SE420623B - AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL - Google Patents
AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEELInfo
- Publication number
- SE420623B SE420623B SE7910719A SE7910719A SE420623B SE 420623 B SE420623 B SE 420623B SE 7910719 A SE7910719 A SE 7910719A SE 7910719 A SE7910719 A SE 7910719A SE 420623 B SE420623 B SE 420623B
- Authority
- SE
- Sweden
- Prior art keywords
- cardable
- austenitic
- exception
- aluminum steel
- steel
- Prior art date
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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Sealing Battery Cases Or Jackets (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Gasket Seals (AREA)
- Exhaust Silencers (AREA)
Description
15 20 25 30 35 1919719-9 Stålet smältes i en 10-ton högfrekvensugn, göts i kokiller och valsades till trâdämnen. Dessa har ämnesbehand- lats och valsats till tråd 0 6.0 mm av charge 3423-71 och 0 5.6 mm av charge #029-71. Normal glödgning vid 105000, bet- ning och syning har utförts innan tråden dragits. 15 20 25 30 35 1919719-9 The steel was melted in a 10-ton high-frequency furnace, cast in molds and rolled into wire blanks. These have been blank treated and rolled to wire 0 6.0 mm of charge 3423-71 and 0 5.6 mm of charge # 029-71. Normal annealing at 105000, pickling and sewing have been carried out before the wire is pulled.
Som jämförelse har en charge (3226-71) tillverkats på samma sätt i stål av typ 17-7 PHÅAISI 631), vilket_är ett ut- skiljningshärdande Cr-Ni-Al-stål med följande analys.For comparison, a batch (3226-71) has been manufactured in the same way in steel of type 17-7 PHÅAISI 631), which is a precipitation hardening Cr-Ni-Al steel with the following analysis.
Tabell 2 ___ë_Cha1"e E §iM_H-_Pi § 02 111212 H flLi 3226-71 .073 .74 .74 .013 .006 16.4 7.1 .l5 .0Ul .QR .09 Charge 3423-71 enligt tabell l och charge 3226-71 har dragits från valstråd 0 6.0 mm i enkeldrag. Brottgräns (Rm), sträckgräns (Re) och kontraktion (Z) jämföres i bifogade fig. l. Som synes ökar sträck- och brottgräns långsammare för le- geringen enligt uppfinningen (heldragen linje) vilket medför att dragbarheten mätt som areareduktíon ökar från 75% till 92%. Dessutom är duktiliteten mätt som kontraktion hela ti- den högre för legeringen enligt uppfinningen särskilt vid större reduktioner. Anmärkningsvärt är att materialet saknar spänningssprickor vid en så stor areareduktion som 92% jäm- fört med 17-7 PH där risken för spänningssprickor finns redan vid 45% reduktion.Table 2 ___ ë_Cha1 "e E §iM_H-_Pi § 02 111212 H fl Li 3226-71 .073 .74 .74 .013 .006 16.4 7.1 .l5 .0Ul .QR .09 Charge 3423-71 according to table l and charge 3226-71 The breaking limit (Rm), yield strength (Re) and contraction (Z) are compared in the attached Fig. 1. As can be seen, the yield strength and yield strength increase more slowly for the alloy according to the invention (solid line) which In addition, the ductility measured as contraction is always higher for the alloy according to the invention, especially at larger reductions. It is noteworthy that the material lacks stress cracks at as large an area reduction as 92%. brought with 17-7 PH where the risk of stress cracks is already at 45% reduction.
Den utskiljningshärdande effekten hos legeringen enligt uppfinningen har provats vid två olika reduktioner och givit resultaten enligt aabell 3 nedan.The precipitation hardening effect of the alloy according to the invention has been tested at two different reductions and has given the results according to Table 3 below.
Tabell 3 Rm N/mmz Re N/mmz Charge Dimension Reduktion Oanlöpt Anlöpt Oanlöpt Anlöpt mm % 0 3423-71 2.68 80.0 1810 1995 1830 1855 4029-71 1.83 89.4 2116 2525 1976 2357 Anlöpningstemperatur 95000 under 30 minuter.Table 3 Rm N / mmz Re N / mmz Charge Dimension Reduction Tempered Tempered Tempered Tempered mm% 0 3423-71 2.68 80.0 1810 1995 1830 1855 4029-71 1.83 89.4 2116 2525 1976 2357 Temperature temperature 95000 for 30 minutes.
