EP3031942A1 - Stainless steel strip for flapper valves - Google Patents
Stainless steel strip for flapper valves Download PDFInfo
- Publication number
- EP3031942A1 EP3031942A1 EP14196949.3A EP14196949A EP3031942A1 EP 3031942 A1 EP3031942 A1 EP 3031942A1 EP 14196949 A EP14196949 A EP 14196949A EP 3031942 A1 EP3031942 A1 EP 3031942A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- strip
- steel
- mpa
- strip according
- following requirements
- 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.)
- Granted
Links
Images
Classifications
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- 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
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
- F04B—POSITIVE-DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS
- F04B39/00—Component parts, details, or accessories, of pumps or pumping systems specially adapted for elastic fluids, not otherwise provided for in, or of interest apart from, groups F04B25/00 - F04B37/00
- F04B39/10—Adaptations or arrangements of distribution members
- F04B39/1073—Adaptations or arrangements of distribution members the members being reed valves
-
- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
- F04B—POSITIVE-DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS
- F04B2201/00—Pump parameters
- F04B2201/06—Valve parameters
- F04B2201/0603—Valve wear
Definitions
- the invention relates to a stainless steel strip for flapper valves in compressors and other reed applications.
- Flapper or reed valves are used in various types of applications where a specific type of compression cycle is regulated for a specific purpose. It can be a refrigeration cycle in a hermetic reciprocating compressor working uninterrupted in a refrigerator or in the air conditioner of a car.
- a flapper valve is basically a spring made from a pre-hardened steel strip. In its simplest form, the flapper valve is tongue shaped, where one end is fixed and the opposite end hangs free and regulates the liquid or gas flow in the compressor.
- the flapper valve suffers from both cyclic bending stresses and cyclic impact stresses during its service. Usually, these cyclic stresses eventually cause fatigue failure. Accordingly, the fatigue properties are of the utmost importance for the flapper valve material.
- a flapper valve made of a steel strip of this invention has its fatigue properties optimized by a combined effect of modifications to the chemical composition of the steel, the non-metallic inclusions and the heat treatment.
- Compressor OEMs require materials that have a higher fatigue life to improve the compressor's performance and life.
- COP coefficient of performance
- the existing steel grades used for reed valves are modified versions of a carbon steel AISI 1095 and a stainless steel AISI 420 produced via conventional melting, casting, rolling and heat treatment processes.
- the industry demands and resulting performance requirements mean that future flapper reeds will increasingly need to be made out of very thin steel strip with an increased fatigue life expectancy and higher damping properties.
- the general object of the present invention is to provide a pre-hardened stainless steel strip for flapper valves having an optimized property profile such that it can be used to produce more efficient and reliable compressors.
- a further object is to provide pre-hardened stainless steel strip for flapper valves, which reduces the flapper reed contribution to the overall noise levels of the compressor.
- Carbon is to be present in a minimum content of 0.3 %, preferably at least 0.32, 0.34, 0.36 or 0.36 %.
- Carbon is a strong austenite stabilizer with relatively large solubility in austenite.
- the upper limit for carbon is 0.5 % and may be set to 0.48, 0.46, 0.44 or 0.42 %.
- a referred range is 0.35 - 0.41 %.
- the amount of carbon should be controlled such that the amount of primary carbides of the type M 23 C 6 , M 7 C 3 and M 6 C in the steel is limited, preferably the steel is free from such primary carbides.
- Si is used for deoxidation.
- Si is a strong ferrite former and increases the carbon activity.
- Si is also a powerful solid-solution strengthening element and strengthens the steel matrix. This effect appears at a content of 0.2 %Si. A preferred range is 0.30 - 0.60 %.
- Manganese is an austenite stabilizer and contributes to improving the hardenability of the steel. Manganese shall therefore be present in a minimum content of 0.2 %, preferably at least 0.3, 0.35 or 0.4 %. When the content of Mn is too large the amount of retained austenite after finish annealing may be too high.
- the steel shall therefore contain maximum 1.0 % Mn, preferably maximum 0.8, 0.7 or 0.65 %.
- Chromium is a ferrite stabilizing element, which is added to impart corrosion resistance to the steel. Cr needs to be present in a content of at least 12.0 % in order to provide a passive film on the steel surface.
- the lower limit may be 12,4, 12, 6, 12, 8 or 13 %. When the content of Cr exceeds 15 %, however, delta ferrite may form.
- Mo is a ferrite stabilizer and is known to have a very favourable effect on the hardenability. Molybdenum is essential for attaining a good secondary hardening response. The minimum content is 0.5 % and may be set to 0.6, 0.7 or 0.8 %. Molybdenum is strong carbide forming element and also a strong ferrite former. The maximum content of molybdenum is therefore 2.0 %. Preferably Mo is limited to 1.5, 1.3 or 1.1 %.
- Vanadium forms evenly distributed fine precipitated carbides, nitrides and carbonitrides of the type V(N,C) in the matrix of the steel.
- This hard phase may also be denoted MX, wherein M is mainly V but other metals like Cr and Mo may be present to some extent.
- X is one or both of C and N. Vanadium shall therefore be present in an amount of 0.01 - 0.2%.
- the upper limit may be set to 0.1 or 0.08 %.
- the lower limit may be 0.02, 0.03, 0.04 or 0.05%.
