EP0031800B1 - Austenitic, precipitation hardenable stainless steel - Google Patents
Austenitic, precipitation hardenable stainless steel Download PDFInfo
- Publication number
- EP0031800B1 EP0031800B1 EP19800850186 EP80850186A EP0031800B1 EP 0031800 B1 EP0031800 B1 EP 0031800B1 EP 19800850186 EP19800850186 EP 19800850186 EP 80850186 A EP80850186 A EP 80850186A EP 0031800 B1 EP0031800 B1 EP 0031800B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- austenitic
- steel
- stainless steel
- precipitation hardenable
- precipitation
- 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
Links
- 238000001556 precipitation Methods 0.000 title claims description 9
- 229910001220 stainless steel Inorganic materials 0.000 title claims description 4
- 239000010935 stainless steel Substances 0.000 title description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 14
- 229910000831 Steel Inorganic materials 0.000 claims description 14
- 239000010959 steel Substances 0.000 claims description 14
- 239000011651 chromium Substances 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052770 Uranium Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 239000002184 metal Substances 0.000 claims description 2
- 150000002739 metals Chemical class 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 claims 1
- 229910000734 martensite Inorganic materials 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 230000009467 reduction Effects 0.000 description 7
- 239000000463 material Substances 0.000 description 6
- 238000005496 tempering Methods 0.000 description 5
- 238000004881 precipitation hardening Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 238000004458 analytical method Methods 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- -1 chromium-nickel-aluminium Chemical compound 0.000 description 1
- 230000001143 conditioned effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000012925 reference material Substances 0.000 description 1
- 238000009877 rendering Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
- JFALSRSLKYAFGM-UHFFFAOYSA-N uranium(0) Chemical compound [U] JFALSRSLKYAFGM-UHFFFAOYSA-N 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
Definitions
- This invention deals with an austenitic stainless, precipitation hardenable chromium-nickel-aluminium steel with good cold workability. By tempering the martensite obtained by cold working, quenching or in some cases cooling to subzero temperatures, precipitation hardening is obtained.
- the new alloy can be produced as hot rolled products such as wire rod, bar, strip and plate.
- Precipitation hardening of stainless steel using aluminium is a well-known technique. These steels can either be given an annealing treatment designed to raise the M s temperature so much that martensite is formed on quenching, or they can be annealed at a higher temperature giving an austenitic structure when quenched. In the latter case the steel can be subsequently cold worked, thus transforming the austenite into martensite. After one of these treatments the material can be precipitation hardened.
- the main purpose of the present invention is thus to improve the workability in the cold condition of Cr-Ni-AI steels by lowering the M s and the M d30 temperatures sufficiently to ensure that good workability is obtained without at the same time lowering them so far that the austenite is not transformed to martensite when cold worked. Martensite is desirable in the final product since it raises the mechanical strength considerably.
- the steel contains either Ti up to 0.5% or Zr up to 0.5% or U up to 1%.
- Both heats were melted in a 10-ton high-frequency induction furnace, ingot teemed and rolled to billets. These were conditioned and rolled to wire rod, 0 6.0 mm for heat 3423-71 and 0 5.6 mm for heat 4029-71.
- the wire rod was subjected to a normal anneal at 1050°C, pickled and inspected before being drawn to wire.
- Heats 3423-71 (Table 1) and 3226-71 have been drawn from wire rod, 0 6.0 mm, using single drafts.
- the tensile strength (R m ), yield strength (R 8 ), and reduction of area (Z) as measured by tensile testing are compared in Figure 1. It is apparent that the yield and tensile strengths increase more slowly for the alloy in the invention (continuous curve) thus causing the drawability, measured as maximum achievable area reduction, to increase from 75% to 92%.
- the ductility measured as reduction of area is higher for the alloy in the invention over the whole range and particularly at large area reductions. It should be noted that stress cracks are completely absent in the material for area reductions as large as 92% compared with 17-7 PH where a definite risk of stress crack formation exists at area reductions as low as 45%.
- the tempering treatment gives an increase of yield and tensile strengths of about 200 N/mm 2 for heat 3423-71 and about 400 N/m M2 for heat 4029-71.
- the large difference between these effects can be explained by the fact that wire rod from heat 3421-71 has not been worked sufficiently, i.e. the austenite has not been transformed to martensite in sufficient quantities prior to tempering.
- the alloy in this invention has mainly been developed in order to improve the cold workability of precipitation hardenable stainless Cr-Ni-AI steels.
- the composition can be set so that annealing in the temperature range 600-900°C leads to a rise in the M s temperature due to carbide precipitation.
- the material can subsequently be cooled to ambient or subzero temperatures in order to obtain a transformation to martensite which can then be tempered.