Sçm synes får man en anlöpningseffekt på ca. 200 N/mm2 för charge 3423-71 och ca. 400 N/mmz för charge 4029-71. Den stora skillnaden mellan dessa effekter förklaras av att charge 3H23-71 ej.har reducerats tillräckligt före anlöpning, d.v.s. austeniten har ej i tillräcklig grad omvandlats till martensit. 1a' 15 20. 25 30 7910719-9 5 ° n Legeringen enligt uppfinningen har främst tagits fram- för att förbättra kallbearbetbarheten hos utskiljningshärdan- de rostfria cr-Ni-Al-srál. inom ytan Aßcn i fig. 2 kan man rikta analysen så att man vid glödgning i temperaturområdet 600-950°C får en höjning av Ms-temperaturen genom karbidut- skiljning. Därefter kan materialet släckas och eventuellt ky- las till temperaturer under rumstemperatur för att få en om- vandling till martensit som sedan kan anlöpas.It seems that you get a tempering effect of approx. 200 N / mm2 for charge 3423-71 and approx. 400 N / mmz for charge 4029-71. The large difference between these effects is explained by the fact that charge 3H23-71 has not been reduced sufficiently before tempering, i.e. the austenite has not been sufficiently converted to martensite. 1a '15 20. 25 30 7910719-9 5 ° n The alloy according to the invention has mainly been developed to improve the cold workability of precipitation-curing stainless cr-Ni-Al-srál. within the surface Aßcn in Fig. 2, the analysis can be directed so that when annealing in the temperature range 600-950 ° C, an increase in the Ms temperature is obtained by carbide precipitation. Thereafter, the material can be quenched and possibly cooled to temperatures below room temperature to obtain a conversion to martensite which can then be annealed.
En intressant tillämpning är särskilt kallstukning då så låga brotthållfastheter som SUG-560 N/mmz har uppmätta på material som glödgats vid temperaturen 105000. Detta gäller båda chargerna 3423-71 och H029-71.An interesting application is particularly cold spreading when such low breaking strengths as SUG-560 N / mmz have been measured on materials annealed at the temperature 105000. This applies to both charges 3423-71 and H029-71.
Den tekniska effekten hos uppfinningen framgår av att dragbarheten väsentligt förbättras samtidigt som man behåller en utskiljningshärdande effekt. Pâ goda grunder kan man för- moda att den goda svetsbarheten kan förbättras med tillsatser av zirkonium och uran i stället för titan. Då legeringen har en mycket trög martensitomvandling i glödgat tillstånd kan materialet lagras och transporteras utomhus vid kall väderlek utan risk för spontan martensitbildning. _ Krom och nickel skall ligga inom ytan ABCD enligt fig. 2 där krom delvis kan ersättas av molybden med upp till max 2% enligt formeln Cr' (kromekvivalenten) = % Cr + % Mo, varjämte nickel kan delvis ersättas av mangan enligt formeln Ni' (nickel- ekvivalenten) = % Ni + 1/2 (% Mn - 1%). Vid den speciellt före- dragna utföringsformen skall krom- och nickelekvivalenterna Cr' och Ni' ligga inom ytan abcd i_figur~g¿ Legeringen enligt uppfinningen glödgas inom temperatur- området 600-950°C, släckes och kyles under rumstemperatur.The technical effect of the invention is apparent from the fact that the drawability is significantly improved while maintaining a precipitation hardening effect. On good grounds, it can be assumed that good weldability can be improved with the addition of zirconium and uranium instead of titanium. As the alloy has a very slow martensite conversion in the annealed state, the material can be stored and transported outdoors in cold weather without the risk of spontaneous martensite formation. Chromium and nickel must be within the surface ABCD according to Fig. 2 where chromium can be partially replaced by molybdenum by up to a maximum of 2% according to the formula Cr '(chromium equivalent) =% Cr +% Mo, and nickel can be partially replaced by manganese according to formula Ni '(nickel equivalents) =% Ni + 1/2 (% Mn - 1%). In the particularly preferred embodiment, the chromium and nickel equivalents Cr 'and Ni' should be within the surface of the figure. The alloy according to the invention is annealed in the temperature range 600-950 ° C, quenched and cooled below room temperature.
Legeringen kan sedan utskiljningshärdas.The alloy can then be hardened by precipitation.
Legeringen kan också snabbkylas direkt efter varmvaïs- ning och kallbearbetas och utskiljningshärdas därefter.The alloy can also be quenched immediately after hot forging and cold worked and precipitation hardened thereafter.
