WO1996014447A1 - Use of a nonmagnetic stainless steel - Google Patents
Use of a nonmagnetic stainless steel Download PDFInfo
- Publication number
- WO1996014447A1 WO1996014447A1 PCT/SE1995/001289 SE9501289W WO9614447A1 WO 1996014447 A1 WO1996014447 A1 WO 1996014447A1 SE 9501289 W SE9501289 W SE 9501289W WO 9614447 A1 WO9614447 A1 WO 9614447A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- stainless steel
- magnetic
- equiv
- aisi
- alloys
- Prior art date
Links
Classifications
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Definitions
- the present invention relates to the use of a non-magnetic high strength stainless steel for the manufacture of super conducting magnet components such as magnet collars used in particle accelerator apparatuses.
- non-stable austenitic spring steels SS2331 with a typical nominal analysis of 17 Cr, 7 Ni, 0.8 Si, 1.2 Mn, 0.1 C and
- the optimized composition (in weight-%) of the alloy of the present invention in its broadest aspect is as follows:
- N 0.10-0.50 The remainder being Fe and normal impurities.
- Cr content should be high in order to achieve good corrosion resistance.
- the alloy can, to advantage, be annealed and precipitate high chromium containing nitrides.
- the Cr content should exceed 16 %. Since Cr is a ferrite stabilizing element, the presence of very high Cr contents with lead to the presence of ferromagnetic ferrite.
- the Cr content should therefore be less than 21 %, preferably less than 19 %.
- Ni is a very efficient austenite stabilizing element. Ni also increases austenite stability against deformation into martensite. In order to achieve a sufficiently stable non ⁇ magnetic structure the Ni-content should exceed 6 % and preferably exceed 7 %. In order to achieve high strength after cold working the Ni-content should not exceed 10 %.
- Mn has beside an austenite stabilizing effect the important -ability of providing solubility of nitrogen, both in melted and solid phases.
- the Mn-content should therefore exceed 3.5 %.
- Production of the testing materials included melting in a high-frequency induction furnace and casting to ingots at about 1600°C. These ingots were heated to about 1200°C and hot worked by forging the material into bars. The materials were then subjected to hot rolling into strips which thereafter were quench annealed and clean pickled. The quench anneal was carried out at about 1080°C and quenching occurred in water.
- the strips obtained after quench annealing were then cold rolled to various amounts of reduction after which test samples were taken out for various tests. In order to avoid variations in temperature and their possible impact on magnetic properties the samples were cooled to room temperature after each cold rolling step.
- Table 1 Chemical analysis, in weight-%, of testing material.
- Table 2 shows that with alloys of the invention very high strength levels can be obtained at cold working.
- AISI 305 appears to show a substantially slower work hardening due to its low contents of dissolved alloy elements, i.e. nitrogen and carbon, combined with rather high nickel content.
- this material whilst exhibiting high strength, also has as low magnetic permeability as possible, i.e. close to 1.
- Table 3 shows the magnetic permeability depending upon field strength for the various alloys after 75 % cold reduction and annealing at 450°C/2 h. Table 3. Permeability values of test alloys. Underlined values indicate maximal measured permeability. The value at the bottom indicates tensile strength in corresponding condition. * alloys of the invention ** comparison samples
- Table 3 shows that with alloys of this invention it is possible, by coldworking and precipitation hardening, to achieve high strength exceeding 1700 or even 1800 MPa combined with very low values of the magnetic permeability ⁇ 1.05.
- the reference alloys with compositions outside the scope of this invention and the reference steels AISI 304 and AISI 305 appear to be too unstable in austenite, or appear to have an insufficient degree of work hardening.
- the relative magnetic permeability coefficient has been measured to a value below 1.005 for temperatures down to 4.2 K or even 1.8 K.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Physics & Mathematics (AREA)
- Materials Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Electromagnetism (AREA)
- Hard Magnetic Materials (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
- Heat Treatment Of Steel (AREA)
- Emergency Protection Circuit Devices (AREA)
Abstract
The invention advises use of a stainless steel alloy as construction material in superconducting magnetic components, said alloy containing in weight percent 0.05-0.25 % C, 0.1-1.5 %, Si, 3.5-7.5 % Mn, 17-21 % Cr, 6-10 % Ni, 0.10-0.50 % N, the remainder being Fe and normal impurities.
Description
Use of a nonmagnetic stainless steel
The present invention relates to the use of a non-magnetic high strength stainless steel for the manufacture of super conducting magnet components such as magnet collars used in particle accelerator apparatuses.
