EP0155011B2 - High-strength alloy for industrial vessels - Google Patents
High-strength alloy for industrial vessels Download PDFInfo
- Publication number
- EP0155011B2 EP0155011B2 EP85103129A EP85103129A EP0155011B2 EP 0155011 B2 EP0155011 B2 EP 0155011B2 EP 85103129 A EP85103129 A EP 85103129A EP 85103129 A EP85103129 A EP 85103129A EP 0155011 B2 EP0155011 B2 EP 0155011B2
- Authority
- EP
- European Patent Office
- Prior art keywords
- content
- alloy according
- alloy
- copper
- nickel
- 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.)
- Expired - Lifetime
Links
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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
- F28F21/081—Heat exchange elements made from metals or metal alloys
- F28F21/087—Heat exchange elements made from metals or metal alloys from nickel or nickel alloys
-
- 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
-
- 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
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28D—HEAT-EXCHANGE APPARATUS, NOT PROVIDED FOR IN ANOTHER SUBCLASS, IN WHICH THE HEAT-EXCHANGE MEDIA DO NOT COME INTO DIRECT CONTACT
- F28D21/00—Heat-exchange apparatus not covered by any of the groups F28D1/00 - F28D20/00
- F28D2021/0019—Other heat exchangers for particular applications; Heat exchange systems not otherwise provided for
- F28D2021/0059—Other heat exchangers for particular applications; Heat exchange systems not otherwise provided for for petrochemical plants
Definitions
- the instant invention relates to nickel-iron-chromium alloys in general and more particularly to a high strength, corrosion resistant alloy having a low work hardenability rate with variable age hardenable characteristics. Tne alloy reduces copper pick-up in fluid streams.
- the present invention provides an austenitic alloy having a low work hardening rate especially suitable for, but not limited to, industrial vessels and particularly for heat exchanger tubing for high temperature, high pressure appiications.
- the instant alloy combines improved corrosion resistance and the requisite high strength in a system that is of lower cost than the more expensive higher alloys.
- the alloy displays good stress corrosion cracking resistance and good high temperature corrosion resistance.
- an austenitic, age-hardenable nickel-iron-chromium alloy having a combination of high strength, low work-hardening rate, resistance to stress-corrosion cracking and resistance to corrosion by high-temperature deaerated water and by hydrochloric, sulphuric, phosphoric and polythionic acids consists, by weight, of from 24 to 32% nickel, from 15 to 18% chromium, from 1 to 3.5% molybdenum, from 2 to 5.5% copper, from 0.8 to 2.5% titanium, from 0 to 1.5% manganese, from 0 to 1.5% silicon, e.g.
- silicon from 0 to 1% niobium plus tantalum, from 0 to 2% aluminum, from 0 to 0.1% cerium, from 0 to 0.01% boron and from 0 to 0.2% nitrogen, the balance, apart from impurities, being iron.
- impurities used herein includes residual amounts of calcium added as a processing aid.
- the molybdenum content is advantageously from 1 to 3%, and the copper content from 2 to 5%.
- the nickel content is from 26 to 29%, the chromium content from 15 to 18%, the molybdenum content not more than 3%, the copper content not more than 5% and the content of niobium plus tantalum not more than 0.4%.
- the nickel is about 28%, the chromium about 16%, the molybdenum about 2% and the copper about 4%.
- the incorporation of a measured quantity of titanium can impart an age hardening response of at least 60 ksi (413 MPa) yield strength and 120 ksi (825 MPa) tensile strength in the cold worked and annealed conditions.
- the titanium raises the work hardening rate of the alloy. Copper, chromium and molybdenum improve the corrosion resistance of the alloy. Aluminum, cerium, boron and calcium assist in the deoxidation of the alloy.
- Nitrogen serves to boost the ability of the alloy to withstand corrosive attack. The nitrogen raises the strength and increases the work hardening rate of the alloy in the annealed condition.
- Table I below sets forth the compositions of a number of heats (Nos. 1-3 and 7-9) of alloys according to the invention within the above composition ranges and also, for purposes of comparison, one alloy (No 4) that is substantially free from copper and molybdenum, one alloy (No. 5) that is substantially free from copper, one alloy (No. 6) that is substantially free from molybdenum and titanium three alloys (Nos. 10-12) having lower titanium contents, and three alloys (Nos. 13-15) having lower nickel contents.