- Nitrogen is a strong austenite former. N is restricted to 0.15% in order to obtain the desired type and amount of hard phases, in particular V(C,N). Higher nitrogen content may lead to work hardening, edge cracking and/or a high amount of retained austenite.
- vanadium rich carbonitrides V(C,N) will form. These will be partly dissolved during the austenitizing step and then precipitated during the tempering step as particles of nanometre size.
- the thermal stability of vanadium carbonitrides is considered to be better than that of vanadium carbides. Therefore the resistance against grain growth at high austenitizing temperatures is enhanced.
- the lower limit may be 0.02, 0.03, 0.04 or 0.05 %.
- the upper limit may be 0.12, 0.10, 0.08 or 0.06 %.
- Nickel is an austenite former. Ni may be present in an amount of ⁇ 2.0 %. It gives the steel a good hardenability and toughness. However, because of the expense, the nickel content of the steel should be limited. The upper limit may therefore be set to 1.0, 0.5 or 0.5%. However, Ni is normally not deliberately added.
- Cobalt is an austenite former. Co causes the solidus temperature to increase and therefore provides an opportunity to raises the hardening temperature. During austenitization it is therefore possible to dissolve larger fraction of carbides and thereby enhance the hardenability. Co also increases the M s temperature. However, large amount of Co may result in a decreased toughness and wear resistance. The maximum amount is 2 % and may be set to 0.5 %. However, for practical reasons, such as scrap handling, a deliberate addition of Co is normally not made.
- Cu is an austenite stabilizing element but has a low solubility in ferrite. Cu may contribute to increasing the hardness and the corrosion resistance of the steel. However, it is not possible to extract copper from the steel once it has been added. This drastically makes the scrap handling more difficult. For this reason, the upper limit may be 1.0, 0.5, or 0.3 %. Copper is normally not deliberately added.
- Aluminium may be used for deoxidation in combination with Si and Mn.
- the lower limit is set to 0.001, 0.003, 0.005 or 0.007% in order to ensure a good deoxidation.
- the upper limit is restricted to 0.06% for avoiding precipitation of undesired phases such as AlN and hard, brittle Alumina inclusions.
- the upper limit may be 0.05, 0.04, 0.03, 0.02 or 0.015%.
- molybdenum may be replaced by twice as much with tungsten because of their chemical similarities.
- tungsten is expensive and it also complicates the handling of scrap metal.
- the maximum amount is therefore limited to 2 %, preferably 0.5 % or 0.3 % and most preferably no deliberate additions are made.
- Niobium is similar to vanadium in that it forms carbonitrides of the type M(N,C) and may in principle be used to replace part of the vanadium but that requires the double amount of niobium as compared to vanadium.
- Nb results in a more angular shape of the M(N,C) and these are also much more stable than V(C,N) and may therefore not be dissolved during austenitising.
- the maximum amount is therefore 0.05%, preferably 0.01 % and most preferably no deliberate additions are made.
- These elements are carbide formers and may be present in the alloy in the claimed ranges for altering the composition of the hard phases. However, normally none of these elements are added.
- B may be used in order to further increase the hardness of the steel.
- the amount is limited to 0.01 %, preferably ⁇ 0.005 or even ⁇ 0.001 %.
- P, S and O are the main impurities, which have a negative effect on the mechanical properties of the steel strip.
- P may therefore be limited to 0.03%, preferably to 0.01%.
- S may be limited to 0.03, 0.01, 0.008, 0.0005 or 0.0002%.
- O may be limited to 0.003, 0.002 or 0.001%.
- the present inventors have systematically investigated the effect of a modified chemical composition and a modified heat treatment on the mechanical properties of the flapper valve material.
- the modifications made to the chemical composition relative to the conventional material were mainly focused on increases in nitrogen and vanadium although some benefits were also gained from increases in austenite levels and tighter control over such elements as carbon, manganese and phosphorus.
- valve strip was undertaken using different furnace parameters to map the hardening response of material from the conventional and modified chemical compositions.
- the production trials were carried out at a constant line speed with hardening temperatures in the range from 1000 °C to 1080°C, quenching into a molten lead alloy at a temperature in the range of 250°C to 350°C and tempering at temperatures in the range from 220°C to 600°C.
- a stainless steel strip according to the invention is compared to a conventional stainless steel strip.
- the composition of the investigated steels was as follows: Conventional Inventive C 0.38 0.40 Si 0.36 0.42 Mn 0.48 0.56 Cr 13.1 13.4 Mo 0.98 0.99 N 0.017 0.052 V 0.009 0.055 Ni 0.31 0.15 P 0.018 0.018 S 0.0004 0.0006
- the cold rolled strips used for the hardening and tempering trials all had a thickness of 0.203 mm and a width of 140 mm.
- the strips were subjected to hardening and tempering in the above mentioned continuous hardening furnace.
- Tensile strength measurements were made according to ISO 6892:2009.
- Fig. 1 discloses tensile properties as a function of the austenitising temperature.
- Fig. 2 discloses the tensile properties as a function of the tempering temperature.
- the inventive steel strip can be used for producing flapper valves for compressors having improved properties.
Abstract
Description
- The invention relates to a stainless steel strip for flapper valves in compressors and other reed applications.