The rapid development of research within various advanced physical laboratories has created an increased demand for more sophisticated materials with combinations of properties not previously considered or easily achievable such as, for example the combination of high mechanical strength and a non-magnetic structure for materials to be used in applications where the material is required to be magnetically inert also at low temperatures.
Among high strength steels, the so-called non-stable austenitic spring steels, SS2331 with a typical nominal analysis of 17 Cr, 7 Ni, 0.8 Si, 1.2 Mn, 0.1 C and
0.03 N are in a special position because of their combination of high strength and good corrosion properties.
Thanks to a systematic development work it has now been found that it is possible, by a carefully selected composition, to achieve, by cold working, a specific deformation hardening effect while preserving a non-magnetic structure. In addition, it has been found possible without affecting the magnetic properties, to provide precipitation hardening of the alloy such that a very high strength combined with low magnetic permeability and good thermal contraction values is achieved at very low temperatures.
The optimized composition (in weight-%) of the alloy of the present invention in its broadest aspect is as follows:
C: 0.05-0.25 Si: 0.1-1.5
Mn: 3.5-7.5
Cr: 17-21
Ni: 6-10
N: 0.10-0.50
The remainder being Fe and normal impurities.
Cr content should be high in order to achieve good corrosion resistance. The alloy can, to advantage, be annealed and precipitate high chromium containing nitrides. In order to reduce the tendency for excessive local reduction of Cr-content with the non- stabilization of the austenite phase and reduction in corrosion resistance the Cr content should exceed 16 %. Since Cr is a ferrite stabilizing element, the presence of very high Cr contents with lead to the presence of ferromagnetic ferrite. The Cr content should therefore be less than 21 %, preferably less than 19 %.
Ni is a very efficient austenite stabilizing element. Ni also increases austenite stability against deformation into martensite. In order to achieve a sufficiently stable non¬ magnetic structure the Ni-content should exceed 6 % and preferably exceed 7 %. In order to achieve high strength after cold working the Ni-content should not exceed 10 %.
Mn has beside an austenite stabilizing effect the important -ability of providing solubility of nitrogen, both in melted and solid phases. The Mn-content should therefore exceed 3.5 %. High amounts of Mn, however, reduce the corrosion resistance in chloride containing environments and should therefore not exceed 7.5 %.
The amounts of the various components of the alloy should be selected such that the nickel equivalent calculated as Ni-equiv = Ni + 30 C + 0.5 Mn + 25 N, and the chromium equivalent calculated as Cr-equiv = Cr + Mo + 1.5 Si both amount to values in the range 16-22, preferably 18-20.
The invention will in the following be disclosed by way of results from research carried out whereby further details about mechanical properties and magnetic properties will be disclosed.
Example
Production of the testing materials included melting in a high-frequency induction
furnace and casting to ingots at about 1600°C. These ingots were heated to about 1200°C and hot worked by forging the material into bars. The materials were then subjected to hot rolling into strips which thereafter were quench annealed and clean pickled. The quench anneal was carried out at about 1080°C and quenching occurred in water.
The strips obtained after quench annealing were then cold rolled to various amounts of reduction after which test samples were taken out for various tests. In order to avoid variations in temperature and their possible impact on magnetic properties the samples were cooled to room temperature after each cold rolling step.
Table 1 : Chemical analysis, in weight-%, of testing material.
* alloys of the invention
** comparison samples
Steel No. C Si Mn Cr Ni Mo Al N
869* 0.11 0.69 4.29 18.52 - - - 0.27 880* 0.052 0.89 3.82 20.25 10.01 - - 0.29
866** 0.11 0.83 1.49 18.79 9.47 - - 0.20
AISI** 0.034 0.59 1.35 18.56 9.50 - - 0.17 304
AISI** 0.042 0.42 1.72 18.44 11.54 - - 0.036 305
P, S < 0.030 weight-% is valid for all alloys above.
The strength of the alloys when subjected to uniaxial tensile testing as function of cold working degree appears from Table 2, where R- 0.05 and R_ 0.2 correspond to the load that gives 0.05 % and 0.2 % remaining elongation, and where R.., corresponds with the maximum load value in the load-elongation diagram and where A10 corresponds with ultimate elongation.