- Heats 1-3 and 12 were vacuum melted and cast to 4 inch (10 cm) diameter ingots. Forged 9/16 inch (1.43 cm) squares plus forged 3/4 x 2 x 12 inch (1.91 x 5.08 x 20.5 cm) flats were made with frequent reheats at 2150°F (1177°C). After overhauling the flats to a uniform thickness, they were hot rolled to 1/4 inch (0.64 cm) at 2150°F. The hot rolled 1/4 inch strip was annealed at 1950°F (1066°C)/one hour water quench and pickled prior to cold rolling. Hardness and tensile tests were taken at various levels of cold work to establish a work hardening response. A low work hardening rate is very desirable in the manufacture of relatively small diameter thin-walled tubing.
- the instant invention was developed with the attributes of good workability characteristics and ease of processing in mind.
- Table 5 shows the strength and ductility characteristics in the annealed and aged conditions.
- Corrosion tests were conducted on heats 4-12. Corrosion test environments relevant to feedwater heater service and other possible applications were examined.
- Table 6 depicts the SCC test results in sodium chloride and sodium hydroxide solutions.
- test data also indicates very good resistance of the alloys to polythionic acid cracking. This is a common cause of failure of stainless steels and high nickel alloys in petrochemical service. The influence of high titanium content on carbide precipitation is believed to be responsible for good polythionic acid SCC resistance.
- Table 7 shows general corrosion test results.
- Tables 6 and 7 also demonstrate the resistance of the alloy to environments other than that posed by feed- water heaters. Molybdenum addition of 2-3% greatly improves resistance to hydrochloric acid. Copper additions of 4% or more improved sulfuric acid resistance. The combination of copper and molybdenum appears to improve resistance to phosphoric acid. The instant alloy lends itself to chemical and petrochemical applications.
- the design strength of the alloys destined for tubular applications is usually based on the tensile strength of the alloy comprising the apparatus.- In the cold worked plus stress relieved conditions, the instant alloy system will meet the 824 MPa minimum tensile strength usually specified by design engineers. This value, compares favorably with such alloys as Inconel alloy 625 and Incoloy alloy 801. Table 8 compares minimum tubular wall thicknesses between MONEL alloy 400, 304 stainless and the instant alloy for various temperature and pressure conditions. Table 8 was constructed to compare the mini mum wall thickness between the listed alloys. The next heavier standard well thickness was used to calculate the weight per meter.
- the object or tube made by methods known to those skilled in the art, may be subjected to a stress relieving heat treatment of about 1100 to 1400°F (593-760°C) for an appropriate period of time.
- the time period is, of course, a function of the temperature selected and the section size.
- the non-age hardenable tubes may be drawn to final size, annealed at about 1700-2000°F (767-933°C) for a suitable time, straightened, bent into the appropriate shape (if desired), and stress relieved at about 593-760°C up to about three hours.
- the age-hardenable tubes may be drawn to final size, annealed at about 767-933°C for a suitable time, straightened, aged for about an hour at 593-760°C, bent into the appropriate shape and stress relieved (which also ages the tube) at about 593-760°C for the appropriate time.
- the pitting resistance of the alloy is about the same as stainless 304 and is not recommended for service where superior resistance to localized attack is required.
- the low chromium lowers resistance to intergranular attack and limits use in highly oxidizing environments such as nitric acid.
- a preferred composition for overall strength, corrosion resistance and economy for feedwater heaters is heat 8 (28 Ni - 16 Cr - 4 Cu - 1.8 Ti - 2 Mo - Bal Fe). This composition appears to have the mechanical and corrosion properties necessary for a high pressure material. It also has excellent general corrosion resistance in hydrochloric, sulfuric and phosphoric acids. The good resistance of this composition to polythionic acid attack also indicates potential petrochemical applications.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- General Engineering & Computer Science (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
- Rigid Pipes And Flexible Pipes (AREA)
- Heat-Exchange Devices With Radiators And Conduit Assemblies (AREA)
Description
- The instant invention relates to nickel-iron-chromium alloys in general and more particularly to a high strength, corrosion resistant alloy having a low work hardenability rate with variable age hardenable characteristics. Tne alloy reduces copper pick-up in fluid streams.