- Flapper or reed valves are used in various types of applications where a specific type of compression cycle is regulated for a specific purpose. It can be a refrigeration cycle in a hermetic reciprocating compressor working uninterrupted in a refrigerator or in the air conditioner of a car. A flapper valve is basically a spring made from a pre-hardened steel strip. In its simplest form, the flapper valve is tongue shaped, where one end is fixed and the opposite end hangs free and regulates the liquid or gas flow in the compressor. The flapper valve suffers from both cyclic bending stresses and cyclic impact stresses during its service. Usually, these cyclic stresses eventually cause fatigue failure. Accordingly, the fatigue properties are of the utmost importance for the flapper valve material.
- A flapper valve made of a steel strip of this invention has its fatigue properties optimized by a combined effect of modifications to the chemical composition of the steel, the non-metallic inclusions and the heat treatment.
- Compressor OEMs require materials that have a higher fatigue life to improve the compressor's performance and life.
- Furthermore, there is a growing interest in the industry to develop more energy efficient and quieter compressors. The coefficient of performance (COP) can be increased by increasing the valve lift and by reducing the thickness of the valves. Compressor designers therefore require valve materials that have enhanced damping properties in addition to fatigue strength improvement.
- The existing steel grades used for reed valves are modified versions of a carbon steel AISI 1095 and a stainless steel AISI 420 produced via conventional melting, casting, rolling and heat treatment processes. However, the industry demands and resulting performance requirements mean that future flapper reeds will increasingly need to be made out of very thin steel strip with an increased fatigue life expectancy and higher damping properties.
- The general object of the present invention is to provide a pre-hardened stainless steel strip for flapper valves having an optimized property profile such that it can be used to produce more efficient and reliable compressors.
- A further object is to provide pre-hardened stainless steel strip for flapper valves, which reduces the flapper reed contribution to the overall noise levels of the compressor.
- It is also an object of the present invention to provide a method of producing such an improved steel strip.
- The foregoing objects, as well as additional advantages are achieved to a significant measure by providing a cold rolled and hardened martensitic stainless steel strip having a composition, microstructure and physical properties as set out in the claims.
- The invention is defined in the claims.
- The importance of the separate elements and their interaction with each other as well as the limitations of the chemical ingredients of the claimed alloy are briefly explained in the following. All percentages for the chemical composition of the steel are given in weight % (wt. %) throughout the description. The amount of microstructural phases is given in volume % (vol. %). Upper and lower limits of the individual elements can be freely combined within the limits set out in the claims.
- is to be present in a minimum content of 0.3 %, preferably at least 0.32, 0.34, 0.36 or 0.36 %. Carbon is a strong austenite stabilizer with relatively large solubility in austenite. The upper limit for carbon is 0.5 % and may be set to 0.48, 0.46, 0.44 or 0.42 %. A referred range is 0.35 - 0.41 %. In any case, the amount of carbon should be controlled such that the amount of primary carbides of the type M23C6, M7C3 and M6C in the steel is limited, preferably the steel is free from such primary carbides.
- Silicon is used for deoxidation. Si is a strong ferrite former and increases the carbon activity. Si is also a powerful solid-solution strengthening element and strengthens the steel matrix. This effect appears at a content of 0.2 %Si. A preferred range is 0.30 - 0.60 %.
- Manganese is an austenite stabilizer and contributes to improving the hardenability of the steel. Manganese shall therefore be present in a minimum content of 0.2 %, preferably at least 0.3, 0.35 or 0.4 %. When the content of Mn is too large the amount of retained austenite after finish annealing may be too high. The steel shall therefore contain maximum 1.0 % Mn, preferably maximum 0.8, 0.7 or 0.65 %.
- Chromium is a ferrite stabilizing element, which is added to impart corrosion resistance to the steel. Cr needs to be present in a content of at least 12.0 % in order to provide a passive film on the steel surface. The lower limit may be 12,4, 12, 6, 12, 8 or 13 %. When the content of Cr exceeds 15 %, however, delta ferrite may form.
- Mo is a ferrite stabilizer and is known to have a very favourable effect on the hardenability. Molybdenum is essential for attaining a good secondary hardening response. The minimum content is 0.5 % and may be set to 0.6, 0.7 or 0.8 %. Molybdenum is strong carbide forming element and also a strong ferrite former. The maximum content of molybdenum is therefore 2.0 %. Preferably Mo is limited to 1.5, 1.3 or 1.1 %.
- Vanadium forms evenly distributed fine precipitated carbides, nitrides and carbonitrides of the type V(N,C) in the matrix of the steel. This hard phase may also be denoted MX, wherein M is mainly V but other metals like Cr and Mo may be present to some extent. X is one or both of C and N. Vanadium shall therefore be present in an amount of 0.01 - 0.2%. The upper limit may be set to 0.1 or 0.08 %. The lower limit may be 0.02, 0.03, 0.04 or 0.05%.
- Nitrogen is a strong austenite former. N is restricted to 0.15% in order to obtain the desired type and amount of hard phases, in particular V(C,N). Higher nitrogen content may lead to work hardening, edge cracking and/or a high amount of retained austenite. When the nitrogen content is properly balanced against the vanadium content, vanadium rich carbonitrides V(C,N) will form. These will be partly dissolved during the austenitizing step and then precipitated during the tempering step as particles of nanometre size. The thermal stability of vanadium carbonitrides is considered to be better than that of vanadium carbides. Therefore the resistance against grain growth at high austenitizing temperatures is enhanced. The lower limit may be 0.02, 0.03, 0.04 or 0.05 %. The upper limit may be 0.12, 0.10, 0.08 or 0.06 %.