- the technical result of the invention is that the drawability is considerably improved at the same time as the precipitation hardening effect is retained. It is reasonable to assume that the good weldability can be improved by additions of zirconium and uranium instead of titanium. Since the alloy has an extremely sluggish martensitic transformation in the annealed state the material can be stored and transported outdoors under cold weather conditions without risk of spontaneous martensite formation.
- the alloy according to the invention is annealed within the temperature range 600 ⁇ 950°C, quenched and cooled to below room temperature.
- the alloy can then be precipitation hardened by tempering.
- the alloy can also be quenched direct after hot rolling and subsequently cold worked and precipitation hardened by tempering.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Gasket Seals (AREA)
- Exhaust Silencers (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Sealing Battery Cases Or Jackets (AREA)
Description
- This invention deals with an austenitic stainless, precipitation hardenable chromium-nickel-aluminium steel with good cold workability. By tempering the martensite obtained by cold working, quenching or in some cases cooling to subzero temperatures, precipitation hardening is obtained. The new alloy can be produced as hot rolled products such as wire rod, bar, strip and plate.
- Precipitation hardening of stainless steel using aluminium is a well-known technique. These steels can either be given an annealing treatment designed to raise the Ms temperature so much that martensite is formed on quenching, or they can be annealed at a higher temperature giving an austenitic structure when quenched. In the latter case the steel can be subsequently cold worked, thus transforming the austenite into martensite. After one of these treatments the material can be precipitation hardened.
- The disadvantage with these steels is that the rate of martensite formation when cold working is extremely high, thus rendering the material difficult to work. The risk of stress cracks, for example, during the wire drawing process is extremely high.
- The main purpose of the present invention is thus to improve the workability in the cold condition of Cr-Ni-AI steels by lowering the Ms and the Md30 temperatures sufficiently to ensure that good workability is obtained without at the same time lowering them so far that the austenite is not transformed to martensite when cold worked. Martensite is desirable in the final product since it raises the mechanical strength considerably.
- An austenitic stainless steel according to the invention is characterized in that the chromium equivalent Cr' defined as Cr'=% Cr+% Mo lies between 16.5% and 18.2%, and the nickel equivalent Ni' defined as Ni'=% Ni+1/2 (% Mn-1%) lies between 8.25% and 9.75% said steel containing C up to 0.15%, Si up to 3.0%, Mn up to 8.0%, P up to 0.045%, S up to 0.040%, Mo up to 2.0%, N up to 0.15%, 0.5-2.5% AI and preferably one or more of the metals Ti, Zr and U up to 2%, with the balance of iron and impurities normally occurring in stainless steels.
- Preferably the steel contains either Ti up to 0.5% or Zr up to 0.5% or U up to 1%.
- Two production heats of the steel according to the invention with the following analyses have been made under production conditions.
- Both heats were melted in a 10-ton high-frequency induction furnace, ingot teemed and rolled to billets. These were conditioned and rolled to wire rod, 0 6.0 mm for heat 3423-71 and 0 5.6 mm for heat 4029-71. The wire rod was subjected to a normal anneal at 1050°C, pickled and inspected before being drawn to wire.
- As reference material a heat (3226-71) in steel of type 17-7 PH (AISI 631) has been produced by the same method. This is a precipitation hardenable Cr-Ni-Al-steel with the following heat analysis (Table 2).
- Heats 3423-71 (Table 1) and 3226-71 have been drawn from wire rod, 0 6.0 mm, using single drafts. The tensile strength (Rm), yield strength (R8), and reduction of area (Z) as measured by tensile testing are compared in Figure 1. It is apparent that the yield and tensile strengths increase more slowly for the alloy in the invention (continuous curve) thus causing the drawability, measured as maximum achievable area reduction, to increase from 75% to 92%. Moreover, the ductility measured as reduction of area is higher for the alloy in the invention over the whole range and particularly at large area reductions. It should be noted that stress cracks are completely absent in the material for area reductions as large as 92% compared with 17-7 PH where a definite risk of stress crack formation exists at area reductions as low as 45%.
- The precipitation hardening effect of the alloy in the invention has been tested for two different area reductions and the results are shown below in Table 3.
- Thus, the tempering treatment gives an increase of yield and tensile strengths of about 200 N/mm2 for heat 3423-71 and about 400 N/m M2 for heat 4029-71. The large difference between these effects can be explained by the fact that wire rod from heat 3421-71 has not been worked sufficiently, i.e. the austenite has not been transformed to martensite in sufficient quantities prior to tempering.