- Power plant operators and boiler manufacturers recognized early on that to improve the efficiency of stream generators (both fossil and nuclear), it was useful to adopt regenerative feedwater heating. Essentially, steam is extracted from the steam turbines to preheat the boi ler/reactor feedwater before it is introduced into the economizer of a boiler or directly into a steam generatorireactor. The heating of the feedwater occurs in, naturally enough, feedwater heaters. Steam is used to heat the feedwater inside the feedwater heater tubing to impart a portion of the steam's latent heat to the water. Water temperatures from about 100-650°F (37-343°C) and pressures up to 5200 psi (36 MPa) are not uncommon. Moroever, advanced designs are now contemplating pressures up to 7200 psi (49.6 MPa) and 700°F (371°C).
- Currently, steels (carbon and stainless) and sometimes nickel-copper alloys (MONEL* nickel-copper al- loysi are utiiized in feedwater heaters. Although the feedwater is treated to remove chemicals and other impurities, corrosion of the tubing may still occur.
- Free oxygen will attack the steels. Superalloys are often difficult to form into tubes due to their high work hardening rates. High copper-containing materials are generally frowned upon since copper and corrosion products are believed to deposit on boiler tubes and may be carried over into the steam. These undesirable entrained products may enter into the turbines resulting in lower efficiencies. Indeed, operators wish to eliminate all possible copper pick-up in the steam because of fouling and the resulting loss of efficiency of the turbine blades when the copper plates out of the steam. It is also believed that the copper deposits may set up local galvanic cells with the ferrous alloys thereby causing additional corrosion. Operators wish to stay away from nickel-copper alloys which otherwise display better chemical and physical properties than the other alloys. However, the substitution of low carbon or stainless steels for the nickel-copper alloys currently available is not always satisfactory since these materials do not have the requisite corrosion resistance, stress corrosion cracking resistance or strength. This leads to high maintenance costs. Moreover, in the case of carbon steels, undesirably short lifetimes of three to eight years have been reported. Contrast this state of affairs with an expected service life in excess of twenty years. Accordingly, power plant operators are in a quandry: steels corrode: high alloys are costly; and the nickel-copper alloys contain high quantities of copper.
- It is apparent that there is a need for a reasonable cost alloy that exhibits corrosion resistance, strength and formability properties suitable for feedwater heaters, chemical and petrochemical installations and other similar applications.
- It has been proposed in DE-A-21 35 180 to use a low-carbon chromium-nickel stainless steel containing 0.2 to 4% vanadium together with 0.3 to 4% copper and molybdenum for applications requiring good resistance to stress corrosion cracking.
- The present invention provides an austenitic alloy having a low work hardening rate especially suitable for, but not limited to, industrial vessels and particularly for heat exchanger tubing for high temperature, high pressure appiications. The instant alloy combines improved corrosion resistance and the requisite high strength in a system that is of lower cost than the more expensive higher alloys. The alloy displays good stress corrosion cracking resistance and good high temperature corrosion resistance.
- According to the invention, an austenitic, age-hardenable nickel-iron-chromium alloy having a combination of high strength, low work-hardening rate, resistance to stress-corrosion cracking and resistance to corrosion by high-temperature deaerated water and by hydrochloric, sulphuric, phosphoric and polythionic acids consists, by weight, of from 24 to 32% nickel, from 15 to 18% chromium, from 1 to 3.5% molybdenum, from 2 to 5.5% copper, from 0.8 to 2.5% titanium, from 0 to 1.5% manganese, from 0 to 1.5% silicon, e.g. less than 0.45% silicon, from 0 to 1% niobium plus tantalum, from 0 to 2% aluminum, from 0 to 0.1% cerium, from 0 to 0.01% boron and from 0 to 0.2% nitrogen, the balance, apart from impurities, being iron.
- The term impurities used herein includes residual amounts of calcium added as a processing aid.