- Nickel is an austenite former. Ni may be present in an amount of ≤2.0 %. It gives the steel a good hardenability and toughness. However, because of the expense, the nickel content of the steel should be limited. The upper limit may therefore be set to 1.0, 0.5 or 0.5%. However, Ni is normally not deliberately added.
- Cobalt is an austenite former. Co causes the solidus temperature to increase and therefore provides an opportunity to raises the hardening temperature. During austenitization it is therefore possible to dissolve larger fraction of carbides and thereby enhance the hardenability. Co also increases the Ms temperature. However, large amount of Co may result in a decreased toughness and wear resistance. The maximum amount is 2 % and may be set to 0.5 %. However, for practical reasons, such as scrap handling, a deliberate addition of Co is normally not made.
- Cu is an austenite stabilizing element but has a low solubility in ferrite. Cu may contribute to increasing the hardness and the corrosion resistance of the steel. However, it is not possible to extract copper from the steel once it has been added. This drastically makes the scrap handling more difficult. For this reason, the upper limit may be 1.0, 0.5, or 0.3 %. Copper is normally not deliberately added.
- Aluminium may be used for deoxidation in combination with Si and Mn. The lower limit is set to 0.001, 0.003, 0.005 or 0.007% in order to ensure a good deoxidation. The upper limit is restricted to 0.06% for avoiding precipitation of undesired phases such as AlN and hard, brittle Alumina inclusions. The upper limit may be 0.05, 0.04, 0.03, 0.02 or 0.015%.
- In principle, molybdenum may be replaced by twice as much with tungsten because of their chemical similarities. However, tungsten is expensive and it also complicates the handling of scrap metal. The maximum amount is therefore limited to 2 %, preferably 0.5 % or 0.3 % and most preferably no deliberate additions are made.
- Niobium is similar to vanadium in that it forms carbonitrides of the type M(N,C) and may in principle be used to replace part of the vanadium but that requires the double amount of niobium as compared to vanadium. However, Nb results in a more angular shape of the M(N,C) and these are also much more stable than V(C,N) and may therefore not be dissolved during austenitising. The maximum amount is therefore 0.05%, preferably 0.01 % and most preferably no deliberate additions are made.
- These elements are carbide formers and may be present in the alloy in the claimed ranges for altering the composition of the hard phases. However, normally none of these elements are added.
- B may be used in order to further increase the hardness of the steel. The amount is limited to 0.01 %, preferably ≤ 0.005 or even ≤ 0.001 %.
- These elements may be added to the steel in the claimed amounts in order to further improve the hot workability and to modify the shape of non-metallic inclusions.
- P, S and O are the main impurities, which have a negative effect on the mechanical properties of the steel strip. P may therefore be limited to 0.03%, preferably to 0.01%. S may be limited to 0.03, 0.01, 0.008, 0.0005 or 0.0002%. O may be limited to 0.003, 0.002 or 0.001%.
- The present inventors have systematically investigated the effect of a modified chemical composition and a modified heat treatment on the mechanical properties of the flapper valve material. The modifications made to the chemical composition relative to the conventional material were mainly focused on increases in nitrogen and vanadium although some benefits were also gained from increases in austenite levels and tighter control over such elements as carbon, manganese and phosphorus.
- The continuous hardening of valve strip was undertaken using different furnace parameters to map the hardening response of material from the conventional and modified chemical compositions. The production trials were carried out at a constant line speed with hardening temperatures in the range from 1000 °C to 1080°C, quenching into a molten lead alloy at a temperature in the range of 250°C to 350°C and tempering at temperatures in the range from 220°C to 600°C.
- The mechanical properties resulting from these hardening trials on conventional material corresponded to:
- a yield strength Rp0.2 range between 1300 MPa and 1600 MPa,
- a tensile strength Rm range between 1740 MPa and 2100 MPa
- an elongation A50 range between 4 % and 6 %
- Further continuous hardening trials were carried out on material with the modified chemical composition and non-metallic inclusion content. The production trials were carried out at a constant line speed with hardening temperatures in the range from 1050 °C to 1100°C, quenching into a molten lead alloy at a temperature in the range of 250°C to 350°C and tempering at temperatures in the range from 220°C to 600°C.
- The mechanical properties resulting from further hardening trials on material with the modified chemical composition and non-metallic inclusion content corresponded to:
- a Rp0.2 range between 1400 MPa and 1750 MPa,
- a Rm range between 1970 MPa and 2300 MPa
- a A50 range between 4 % and 8 %
- In this example a stainless steel strip according to the invention is compared to a conventional stainless steel strip. The composition of the investigated steels was as follows:
Conventional Inventive C 0.38 0.40 Si 0.36 0.42 Mn 0.48 0.56 Cr 13.1 13.4 Mo 0.98 0.99 N 0.017 0.052 V 0.009 0.055 Ni 0.31 0.15 P 0.018 0.018 S 0.0004 0.0006 - The cold rolled strips used for the hardening and tempering trials all had a thickness of 0.203 mm and a width of 140 mm. The strips were subjected to hardening and tempering in the above mentioned continuous hardening furnace. Tensile strength measurements were made according to ISO 6892:2009.