- The alloy in this invention has mainly been developed in order to improve the cold workability of precipitation hardenable stainless Cr-Ni-AI steels. Within the area abcd in Figure 2, the composition can be set so that annealing in the temperature range 600-900°C leads to a rise in the Ms temperature due to carbide precipitation. The material can subsequently be cooled to ambient or subzero temperatures in order to obtain a transformation to martensite which can then be tempered.
- A particularly interesting application is cold heading where tensile strengths as low as 540-560 N/mm2 have been measured on material annealed at 1050°C. This is true for both heats 3423-71 and 4029-71.
- The technical result of the invention is that the drawability is considerably improved at the same time as the precipitation hardening effect is retained. It is reasonable to assume that the good weldability can be improved by additions of zirconium and uranium instead of titanium. Since the alloy has an extremely sluggish martensitic transformation in the annealed state the material can be stored and transported outdoors under cold weather conditions without risk of spontaneous martensite formation.
- Chromium and nickel equivalents should lie within the area abcd as shown in Figure 2 where chromium can be partly replaced by molybdenum with up to 2%, and nickel can be partly replaced by manganese according to the formula % Ni=1/2(% Mn-1 %).
- The alloy according to the invention is annealed within the temperature range 600―950°C, quenched and cooled to below room temperature. The alloy can then be precipitation hardened by tempering.
- The alloy can also be quenched direct after hot rolling and subsequently cold worked and precipitation hardened by tempering.
Claims (2)
1. Austenitic, precipitation hardenable, stainless Cr-Ni-AI steel with good cold workability characterized in that the chromium equivalent Cr' defined as Cr'=% Cr+% Mo lies between 16.5% and 18.2%, and the nickel equivalent Ni' defined as Ni'=% Ni+1/2(% Mn-1%) lies between 8.25% and 9.75%, said steel containing Ni at least 5%, C up to 0.15%, Si up to 3.0%, Mn up to 8.0%, P up to 0.045%, S up to 0.040%, Mo up to 2.0%, N up to 0.15%, 0.5-2.5% AI and preferably one or more of the metals Ti, Zr and U up to 2%, with the balance of iron and impurities normally occurring in stainless steels.
2. Steel according to claim 1, characterized in that it contains either Ti up to 0.5% or Zr up to 0.5% or U up to 1%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE7910719A SE420623B (en) | 1979-12-28 | 1979-12-28 | AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL |
| SE7910719 | 1979-12-28 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP0031800A1 EP0031800A1 (en) | 1981-07-08 |
| EP0031800B1 true EP0031800B1 (en) | 1983-12-14 |
Family
ID=20339661
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP19800850186 Expired EP0031800B1 (en) | 1979-12-28 | 1980-12-10 | Austenitic, precipitation hardenable stainless steel |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP0031800B1 (en) |
| JP (1) | JPS56105457A (en) |
| DE (1) | DE3065923D1 (en) |
| ES (1) | ES8206655A1 (en) |
| SE (1) | SE420623B (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2006125412A1 (en) | 2005-05-23 | 2006-11-30 | Scheller Piotr R | Austenitic lightweight steel and use thereof |
| DE102005030413B3 (en) * | 2005-06-28 | 2007-03-15 | Technische Universität Bergakademie Freiberg | High-strength austenitic-martensitic lightweight steel and its use |
Families Citing this family (9)
| 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 |
| 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 |
| US3071460A (en) * | 1959-11-20 | 1963-01-01 | Armco Steel Corp | Stainless steel composition |
| US3253908A (en) * | 1959-11-20 | 1966-05-31 | Armco Steel Corp | Stainless steel and method |
| 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 EP EP19800850186 patent/EP0031800B1/en not_active Expired
- 1980-12-10 DE DE8080850186T patent/DE3065923D1/en not_active Expired
- 1980-12-24 ES ES498616A patent/ES8206655A1/en not_active Expired
- 1980-12-27 JP JP18949080A patent/JPS56105457A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2006125412A1 (en) | 2005-05-23 | 2006-11-30 | Scheller Piotr R | Austenitic lightweight steel and use thereof |
| DE102005030413B3 (en) * | 2005-06-28 | 2007-03-15 | Technische Universität Bergakademie Freiberg | High-strength austenitic-martensitic 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 |
Also Published As
| Publication number | Publication date |
|---|---|
| ES498616A0 (en) | 1982-08-01 |
| SE7910719L (en) | 1981-06-29 |
| ES8206655A1 (en) | 1982-08-01 |
| DE3065923D1 (en) | 1984-01-19 |
| EP0031800A1 (en) | 1981-07-08 |
| SE420623B (en) | 1981-10-19 |
| JPS56105457A (en) | 1981-08-21 |
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