- The molybdenum content is advantageously from 1 to 3%, and the copper content from 2 to 5%. Preferably the nickel content is from 26 to 29%, the chromium content from 15 to 18%, the molybdenum content not more than 3%, the copper content not more than 5% and the content of niobium plus tantalum not more than 0.4%. In one alloy according to the invention the nickel is about 28%, the chromium about 16%, the molybdenum about 2% and the copper about 4%.
- Owing to its low work hardening rate (caused in part by the nickel-chromium combinations) the instant
- *A trademark of the Inco family of companies.
- In the alloy of the invention, the incorporation of a measured quantity of titanium can impart an age hardening response of at least 60 ksi (413 MPa) yield strength and 120 ksi (825 MPa) tensile strength in the cold worked and annealed conditions. The titanium raises the work hardening rate of the alloy. Copper, chromium and molybdenum improve the corrosion resistance of the alloy. Aluminum, cerium, boron and calcium assist in the deoxidation of the alloy. Nitrogen serves to boost the ability of the alloy to withstand corrosive attack. The nitrogen raises the strength and increases the work hardening rate of the alloy in the annealed condition.
- Table I below sets forth the compositions of a number of heats (Nos. 1-3 and 7-9) of alloys according to the invention within the above composition ranges and also, for purposes of comparison, one alloy (No 4) that is substantially free from copper and molybdenum, one alloy (No. 5) that is substantially free from copper, one alloy (No. 6) that is substantially free from molybdenum and titanium three alloys (Nos. 10-12) having lower titanium contents, and three alloys (Nos. 13-15) having lower nickel contents.
- Other alloys used in comparative tests were commercial MONEL alloy 400 (nominal composition: 32.56% copper, 2.40% iron, 1.04% manganese, 0.1% silicon, 0.1% carbon, balance essentially nickel) and 304 stainless steel (nominal composition: 18.09% chromium, 9.18% nickel, 1.77% manganese, 0.73% silicon, 0.24% molybdenum, balance essentially iron).
-
- Heats 1-3 and 12 (14 kg melts) were vacuum melted and cast to 4 inch (10 cm) diameter ingots. Forged 9/16 inch (1.43 cm) squares plus forged 3/4 x 2 x 12 inch (1.91 x 5.08 x 20.5 cm) flats were made with frequent reheats at 2150°F (1177°C). After overhauling the flats to a uniform thickness, they were hot rolled to 1/4 inch (0.64 cm) at 2150°F. The hot rolled 1/4 inch strip was annealed at 1950°F (1066°C)/one hour water quench and pickled prior to cold rolling. Hardness and tensile tests were taken at various levels of cold work to establish a work hardening response. A low work hardening rate is very desirable in the manufacture of relatively small diameter thin-walled tubing.
- Of particular importance is the yield strength at high levels of cold reduction such as 60 to 80% reduction. Many tube mills produce a large hot-worked tube shell which must be reduced in size during a number of cold working and annealing stages. Experience has shown that alloys which have lower yield strength after high cold reductions may be cold worked to a greater degree without splitting, requiring less annealing stages and lower manufacturing costs.
- The instant invention was developed with the attributes of good workability characteristics and ease of processing in mind.
-
- When titanium was raised to 2.0%, the work hardening rate increased but no change occurred as titanium was raised to 2.3%. The aged tensile test results in Table 4 indicate that 414 MPa yield strength and 827 MPa tensile strength can be accomplished with approximately 1.75% titanium and low level cold working. Indeed, the combination of about 20% cold reduction with a slightly lower titanium content might be optimum for feed- water heaters.
-
- Corrosion tests were conducted on heats 4-12. Corrosion test environments relevant to feedwater heater service and other possible applications were examined.
-
- The tests show that the instant alloy is more resistant to SCC (caused by chlorides and sodium hydroxide) than 304 stainless. The relatively high nickel content of the instant alloys provides the increased chloride and caustic cracking resistance.
- The test data also indicates very good resistance of the alloys to polythionic acid cracking. This is a common cause of failure of stainless steels and high nickel alloys in petrochemical service. The influence of high titanium content on carbide precipitation is believed to be responsible for good polythionic acid SCC resistance.