Fig. 1 discloses tensile properties as a function of the austenitising temperature.Fig. 2 discloses the tensile properties as a function of the tempering temperature. - The inventive steel strip can be used for producing flapper valves for compressors having improved properties.
Claims (12)
- A cold rolled and hardened martensitic/austenitic stainless steel strip for flapper valves in the compressors, wherein the steel stripa) is made from steel having the following composition in weight % (wt. %):
C 0.3 - 0.5 Si 0.2 - 0.8 Mn 0.2 - 1.0 Cr 12.0 - 15.0 Mo 0.50 - 2.00 N 0.02 - 0.15 V 0.01 - 0.20 Ni ≤ 2.0 Co ≤ 2.0 Cu ≤ 2.0 W ≤ 2.0 Al ≤ 0.05 Ti ≤ 0.05 Zr ≤ 0.05 Nb ≤ 0.05 Ta ≤ 0.05 B ≤ 0.01 Ca ≤ 0.009 REM ≤ 0.2 b) has a matrix consisting of tempered martensite and between 5 and 15 volume % austenite,c) has a tensile strength (Rm) of 1970-2300 MPa,d) has a thickness of 0.07- 3 mm and a width of ≤ 500 mm. - A strip according to claim 1 fulfilling at least one of the following requirements:
C 0.35 - 0.41 Si 0.30 - 0.60 Mn 0.40 - 0.65 Cr 13 - 14 Mo 0.8 - 1.2 N 0.03 - 0.13 V 0.02 - 0.10 Ni ≤ 0.5 Co ≤ 0.5 Cu ≤ 0.5 W ≤ 0.5 Al ≤ 0.01 Ti ≤ 0.01 Zr ≤ 0.01 Nb ≤ 0.01 Ta ≤ 0.01 B ≤ 0.001 Ca 0.0005 - 0.002 P ≤ 0.03 S ≤ 0.03 O ≤ 0.003 - A strip according to claim 1 or 2 fulfilling the following requirements:
C 0.35 - 0.41 Si 0.30 - 0.60 Mn 0.40 - 0.65 Cr 13 - 14 Mo 0.8 - 1.2 N 0.03 - 0.10 V 0.03 - 0.09 - A strip according to any of the preceding claims, fulfilling at least one of the following requirements:a tensile strength (Rm) of 2000-2200 MPa,a yield strength (RP0.2) of 1500-1750 MPa,a Vickers Hardness (HV1) of 570 - 650,a ductility A50 of 4-9 %.
- A strip according to any of the preceding claims, fulfilling the following requirements:reverse bending fatigue is > 850 MPa
- A strip according to any of the preceding claims having a thickness of 0.1 - 1.5 mm and/or a width of 5 - 150 mm.
- A strip according to any of the preceding claims, wherein the maximum globular inclusion size is 6 µm.
- A strip according to any of the preceding claims, wherein the primary inclusion species are Silicate type with a maximum width of 4 µm.
- A method of producing a strip according to any of claims 1-8, wherein the method comprises the following steps:a) Hot rolling a steel having a composition as defined in any of claims 1-3,b) Cold rolling the hot rolled strip to a thickness of 0.07-3mm,c) Continuously hardening and tempering the cold rolled strip,d) Optionally, slitting the cold rolled strip.
- A method according claim 9, wherein the austenitising temperature is 1000 - 1150 °C in step c) and wherein tempering temperature is 200 - 600 °C.
- A method according claim 9 or 10, wherein the hardening involves quenching the strip in a bath of molten lead or lead alloy, the bath preferably holding a temperature of 250 - 350 °C.
- A method according to any of claims 9-11, wherein the steel used is produced by powder metallurgy and wherein the maximum globular inclusion size of said steel is 6 µm.
Priority Applications (9)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP14196949.3A EP3031942B1 (en) | 2014-12-09 | 2014-12-09 | Stainless steel strip for flapper valves |
ES14196949.3T ES2643579T3 (en) | 2014-12-09 | 2014-12-09 | Stainless steel strip for flap valves |
CN201580003829.XA CN105934530B (en) | 2014-12-09 | 2015-12-08 | Stainless steel for flapper valves |
BR112016015645-5A BR112016015645B1 (en) | 2014-12-09 | 2015-12-08 | STAINLESS STEEL STRIP FOR HINGE VALVES |
US15/102,217 US9890436B2 (en) | 2014-12-09 | 2015-12-08 | Stainless steel strip for flapper valves |
PCT/SE2015/051316 WO2016093762A1 (en) | 2014-12-09 | 2015-12-08 | Stainless steel for flapper valves |
SG11201703857WA SG11201703857WA (en) | 2014-12-09 | 2015-12-08 | Stainless steel for flapper valves |
KR1020177018768A KR102274408B1 (en) | 2014-12-09 | 2015-12-08 | Stainless steel strip for flapper valves |
JP2016535110A JP6196381B2 (en) | 2014-12-09 | 2015-12-08 | Stainless steel strip for flapper valves |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP14196949.3A EP3031942B1 (en) | 2014-12-09 | 2014-12-09 | Stainless steel strip for flapper valves |
Publications (2)
Publication Number | Publication Date |
---|---|
EP3031942A1 true EP3031942A1 (en) | 2016-06-15 |
EP3031942B1 EP3031942B1 (en) | 2017-07-12 |
Family
ID=52015965
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP14196949.3A Revoked EP3031942B1 (en) | 2014-12-09 | 2014-12-09 | Stainless steel strip for flapper valves |
Country Status (2)
Country | Link |
---|---|
EP (1) | EP3031942B1 (en) |
ES (1) | ES2643579T3 (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107779778A (en) * | 2017-09-22 | 2018-03-09 | 钢铁研究总院 | A kind of rail fastener stainless steel spring material |
CN108380835A (en) * | 2018-04-17 | 2018-08-10 | 攀钢集团江油长城特殊钢有限公司 | The low segregation air valve steel continuous casting billet of one kind and its manufacturing method |
CN109778079A (en) * | 2017-11-13 | 2019-05-21 | 路肯(上海)医疗科技有限公司 | A kind of medical instrument stainless steel, production method, heat treatment method and application |
WO2020245285A1 (en) | 2019-06-05 | 2020-12-10 | Ab Sandvik Materials Technology | A martensitic stainless alloy |
EP3822380A4 (en) * | 2018-07-11 | 2022-04-13 | Hitachi Metals, Ltd. | Martensitic stainless steel strip and method for producing same |