Table 2. Yield point, tensile strength and elongation of testing materials. * alloys of the invention ** comparison samples
Steel No. Condition R-.0.05 RpO.2. Rm A10
MPa MPa MPa %
869* 35 % reduction 792 1062 1203 9
50 1007 1311 1464 6
75 1082 1434 1638 4
880* 35 836 1086 1208 7
50 1025 1288 1410 5
75 985 1343 '1566 4
866** 35 796 1036 1151 8
50 986 1239 1366 5
75 997 1356 1558 4
AISI** 35 683 912 1080 9
304 50 841 1127 1301 6
75 910 1300 1526 5
AISI** 35 555 701 791 15
305 50 841 1042 1139 6
75 868 1177 1338 5
Table 2 shows that with alloys of the invention very high strength levels can be obtained at cold working. AISI 305 appears to show a substantially slower work hardening due to its low contents of dissolved alloy elements, i.e. nitrogen and carbon, combined with rather high nickel content.
For a material according to this invention there is the requirement that this material, whilst exhibiting high strength, also has as low magnetic permeability as possible, i.e. close to 1.
Table 3 shows the magnetic permeability depending upon field strength for the various alloys after 75 % cold reduction and annealing at 450°C/2 h.
Table 3. Permeability values of test alloys. Underlined values indicate maximal measured permeability. The value at the bottom indicates tensile strength in corresponding condition. * alloys of the invention ** comparison samples
Field strength Steel No. Oersted
869* 880* 866 ** AISI AISI 304** 305**
25 1.0350
50 1.0389 1.0099 1.0346 1.5231 1.0593
100 1.0372 1.0118 1.0248 1.8930 1.0666
150 1.0359 1.0115 1.0413 2.1056 1.0688
200 1.0350 1.0110 1.0505 2.2136 1.0729
300 1.0329 1.0099 1.0640 2.2258 1.0803
400 1.0322 1.0089 1.0754 2.1506 1.0855
500 1.0321 1.0081 1.0843 2.0601 1.0884
700 - 1.0071 1.0917 1.0859
1000 - 1.0882
Rm MPa 1840 1740 1720 1644 1380
Table 3 shows that with alloys of this invention it is possible, by coldworking and precipitation hardening, to achieve high strength exceeding 1700 or even 1800 MPa combined with very low values of the magnetic permeability < 1.05. The reference alloys with compositions outside the scope of this invention and the reference steels AISI 304 and AISI 305 appear to be too unstable in austenite, or appear to have an insufficient degree of work hardening.
As appears from the results in Table 4 it is impossible with alloys of this invention, by cold working and precipitation hardening, to achieve a strength exceeding 1700 MPa combined with very low values of the magnetic permeability of < 1.05. The reference steels AISI 304 and AISI 305 appear to be too unstable in austenite, and alloys 866 and
AISI 304 appear to be magnetic at high strength or appear to have an insufficient degree of work-hardening.
As a further result of such material having low values of magnetic permeability it was found that such material also possesses a desirable degree of thermal contraction value at low temperatures. Conducted measurements have shown that integrated thermal contraction for a temperature range 77K-300K is about 0.25 %.
Further, for the material in the annealed or slightly cold rolled conditions (tensile strength ~ 1000 N/mm2) the relative magnetic permeability coefficient has been measured to a value below 1.005 for temperatures down to 4.2 K or even 1.8 K.
Measurements have been carried out on a material with following anah sis with amounts given in weight-%:
c si Mn Cr Ni N
0.11 0.8 6.0 18.5 7.2 0.-25
the remainder being Fe and normal impurities.
Table 4.
Condition Temp. K R-, 0.2 Rm
Annealed 293 475 850 N/mm2
77 1090 1620
Cold rolled 293 1375 1630
77 1820 2385
Claims
1. Use of a non-magnetic, stainless steel alloy having high strength, consisting essentially of, in percent by weight:
C: 0.05-0.25
Si: 0.1-1.5
Mn: 3.5-7.5
Cr: 17-21 Ni: 6-10
N: 0.10-0.50
the remainder being Fe and normal impurities, as material for the manufacture of superconducting magnet components to satisfy demands on low magnetic permeability and good thermal contraction values at low temperatures.
2. Use of a non-magnetic stainless steel as defined in claim 1, characterized in that the alloy contains 17-19 % Cr and 7-10 % Ni.
3. Use of a non-magnetic stainless steel as defined in claim 1 or 2, characterized in that the contents of the alloying elements are so adjusted that the following conditions are fulfilled:
Cr-equiv = Cr + Mo + 1.15 Si = 16-22. Ni-equiv = Ni + 30 C + 0.5 Mn + 25 N = 16-22.
