typically carried out at approximately 850° C. This is particularly important if the material according to the invention is quenched starting from the solution annealing temperature. As a result of the presence of nickel, the austenite is stabilised here to the extent that martensite is reliably formed during quenching. If too little nickel is present in the steel matrix provided according to the invention, then this effect is no longer achieved with the necessary reliability.
- the second function of nickel in the steel according to the invention is precipitation hardening by forming intermetallic phases with elements like Al and Ti. Therefore, the contents of Ni, Al and Ti are geared to one another in the steel matrix of the steel according to the invention in such a way that, on the one hand, there is formation of martensite and, on the other hand, the precipitation hardening is made possible.
- the Ni content of the steel according to the invention is 4.5-5.5% wt. for this purpose.
- Titanium is present in contents of 0.1-2.0% wt. in the steel according to the invention, so that, as already mentioned above, in combination with Ni the precipitation hardening is made possible.
- the Ti content of the steel according to the invention is 0.8-1.2% wt. for this purpose.
- Aluminium is also present in contents of 0.1-2.0% wt. in the steel according to the invention, so that in combination with Ni the precipitation hardening is brought about.
- the Al content of the steel according to the invention is 1.0-1.4% wt. for this purpose.
- the steel according to the invention can be hardened with extremely low warping, since titanium carbide has a low thermal expansion and no transformation.
- the wear resistance of the steel according to the invention is increased by adding up to 4.5% wt. of NbC particles.
- the NbC particles have a lower thermal conductivity than TiC, which has a favourable effect on the performance characteristics of the steel according to the invention.
- TiC and NbC are isomorphic carbides and are therefore miscible with one another. In the case of diffusion reactions this results in the formation of composite carbides.
- the thermal conductivity of the steel according to the invention is lowered and the fitness for purpose improved. This effect can in particular be achieved if at least 2.0% wt. of NbC is present in the steel according to the invention. There is an optimum effect if the NbC content is 2.0-3.0% wt.
- the steel according to the invention By producing the steel according to the invention in a conventional way by powder metallurgy, it can be ensured that its microstructure is free of segregations and fibre orientations.
- the carbide, nitride and oxide particles used as hard phases according to the invention are already provided as “complete” particles during powder-metallurgical production.
- Both the sintering and the HIP (Hot Isostatic Pressing) routes can be used for powder-metallurgical production.
- supersolidus liquid-phase sintering based on gas atomised steel powder is also suitable for producing steels according to the invention.
- the steel according to the invention can be subjected to a conventional heat treatment for setting its mechanical properties, in which it is heated for 2-4 hours, subsequently quenched in a nitrogen atmosphere subjected to a pressure of 1-4.5 bar and finally aged over 6-8 hours at 480° C.
- steel according to the invention consistently has a hardness of more than 62 HRC.
- By heating taking place in a vacuum and quenching being carried out in an inert gas atmosphere negative influence zones in the edge region of the semi-finished product in each case formed from the steel for the heat treatment can be prevented. If the heat treatment is limited to a soft annealing operation at 850° C. over 2-4 hours, then the steel according to the invention has a hardness of more than 50 HRC.
- FIG. 1 a part of a scanning electron micrograph of a section of a sample according to the invention
- FIG. 2 a diagram, in which the results of the measurement of the thermal conductivity of steel samples produced according to the invention and produced for comparison are illustrated;
- FIG. 3 a diagram with the result of a current density potential measurement carried out on steel samples produced according to the invention and produced for comparison;
- FIG. 4 a diagram which reproduces the result of a dilatometer measurement on a sample produced from steel according to the invention.
- the steel E according to the invention and the known steel V have been produced for comparing the properties of a steel according to the invention, which is intended for producing die plates or knives for an underwater pelletizing machine, to the properties of a known steel intended for the same purpose.
- the composition of both steels E and V is indicated in Table 1.
- the composition of steel V corresponded to the composition of the steel known under the designation “Ferro-Titanit Nikro 128” documented for example in the publication already mentioned above.
- the production steps completed during powder-metallurgical production of both steels E, V corresponded to the production steps which are normally carried out during powder-metallurgical production of the steel “Ferro-Titanit Nikro 128”. They are explained in the technical literature already mentioned above.
- samples PE1, PV1 of the steels E and V were subjected to a heat treatment which likewise corresponded to the heat treatment carried out in a standard manner for the steel Ferro-Titanit Nikro 128.
- the probes PE1 and PV1 were firstly held at a temperature of 850° C. in a vacuum over a period of two to four hours and were then quenched in a nitrogen atmosphere subjected to a pressure of 1-4.5 bar.
- FIG. 1 shows a part of a scanning electron micrograph of a section of a sample PE1 of the steel E according to the invention heat-treated in such a way in a standard manner.
- the metal matrix can be identified by the light areas, whereas the TiC inclusions surrounded by the matrix are reproduced dark in colour.
- the hard-phase contents were determined in the samples PE1, PV1, PE2, PV2.