Claims (2)
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE7910719A SE420623B (en) | 1979-12-28 | 1979-12-28 | AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL |
EP19800850186 EP0031800B1 (en) | 1979-12-28 | 1980-12-10 | Austenitic, precipitation hardenable stainless steel |
DE8080850186T DE3065923D1 (en) | 1979-12-28 | 1980-12-10 | Austenitic, precipitation hardenable stainless steel |
ES498616A ES498616A0 (en) | 1979-12-28 | 1980-12-24 | PROCEDURE FOR CONVERTING AUSTENITIC STEEL. |
JP18949080A JPS56105457A (en) | 1979-12-28 | 1980-12-27 | Austenite type precipitation hardening antiirust steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE7910719A SE420623B (en) | 1979-12-28 | 1979-12-28 | AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL |
Publications (2)
Publication Number | Publication Date |
---|---|
SE7910719L SE7910719L (en) | 1981-06-29 |
SE420623B true SE420623B (en) | 1981-10-19 |
Family
ID=20339661
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
SE7910719A SE420623B (en) | 1979-12-28 | 1979-12-28 | AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL |
Country Status (5)
Country | Link |
---|---|
EP (1) | EP0031800B1 (en) |
JP (1) | JPS56105457A (en) |
DE (1) | DE3065923D1 (en) |
ES (1) | ES498616A0 (en) |
SE (1) | SE420623B (en) |
Families Citing this family (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE8102015L (en) * | 1980-04-07 | 1981-10-08 | Armco Inc | FERRIT-FREE SEPARATION HARDENABLE STAINLESS STEEL |
JPS5993856A (en) * | 1982-11-18 | 1984-05-30 | Nippon Seisen Kk | Fine stainless steel wire |
SE466265B (en) * | 1990-05-29 | 1992-01-20 | Uddeholm Tooling Ab | EXCELLENT HANDLING TOOL STEEL |
DE102005024029B3 (en) * | 2005-05-23 | 2007-01-04 | Technische Universität Bergakademie Freiberg | Austenitic lightweight steel and its use |
DE102005030413C5 (en) * | 2005-06-28 | 2009-12-10 | Technische Universität Bergakademie Freiberg | High-strength austenitic-martensitic lightweight steel and its use |
DE102006033973A1 (en) * | 2006-07-20 | 2008-01-24 | Technische Universität Bergakademie Freiberg | Stainless austenitic cast steel and its use |
CN100464000C (en) * | 2007-06-12 | 2009-02-25 | 江阴康瑞不锈钢制品有限公司 | Austenite cold-forged stainless-steel and steel wire making method |
JP5744678B2 (en) * | 2010-10-07 | 2015-07-08 | 新日鐵住金ステンレス株式会社 | Precipitation hardening type metastable austenitic stainless steel wire excellent in fatigue resistance and method for producing the same |
CN102747307A (en) * | 2012-06-06 | 2012-10-24 | 兰州理工大学 | High aluminum stainless steel sheet material and rolling method |
CN103447348A (en) * | 2013-07-25 | 2013-12-18 | 张家港市胜达钢绳有限公司 | Manufacturing method of stainless steel wire |
SE541925C2 (en) | 2018-04-26 | 2020-01-07 | Suzuki Garphyttan Ab | A stainless steel |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2505762A (en) * | 1946-09-06 | 1950-05-02 | Armco Steel Corp | Stainless steel and method |
US3117861A (en) * | 1956-11-14 | 1964-01-14 | Armco Steel Corp | Stainless steel and article |
US3253908A (en) * | 1959-11-20 | 1966-05-31 | Armco Steel Corp | Stainless steel and method |
US3071460A (en) * | 1959-11-20 | 1963-01-01 | Armco Steel Corp | Stainless steel composition |
US3347663A (en) * | 1964-09-23 | 1967-10-17 | Int Nickel Co | Precipitation hardenable stainless steel |
US3408178A (en) * | 1967-06-27 | 1968-10-29 | Carpenter Steel Co | Age hardenable stainless steel alloy |
-
1979
- 1979-12-28 SE SE7910719A patent/SE420623B/en unknown
-
1980
- 1980-12-10 DE DE8080850186T patent/DE3065923D1/en not_active Expired
- 1980-12-10 EP EP19800850186 patent/EP0031800B1/en not_active Expired
- 1980-12-24 ES ES498616A patent/ES498616A0/en active Granted
- 1980-12-27 JP JP18949080A patent/JPS56105457A/en active Pending
Also Published As
Publication number | Publication date |
---|---|
SE7910719L (en) | 1981-06-29 |
EP0031800A1 (en) | 1981-07-08 |
ES8206655A1 (en) | 1982-08-01 |
EP0031800B1 (en) | 1983-12-14 |
DE3065923D1 (en) | 1984-01-19 |
ES498616A0 (en) | 1982-08-01 |
JPS56105457A (en) | 1981-08-21 |
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