Citations (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0533244A (en) * | 1991-07-19 | 1993-02-09 | Kanai Hiroyuki | Reed material for loom |
JPH08144023A (en) | 1994-11-16 | 1996-06-04 | Aichi Steel Works Ltd | Precipitation hardening type stainless steel excellent in strength, toughness, and corrosion resistance |
JPH09256116A (en) * | 1996-03-19 | 1997-09-30 | Nisshin Steel Co Ltd | High strength martensitic stainless steel excellent in antibacterial characteristic |
JPH1018002A (en) * | 1996-07-01 | 1998-01-20 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JPH1018001A (en) * | 1996-07-01 | 1998-01-20 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
US5714114A (en) * | 1995-01-13 | 1998-02-03 | Hitachi Metals, Ltd. | High hardness martensitic stainless steel with good pitting corrosion resistance |
JPH10110248A (en) * | 1996-10-03 | 1998-04-28 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JP2000129401A (en) | 1998-10-21 | 2000-05-09 | Nisshin Steel Co Ltd | High toughness skin pass-rolled martensitic stainless steel plate having high spring characteristic and its production |
JP2002194504A (en) | 2000-12-21 | 2002-07-10 | Sumitomo Metal Ind Ltd | Chromium stainless steel foil and production method of the same |
EP1739199A1 (en) * | 2005-06-30 | 2007-01-03 | OUTOKUMPU, Oyj | Martensitic stainless steel and method of the manufacture |
JP2008133499A (en) | 2006-11-27 | 2008-06-12 | Daido Steel Co Ltd | High-hardness martensitic stainless steel |
JP2009203528A (en) * | 2008-02-28 | 2009-09-10 | Nippon Steel & Sumikin Stainless Steel Corp | Martensitic stainless steel for loom member having excellent corrosion resistance and wear resistance, and method for producing steel strip thereof |
US20090301615A1 (en) * | 2006-01-26 | 2009-12-10 | Jacques Montagnon | Method for producing an internal combustion engine valve and valve obtained in this manner |
JP2010024486A (en) | 2008-07-17 | 2010-02-04 | Daido Steel Co Ltd | High-nitrogen martensitic stainless steel |
JP2011184780A (en) | 2010-03-10 | 2011-09-22 | Nisshin Steel Co Ltd | Stainless steel sheet with austenite-martensite dual-phase structure and method of producing the same |
CN102337461A (en) * | 2010-07-23 | 2012-02-01 | 宝山钢铁股份有限公司 | High-hardness martensitic stainless steel and its production method |
-
2014
- 2014-12-09 EP EP14196949.3A patent/EP3031942B1/en not_active Revoked
- 2014-12-09 ES ES14196949.3T patent/ES2643579T3/en active Active
Patent Citations (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0533244A (en) * | 1991-07-19 | 1993-02-09 | Kanai Hiroyuki | Reed material for loom |
JPH08144023A (en) | 1994-11-16 | 1996-06-04 | Aichi Steel Works Ltd | Precipitation hardening type stainless steel excellent in strength, toughness, and corrosion resistance |
US5714114A (en) * | 1995-01-13 | 1998-02-03 | Hitachi Metals, Ltd. | High hardness martensitic stainless steel with good pitting corrosion resistance |
JPH09256116A (en) * | 1996-03-19 | 1997-09-30 | Nisshin Steel Co Ltd | High strength martensitic stainless steel excellent in antibacterial characteristic |
JPH1018002A (en) * | 1996-07-01 | 1998-01-20 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JPH1018001A (en) * | 1996-07-01 | 1998-01-20 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JPH10110248A (en) * | 1996-10-03 | 1998-04-28 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JP2000129401A (en) | 1998-10-21 | 2000-05-09 | Nisshin Steel Co Ltd | High toughness skin pass-rolled martensitic stainless steel plate having high spring characteristic and its production |
JP2002194504A (en) | 2000-12-21 | 2002-07-10 | Sumitomo Metal Ind Ltd | Chromium stainless steel foil and production method of the same |
EP1739199A1 (en) * | 2005-06-30 | 2007-01-03 | OUTOKUMPU, Oyj | Martensitic stainless steel and method of the manufacture |
US20090301615A1 (en) * | 2006-01-26 | 2009-12-10 | Jacques Montagnon | Method for producing an internal combustion engine valve and valve obtained in this manner |
JP2008133499A (en) | 2006-11-27 | 2008-06-12 | Daido Steel Co Ltd | High-hardness martensitic stainless steel |
JP2009203528A (en) * | 2008-02-28 | 2009-09-10 | Nippon Steel & Sumikin Stainless Steel Corp | Martensitic stainless steel for loom member having excellent corrosion resistance and wear resistance, and method for producing steel strip thereof |
JP2010024486A (en) | 2008-07-17 | 2010-02-04 | Daido Steel Co Ltd | High-nitrogen martensitic stainless steel |
JP2011184780A (en) | 2010-03-10 | 2011-09-22 | Nisshin Steel Co Ltd | Stainless steel sheet with austenite-martensite dual-phase structure and method of producing the same |
CN102337461A (en) * | 2010-07-23 | 2012-02-01 | 宝山钢铁股份有限公司 | High-hardness martensitic stainless steel and its production method |
Non-Patent Citations (5)
Title |
---|
"440M", 13 April 2014 (2014-04-13), XP055557219, Retrieved from the Internet <URL:https://web.archive.Org/web/20140413193945/http://www.bircelik.com:80/440m_-830_tr_lc.html> |
"HARDNESS CONVERSION TABLE", 4 December 2014 (2014-12-04), XP055557226, Retrieved from the Internet <URL:https://web.archive.Org/web/20141204211436/http://www.magmaweld.com/hardness_conversion_table.html> |
"UGINE 4116N", DATASHEET, November 2005 (2005-11-01), XP055557221, Retrieved from the Internet <URL:https://web.archive.Org/web/20150421140442/http://bircelik.com/img/uploads/440M%20-%20440B%20-%20440C%20KIYASLAMASI.pdf> |