- the samples PE1, PE2 produced from the steel according to the invention they on average amounted to more than 30% wt., whereas the samples PV1, PV2 produced from the comparison steel V had on average only 30% wt. of hard phases.
- ⁇ (T) was determined by means of the indirect method at room temperature, 100° C., 200° C. and 300° C.:
- ⁇ ( T ) a ( T ) ⁇ ( T ) ⁇ c ⁇ ( T )
- the TiC content of the samples PE1, PE2 was, as indicated in Table 1, in each case more than 30% wt.
- the density of the samples PE1, PE2 produced from the steel E according to the invention was 6.55 g/cm 3 , whereby the theoretical density was reached. As becomes evident from FIG. 1 , the microstructure has no residual porosity.
- FIG. 3 The result of a current density potential measurement carried out on samples PE1 produced from the steel E according to the invention and on samples PV1 produced from the comparison steel V is illustrated in FIG. 3 .
- the current density potential curve determined for the samples PE1 is illustrated as a continuous line and the current density potential curve determined for the samples PV1 is illustrated as a broken line.
- the current density potential curves were measured in oxygen-fee 0.5 molar sulphuric acid with a potential change speed of 600 mV/h against a calomel reference electrode at 20° C.
- the passive current densities determined for the samples PE1 according to the invention were in each case below 5 ⁇ A/cm 2 .
- the elasticity modulus was determined as 318 GPa for the samples PE1 produced from the steel E according to the invention by ultrasonic means subject to the sound-propagation velocity.
- the elasticity module of the conventional samples PV1 was 294 GPa.
- Table 3 gives an overview of the thermal expansion of the steel E. This was measured by means of a Bähr dilatometer in temperature steps of 100° C. up to a maximum temperature of 600° C. It can be identified that the thermal coefficient of expansion ⁇ th lies in this temperature range between 7 and 12 10- 6 /K.
- FIG. 4 shows, by way of example, the result of a dilatometer measurement on a sample PE1 produced from the steel according to the invention, which confirms this result.
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Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
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DE102014112374.3A DE102014112374A1 (de) | 2014-08-28 | 2014-08-28 | Stahl mit hoher Verschleißbeständigkeit, Härte und Korrosionsbeständigkeit sowie niedriger Wärmeleitfähigkeit und Verwendung eines solchen Stahls |
DE102014112374.3 | 2014-08-28 | ||
PCT/EP2015/069477 WO2016030396A1 (fr) | 2014-08-28 | 2015-08-26 | Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier |
Publications (1)
Publication Number | Publication Date |
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US20180119257A1 true US20180119257A1 (en) | 2018-05-03 |
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Family Applications (1)
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US15/507,004 Abandoned US20180119257A1 (en) | 2014-08-28 | 2015-08-26 | Steel with High Wear Resistance, Hardness and Corrosion Resistance as well as Low Thermal Conductivity |
Country Status (9)
Country | Link |
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US (1) | US20180119257A1 (fr) |
EP (1) | EP3186405B1 (fr) |
JP (1) | JP6210502B1 (fr) |
KR (1) | KR20170041276A (fr) |
CN (1) | CN107075624A (fr) |
BR (1) | BR112017002127A2 (fr) |
DE (1) | DE102014112374A1 (fr) |
RU (1) | RU2674174C2 (fr) |
WO (1) | WO2016030396A1 (fr) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
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CN112251749A (zh) * | 2020-10-23 | 2021-01-22 | 黑龙江科技大学 | 一种利用等离子熔覆制备定向阵列的陶瓷相增强高熵合金耐磨涂层的方法 |
WO2022102805A1 (fr) * | 2020-11-10 | 2022-05-19 | 한국재료연구원 | Matériau composite à base de fe renforcé par des particules de tic et procédé pour la préparation de celui-ci |
EP4104953A4 (fr) * | 2020-03-12 | 2023-08-09 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Procédé de fabrication d'article fabriqué de manière additive, et article fabriqué de manière additive |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