- Table 7 shows general corrosion test results.
- Tables 6 and 7 also demonstrate the resistance of the alloy to environments other than that posed by feed- water heaters. Molybdenum addition of 2-3% greatly improves resistance to hydrochloric acid. Copper additions of 4% or more improved sulfuric acid resistance. The combination of copper and molybdenum appears to improve resistance to phosphoric acid. The instant alloy lends itself to chemical and petrochemical applications.
- The design strength of the alloys destined for tubular applications is usually based on the tensile strength of the alloy comprising the apparatus.- In the cold worked plus stress relieved conditions, the instant alloy system will meet the 824 MPa minimum tensile strength usually specified by design engineers. This value, compares favorably with such alloys as Inconel alloy 625 and Incoloy alloy 801. Table 8 compares minimum tubular wall thicknesses between MONEL alloy 400, 304 stainless and the instant alloy for various temperature and pressure conditions. Table 8 was constructed to compare the mini mum wall thickness between the listed alloys. The next heavier standard well thickness was used to calculate the weight per meter.
- In order to produce objects and, more particularly, tubes which may seamless or welded, the object or tube, made by methods known to those skilled in the art, may be subjected to a stress relieving heat treatment of about 1100 to 1400°F (593-760°C) for an appropriate period of time. The time period is, of course, a function of the temperature selected and the section size.
- In particular, the non-age hardenable tubes may be drawn to final size, annealed at about 1700-2000°F (767-933°C) for a suitable time, straightened, bent into the appropriate shape (if desired), and stress relieved at about 593-760°C up to about three hours. The age-hardenable tubes may be drawn to final size, annealed at about 767-933°C for a suitable time, straightened, aged for about an hour at 593-760°C, bent into the appropriate shape and stress relieved (which also ages the tube) at about 593-760°C for the appropriate time.
- It should be noted that due to the relatively low chromium content, the pitting resistance of the alloy is about the same as stainless 304 and is not recommended for service where superior resistance to localized attack is required. The low chromium lowers resistance to intergranular attack and limits use in highly oxidizing environments such as nitric acid.
- A preferred composition for overall strength, corrosion resistance and economy for feedwater heaters is heat 8 (28 Ni - 16 Cr - 4 Cu - 1.8 Ti - 2 Mo - Bal Fe). This composition appears to have the mechanical and corrosion properties necessary for a high pressure material. It also has excellent general corrosion resistance in hydrochloric, sulfuric and phosphoric acids. The good resistance of this composition to polythionic acid attack also indicates potential petrochemical applications.
Claims (10)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US59039384A | 1984-03-16 | 1984-03-16 | |
US590393 | 1984-03-16 |
Publications (4)
Publication Number | Publication Date |
---|---|
EP0155011A2 EP0155011A2 (en) | 1985-09-18 |
EP0155011A3 EP0155011A3 (en) | 1987-04-08 |
EP0155011B1 EP0155011B1 (en) | 1990-07-18 |
EP0155011B2 true EP0155011B2 (en) | 1994-07-06 |
Family
ID=24362074
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP85103129A Expired - Lifetime EP0155011B2 (en) | 1984-03-16 | 1985-03-18 | High-strength alloy for industrial vessels |
Country Status (9)
Country | Link |
---|---|
EP (1) | EP0155011B2 (en) |
JP (1) | JPS60211053A (en) |
KR (1) | KR900001561B1 (en) |
AU (1) | AU580758B2 (en) |
BR (1) | BR8501127A (en) |
CA (1) | CA1246902A (en) |
DE (1) | DE3578673D1 (en) |
ES (1) | ES8608055A1 (en) |
FI (1) | FI75869C (en) |
Families Citing this family (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3716665A1 (en) * | 1987-05-19 | 1988-12-08 | Vdm Nickel Tech | CORROSION RESISTANT ALLOY |