JACQUES ET AL.: "On measurement of retained austenite in multiple TRIP steels - results of blind round robin test involving six different techniques", MATERIALS SCIENCE AND TECHNOLOGY, vol. 25, no. 5, 2009, pages 567 - 574, XP055496371 |
TANAKA ET AL: "Effect of Surface Modification by Ion Implantation on Fatigue Behaviors of High Strength 13Cr Martensitic Stainless Steels", JOURNAL OF THE SOCIETY OF MATERIALS SCIENCE, vol. 42, no. 474, March 1993 (1993-03-01), pages 283 - 289, XP055557231 |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107779778A (en) * | 2017-09-22 | 2018-03-09 | 钢铁研究总院 | A kind of rail fastener stainless steel spring material |
CN109778079A (en) * | 2017-11-13 | 2019-05-21 | 路肯(上海)医疗科技有限公司 | A kind of medical instrument stainless steel, production method, heat treatment method and application |
CN108380835A (en) * | 2018-04-17 | 2018-08-10 | 攀钢集团江油长城特殊钢有限公司 | The low segregation air valve steel continuous casting billet of one kind and its manufacturing method |
CN108380835B (en) * | 2018-04-17 | 2020-03-27 | 攀钢集团江油长城特殊钢有限公司 | Low-segregation gas valve steel continuous casting billet and manufacturing method thereof |
EP3822380A4 (en) * | 2018-07-11 | 2022-04-13 | Hitachi Metals, Ltd. | Martensitic stainless steel strip and method for producing same |
US11814697B2 (en) | 2018-07-11 | 2023-11-14 | Proterial, Ltd. | Martensitic stainless steel strip and method for producing same |
WO2020245285A1 (en) | 2019-06-05 | 2020-12-10 | Ab Sandvik Materials Technology | A martensitic stainless alloy |
CN113966405A (en) * | 2019-06-05 | 2022-01-21 | 山特维克材料技术公司 | Martensitic stainless steel alloy |
Also Published As
Publication number | Publication date |
---|---|
ES2643579T3 (en) | 2017-11-23 |
EP3031942B1 (en) | 2017-07-12 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US9890436B2 (en) | Stainless steel strip for flapper valves | |
KR100912570B1 (en) | High-strength hot-dip galvanized steel sheet excellent in formability and method for producing same | |
JP4650013B2 (en) | Abrasion resistant steel plate with excellent low temperature toughness and method for producing the same | |
EP2520684B1 (en) | Austenite steel material having superior ductility | |
EP3031942B1 (en) | Stainless steel strip for flapper valves | |
CN111479945A (en) | Wear-resistant steel having excellent hardness and impact toughness and method for manufacturing same | |
JP2020536169A (en) | Use of stainless steel, pre-alloy powder and pre-alloy powder obtained by atomizing stainless steel | |
JP2009013439A (en) | High toughness high-speed tool steel | |
JP4645307B2 (en) | Wear-resistant steel with excellent low-temperature toughness and method for producing the same | |
CN113166901B (en) | Chromium-molybdenum steel plate with excellent creep strength and preparation method thereof | |
KR101301617B1 (en) | Material having high strength and toughness and method for forming tower flange using the same | |
JP4645306B2 (en) | Wear-resistant steel with excellent low-temperature toughness and method for producing the same | |
CN113966405A (en) | Martensitic stainless steel alloy | |
SE1551093A1 (en) | Stainless steel strip for flapper valves | |
JP2018159133A (en) | Cold work tool steel | |
RU2813064C1 (en) | Method for producing high-strength steel sheet | |
EP3980571A1 (en) | Steel strip for flapper valves | |
RU2477333C1 (en) | Low-carbon alloyed steel | |
JP2017190519A (en) | High strength spring steel having excellent corrosion resistance | |
KR101721587B1 (en) | Bainitic Steel For Automotive Hub With High Strength And High Toughness And Method For Manufacturing the Same | |
KR20230125712A (en) | Chromium-molybdenum steel having excellent strength and ductility and manufacturing the same | |
JP2002206147A (en) | Precipitation hardening martensitic stainless steel having excellent cold workability and high fatigue strength and production method therefor | |
CN112501491A (en) | Martensitic stainless steel alloy | |
EA041604B1 (en) | STAINLESS STEEL | |
JPH0539546A (en) | High strength and high corrosion resistance stainless steel excellent in cold workability |
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: 20150812 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
AX | Request for extension of the european patent |
Extension state: BA ME |
|
17Q | First examination report despatched |
Effective date: 20160808 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
INTG | Intention to grant announced |
Effective date: 20170102 |
|
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 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
INTC | Intention to grant announced (deleted) | ||
INTG | Intention to grant announced |
Effective date: 20170213 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