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EP3263726A1 (fr) * | 2016-06-29 | 2018-01-03 | Deutsche Edelstahlwerke GmbH | Matériau à base de fe et son procédé de fabrication |
CN111455274A (zh) * | 2020-04-08 | 2020-07-28 | 鞍钢股份有限公司 | 一种80Ksi级别9Cr火驱热采油井管及其制造方法 |
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DE3015709A1 (de) * | 1980-04-24 | 1981-10-29 | Thyssen Edelstahlwerke AG, 4000 Düsseldorf | Hartstofflegierung |
JP2000273503A (ja) * | 1999-03-25 | 2000-10-03 | Kobe Steel Ltd | 硬質粒分散焼結鋼及びその製造方法 |
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US3966423A (en) * | 1973-11-06 | 1976-06-29 | Mal M Kumar | Grain refinement of titanium carbide tool steel |
JPH0229736B2 (ja) * | 1984-09-14 | 1990-07-02 | Mitsubishi Metal Corp | Bunsankyokagatashoketsugokinkoseinetsukantaimamobuzai |
JPH0586435A (ja) * | 1991-09-27 | 1993-04-06 | Hitachi Metals Ltd | 高耐食高耐摩耗性工具部品材料 |
SE9604538D0 (sv) * | 1996-12-10 | 1996-12-10 | Hoeganaes Ab | Agglomerated iron-based powders |
US6521353B1 (en) * | 1999-08-23 | 2003-02-18 | Kennametal Pc Inc. | Low thermal conductivity hard metal |
SE529041C2 (sv) * | 2005-08-18 | 2007-04-17 | Erasteel Kloster Ab | Användning av ett pulvermetallurgiskt tillverkat stål |
SE528991C2 (sv) * | 2005-08-24 | 2007-04-03 | Uddeholm Tooling Ab | Ställegering och verktyg eller komponenter tillverkat av stållegeringen |
GB2440737A (en) * | 2006-08-11 | 2008-02-13 | Federal Mogul Sintered Prod | Sintered material comprising iron-based matrix and hard particles |
SE533988C2 (sv) * | 2008-10-16 | 2011-03-22 | Uddeholms Ab | Stålmaterial och förfarande för framställning därav |
CN104805346A (zh) * | 2010-02-05 | 2015-07-29 | 伟尔矿物澳大利亚私人有限公司 | 硬金属材料 |
RU2443795C2 (ru) * | 2010-04-16 | 2012-02-27 | Тамара Федоровна Волынова | МНОГОФУНКЦИОНАЛЬНЫЕ АНТИФРИКЦИОННЫЕ НАНОСТРУКТУРИРОВАННЫЕ ИЗНОСОСТОЙКИЕ ДЕМПФИРУЮЩИЕ С ЭФФЕКТОМ ПАМЯТИ ФОРМЫ СПЛАВЫ НА МЕТАСТАБИЛЬНОЙ ОСНОВЕ ЖЕЛЕЗА СО СТРУКТУРОЙ ГЕКСАГОНАЛЬНОГО ε-МАРТЕНСИТА И ИЗДЕЛИЯ С ИСПОЛЬЗОВАНИЕМ ЭТИХ СПЛАВОВ С ЭФФЕКТОМ САМООРГАНИЗАЦИИ НАНОСТРУКТУРНЫХ КОМПОЗИЦИЙ, САМОУПРОЧНЕНИЯ И САМОСМАЗЫВАНИЯ ПОВЕРХНОСТЕЙ ТРЕНИЯ, С ЭФФЕКТОМ САМОГАШЕНИЯ ВИБРАЦИЙ И ШУМОВ |
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- 2015-08-26 WO PCT/EP2015/069477 patent/WO2016030396A1/fr active Application Filing
- 2015-08-26 US US15/507,004 patent/US20180119257A1/en not_active Abandoned
- 2015-08-26 EP EP15756892.4A patent/EP3186405B1/fr active Active
- 2015-08-26 RU RU2017106319A patent/RU2674174C2/ru not_active IP Right Cessation
- 2015-08-26 KR KR1020177008168A patent/KR20170041276A/ko not_active Application Discontinuation
- 2015-08-26 CN CN201580046492.0A patent/CN107075624A/zh active Pending
- 2015-08-26 JP JP2017502268A patent/JP6210502B1/ja active Active
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DE3015709A1 (de) * | 1980-04-24 | 1981-10-29 | Thyssen Edelstahlwerke AG, 4000 Düsseldorf | Hartstofflegierung |
JP2000273503A (ja) * | 1999-03-25 | 2000-10-03 | Kobe Steel Ltd | 硬質粒分散焼結鋼及びその製造方法 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
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EP4104953A4 (fr) * | 2020-03-12 | 2023-08-09 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Procédé de fabrication d'article fabriqué de manière additive, et article fabriqué de manière additive |
CN112251749A (zh) * | 2020-10-23 | 2021-01-22 | 黑龙江科技大学 | 一种利用等离子熔覆制备定向阵列的陶瓷相增强高熵合金耐磨涂层的方法 |
WO2022102805A1 (fr) * | 2020-11-10 | 2022-05-19 | 한국재료연구원 | Matériau composite à base de fe renforcé par des particules de tic et procédé pour la préparation de celui-ci |
Also Published As
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KR20170041276A (ko) | 2017-04-14 |
JP2017532434A (ja) | 2017-11-02 |
EP3186405B1 (fr) | 2018-10-03 |
EP3186405A1 (fr) | 2017-07-05 |
BR112017002127A2 (pt) | 2017-11-21 |
RU2674174C2 (ru) | 2018-12-05 |
RU2017106319A3 (fr) | 2018-08-28 |
RU2017106319A (ru) | 2018-08-28 |
CN107075624A (zh) | 2017-08-18 |
WO2016030396A1 (fr) | 2016-03-03 |
JP6210502B1 (ja) | 2017-10-11 |
DE102014112374A1 (de) | 2016-03-03 |
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