JP2002241900A (en) * | 1997-08-13 | 2002-08-28 | Sumitomo Metal Ind Ltd | Austenitic stainless steel having excellent sulfuric acid corrosion resistance and workability |
US5945067A (en) * | 1998-10-23 | 1999-08-31 | Inco Alloys International, Inc. | High strength corrosion resistant alloy |
US7815848B2 (en) | 2006-05-08 | 2010-10-19 | Huntington Alloys Corporation | Corrosion resistant alloy and components made therefrom |
JP5792905B2 (en) * | 2011-09-30 | 2015-10-14 | ユーオーピー エルエルシー | Method and apparatus for treating hydrocarbon streams |
KR20150060942A (en) * | 2012-10-30 | 2015-06-03 | 가부시키가이샤 고베 세이코쇼 | Austenitic stainless steel |
EP3495526A4 (en) * | 2016-08-03 | 2020-01-08 | Nippon Steel Corporation | Austenitic stainless steel |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB708820A (en) * | 1951-03-29 | 1954-05-12 | Carpenter Steel Co | Improvements in alloys |
GB812582A (en) * | 1956-07-18 | 1959-04-29 | Universal Cyclops Steel Corp | Ferrous base alloys |
ZA726262B (en) * | 1971-09-20 | 1973-06-27 | Int Nickel Ltd | Steels |
BE795564A (en) * | 1972-02-16 | 1973-08-16 | Int Nickel Ltd | CORROSION RESISTANT NICKEL-IRON ALLOY |
US4040876A (en) * | 1974-07-02 | 1977-08-09 | Westinghouse Electric Corporation | High temperature alloys and members thereof |
DE2528610A1 (en) * | 1974-07-02 | 1976-01-22 | Westinghouse Electric Corp | Iron-nickel-chromium alloy for fast breeder reactors - has high corrosion resistance to liq. sodium and low radiation-swelling |
-
1985
- 1985-03-11 AU AU39698/85A patent/AU580758B2/en not_active Ceased
- 1985-03-12 KR KR1019850001581A patent/KR900001561B1/en not_active IP Right Cessation
- 1985-03-13 BR BR8501127A patent/BR8501127A/en unknown
- 1985-03-15 FI FI851036A patent/FI75869C/en not_active IP Right Cessation
- 1985-03-15 ES ES541303A patent/ES8608055A1/en not_active Expired
- 1985-03-15 CA CA000476603A patent/CA1246902A/en not_active Expired
- 1985-03-16 JP JP60053213A patent/JPS60211053A/en active Granted
- 1985-03-18 DE DE8585103129T patent/DE3578673D1/en not_active Expired - Fee Related
- 1985-03-18 EP EP85103129A patent/EP0155011B2/en not_active Expired - Lifetime
Also Published As
Publication number | Publication date |
---|---|
DE3578673D1 (en) | 1990-08-23 |
EP0155011A3 (en) | 1987-04-08 |
BR8501127A (en) | 1985-11-05 |
JPH0525944B2 (en) | 1993-04-14 |
AU580758B2 (en) | 1989-02-02 |
CA1246902A (en) | 1988-12-20 |
FI851036L (en) | 1985-09-17 |
ES541303A0 (en) | 1986-06-01 |
EP0155011B1 (en) | 1990-07-18 |
EP0155011A2 (en) | 1985-09-18 |
KR900001561B1 (en) | 1990-03-15 |
FI75869B (en) | 1988-04-29 |
KR850007098A (en) | 1985-10-30 |
FI851036A0 (en) | 1985-03-15 |
ES8608055A1 (en) | 1986-06-01 |
JPS60211053A (en) | 1985-10-23 |
AU3969885A (en) | 1985-09-19 |
FI75869C (en) | 1988-08-08 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
AU609738B2 (en) | Corrosion resistant high strength nickel-base | |
EP0066361B1 (en) | Corrosion resistant high strength nickel-based alloy | |
US5879818A (en) | Nickel-based alloy excellent in corrosion resistance and workability | |
US4119765A (en) | Welded ferritic stainless steel articles | |
JP3355510B2 (en) | Austenitic alloys and their use | |
US5378427A (en) | Corrosion-resistant alloy heat transfer tubes for heat-recovery boilers | |
EP0155011B2 (en) | High-strength alloy for industrial vessels | |
US3516826A (en) | Nickel-chromium alloys | |
US4816217A (en) | High-strength alloy for industrial vessels | |
JP2002235154A (en) | HIGH Cr FERRITIC HEAT RESISTANT STEEL | |
JP3864437B2 (en) | High Mo nickel base alloy and alloy tube | |
CA1076396A (en) | Matrix-stiffened heat and corrosion resistant alloy | |
US4033767A (en) | Ductile corrosion resistant alloy | |
EP0384013A1 (en) | Method for strengthening coldworked nickel-base alloys | |
JP2643709B2 (en) | High corrosion resistant alloy for boiler heat transfer tubes | |
US3573034A (en) | Stress-corrosion resistant stainless steel | |