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 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 908393 Country of ref document: AT Kind code of ref document: T Effective date: 20170715 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602014011688 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20170712 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2643579 Country of ref document: ES Kind code of ref document: T3 Effective date: 20171123 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 4 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20171012 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: 20170712 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: 20170712 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: 20170712 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: 20170712 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: 20170712 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: T3 Ref document number: E 25523 Country of ref document: SK |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20170712 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: 20170712 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: 20171013 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: 20171112 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: 20171012 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: 20170712 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R026 Ref document number: 602014011688 Country of ref document: DE |
|
PLBI | Opposition filed |
Free format text: ORIGINAL CODE: 0009260 |
|
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: 20170712 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: 20170712 Ref country code: RO 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: 20170712 |
|
PLAX | Notice of opposition and request to file observation + time limit sent |
Free format text: ORIGINAL CODE: EPIDOSNOBS2 |
|
PLAB | Opposition data, opponent's data or that of the opponent's representative modified |
Free format text: ORIGINAL CODE: 0009299OPPO |
|
PLBB | Reply of patent proprietor to notice(s) of opposition received |
Free format text: ORIGINAL CODE: EPIDOSNOBS3 |
|
26 | Opposition filed |
Opponent name: AB SANDVIK MATERIALS TECHNOLOGY Effective date: 20180412 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20170712 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: 20170712 |
|
R26 | Opposition filed (corrected) |
Opponent name: AB SANDVIK MATERIALS TECHNOLOGY Effective date: 20180412 |
|
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: 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: 20170712 |
|
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: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171209 Ref country code: MT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171209 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20171231 |
|
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: 20171209 |
|
PLAB | Opposition data, opponent's data or that of the opponent's representative modified |
Free format text: ORIGINAL CODE: 0009299OPPO |
|
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: 20171231 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171231 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171231 |
|
R26 | Opposition filed (corrected) |
Opponent name: AB SANDVIK MATERIALS TECHNOLOGY Effective date: 20180412 |
|
TPAC | Observations filed by third parties |
Free format text: ORIGINAL CODE: EPIDOSNTIPA |
|
RDAF | Communication despatched that patent is revoked |
Free format text: ORIGINAL CODE: EPIDOSNREV1 |
|
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: 20170712 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: 20141209 |
|
APBM | Appeal reference recorded |
Free format text: ORIGINAL CODE: EPIDOSNREFNO |
|
APBP | Date of receipt of notice of appeal recorded |
Free format text: ORIGINAL CODE: EPIDOSNNOA2O |
|
APAH | Appeal reference modified |
Free format text: ORIGINAL CODE: EPIDOSCREFNO |
|
APBQ | Date of receipt of statement of grounds of appeal recorded |
Free format text: ORIGINAL CODE: EPIDOSNNOA3O |
|
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: 20170712 |
|
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: 20170712 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20170712 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20170712 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20201119 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20201210 Year of fee payment: 7 Ref country code: IT Payment date: 20201214 Year of fee payment: 7 Ref country code: GB Payment date: 20201218 Year of fee payment: 7 Ref country code: AT Payment date: 20201222 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SK Payment date: 20201110 Year of fee payment: 7 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R064 Ref document number: 602014011688 Country of ref document: DE Ref country code: DE Ref legal event code: R103 Ref document number: 602014011688 Country of ref document: DE |
|
APBU | Appeal procedure closed |
Free format text: ORIGINAL CODE: EPIDOSNNOA9O |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20201221 Year of fee payment: 7 Ref country code: ES Payment date: 20210102 Year of fee payment: 7 |
|
RDAG | Patent revoked |
Free format text: ORIGINAL CODE: 0009271 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: PATENT REVOKED |
|
REG | Reference to a national code |
Ref country code: FI Ref legal event code: MGE |
|
27W | Patent revoked |
Effective date: 20210520 |
|
GBPR | Gb: patent revoked under art. 102 of the ep convention designating the uk as contracting state |
Effective date: 20210520 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: MC4A Ref document number: E 25523 Country of ref document: SK Effective date: 20210520 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MA03 Ref document number: 908393 Country of ref document: AT Kind code of ref document: T Effective date: 20210520 |