US4050928A (en) | Corrosion-resistant matrix-strengthened alloy | |
JPH0359135B2 (en) | ||
US3023098A (en) | Low carbon ferritic stainless steel | |
JPH05195127A (en) | Highly corrosion resistant alloy for heat exchanger tube of boiler | |
JP2001152293A (en) | HIGH Cr FERRITIC HEAT RESISTING STEEL | |
US2222621A (en) | Alloy steel article | |
JPS62180028A (en) | Mo-containing high cr-ni alloy having excellent corrosion resistance and pitting resistance | |
Sugahara | A Ni-45Cr-1Mo alloy for industrial cleaning agents such as a mixture of nitric and hydrofluoric acids | |
JPH07126814A (en) | Corrosion resistant alloy for heat exchanger tube for coal gasification plant |
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 |
|
AK | Designated contracting states |
Designated state(s): BE CH DE FR GB IT LI NL SE |
|
PUAL | Search report despatched |
Free format text: ORIGINAL CODE: 0009013 |
|
AK | Designated contracting states |
Kind code of ref document: A3 Designated state(s): BE CH DE FR GB IT LI NL SE |
|
17P | Request for examination filed |
Effective date: 19871007 |
|
17Q | First examination report despatched |
Effective date: 19881004 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): BE CH DE FR GB IT LI NL SE |
|
REF | Corresponds to: |
Ref document number: 3578673 Country of ref document: DE Date of ref document: 19900823 |
|
ET | Fr: translation filed | ||
ITF | It: translation for a ep patent filed |
Owner name: SOCIETA' ITALIANA BREVETTI S.P.A. |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: CH Payment date: 19910219 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 19910331 Year of fee payment: 7 |
|
PLBI | Opposition filed |
Free format text: ORIGINAL CODE: 0009260 |
|
26 | Opposition filed |
Opponent name: THYSSEN EDELSTAHLWERKE AG Effective date: 19910415 |
|
NLR1 | Nl: opposition has been filed with the epo |
Opponent name: THYSSEN EDELSTAHLWERKE AG |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 19920217 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 19920219 Year of fee payment: 8 |
|
ITTA | It: last paid annual fee | ||
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Effective date: 19920331 Ref country code: CH Effective date: 19920331 |
|
PLAB | Opposition data, opponent's data or that of the opponent's representative modified |
Free format text: ORIGINAL CODE: 0009299OPPO |
|
R26 | Opposition filed (corrected) |
Opponent name: THYSSEN EDELSTAHLWERKE AG Effective date: 19910415 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Effective date: 19921001 |
|
NLV4 | Nl: lapsed or anulled due to non-payment of the annual fee | ||
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 19930211 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 19930217 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 19930222 Year of fee payment: 9 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SE Effective date: 19930319 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Effective date: 19930331 |
|
BERE | Be: lapsed |
Owner name: INCO ALLOYS INTERNATIONAL INC. Effective date: 19930331 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Effective date: 19940318 |
|
PUAH | Patent maintained in amended form |
Free format text: ORIGINAL CODE: 0009272 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: PATENT MAINTAINED AS AMENDED |
|
27A | Patent maintained in amended form |
Effective date: 19940706 |
|
AK | Designated contracting states |
Kind code of ref document: B2 Designated state(s): BE CH DE FR GB IT LI NL SE |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 19940318 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DE Effective date: 19941201 |
|
EN3 | Fr: translation not filed ** decision concerning opposition | ||
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Effective date: 19941202 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST |
|
EUG | Se: european patent has lapsed |
Ref document number: 85103129.4 Effective date: 19931008 |