4. Use of a non-magnetic stainless steel as defined in any of the claims 1-3, characterized in that the contents of the alloying elements are so adjusted that the following conditions are fulfilled:
Cr-equiv = Cr + Mo + 1.5 Si + 0.5 Nb = 18-20. Ni-equiv = Ni + 30 C + 0.5 Mn + 25 N = 18-20.
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP95936833A EP0783595B1 (en) | 1994-11-02 | 1995-10-31 | Use of a nonmagnetic stainless steel |
JP8515240A JPH10508658A (en) | 1994-11-02 | 1995-10-31 | Applications of non-magnetic stainless steel |
DE69519677T DE69519677T2 (en) | 1994-11-02 | 1995-10-31 | USE OF NON-MAGNETIC, STAINLESS STEEL |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE9403749A SE506550C2 (en) | 1994-11-02 | 1994-11-02 | Use of an non-magnetic stainless steel in superconducting low temperature applications |
SE9403749-6 | 1994-11-02 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO1996014447A1 true WO1996014447A1 (en) | 1996-05-17 |
Family
ID=20395822
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/SE1995/001289 WO1996014447A1 (en) | 1994-11-02 | 1995-10-31 | Use of a nonmagnetic stainless steel |
Country Status (7)
Country | Link |
---|---|
US (1) | US5951788A (en) |
EP (1) | EP0783595B1 (en) |
JP (2) | JPH10508658A (en) |
DE (1) | DE69519677T2 (en) |
ES (1) | ES2154350T3 (en) |
SE (1) | SE506550C2 (en) |
WO (1) | WO1996014447A1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2058415A1 (en) * | 2007-11-09 | 2009-05-13 | General Electric Company | Forged Austenitic Stainless Steel Alloy Components and Method Therefor |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3408203B2 (en) * | 1999-07-08 | 2003-05-19 | 日興商事株式会社 | Automatic opening bag making method and apparatus |
US6488668B1 (en) * | 2000-11-16 | 2002-12-03 | Ideal Instruments, Inc. | Detectable heavy duty needle |
EP2813906A1 (en) * | 2013-06-12 | 2014-12-17 | Nivarox-FAR S.A. | Part for clockwork |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0254787A1 (en) * | 1986-07-28 | 1988-02-03 | Manoir Industries | Stainless, austenitic and amagnetic steel |
SE466919B (en) * | 1990-02-26 | 1992-04-27 | Sandvik Ab | Non-magnetic, non-rusting Mn-Cr-Ni-N-steel alloy |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4819806B2 (en) * | 1971-04-19 | 1973-06-16 | ||
IT1108126B (en) * | 1977-11-30 | 1985-12-02 | Fischer Ag Georg | ALLOY FOR NON MAGENTIZABLE AUSTENITIC STEEL JETS |
JPS56158851A (en) * | 1980-05-14 | 1981-12-07 | Aichi Steel Works Ltd | High-strength austenite stainless steel |
JPS62103348A (en) * | 1985-10-31 | 1987-05-13 | Kawasaki Steel Corp | Nonmagnetic austenitic stainless steel having superior weldability and working stability |
JPS62240749A (en) * | 1986-04-14 | 1987-10-21 | Yoshiaki Kanai | Low permeability stainless steel |
JPS64254A (en) * | 1987-03-11 | 1989-01-05 | Nippon Steel Corp | High-hardness nonmagnetic stainless steel |
SE506886C2 (en) * | 1990-02-26 | 1998-02-23 | Sandvik Ab | Vanadium-alloyed precipitable, non-magnetic austenitic steel |
JP2715033B2 (en) * | 1992-12-28 | 1998-02-16 | 新日本製鐵株式会社 | Non-magnetic PC steel wire and method of manufacturing the same |
-
1994
- 1994-11-02 SE SE9403749A patent/SE506550C2/en not_active IP Right Cessation
-
1995
- 1995-10-31 JP JP8515240A patent/JPH10508658A/en not_active Withdrawn
- 1995-10-31 ES ES95936833T patent/ES2154350T3/en not_active Expired - Lifetime
- 1995-10-31 DE DE69519677T patent/DE69519677T2/en not_active Expired - Lifetime
- 1995-10-31 WO PCT/SE1995/001289 patent/WO1996014447A1/en active IP Right Grant
- 1995-10-31 EP EP95936833A patent/EP0783595B1/en not_active Expired - Lifetime
-
1997
- 1997-08-01 US US08/904,456 patent/US5951788A/en not_active Expired - Lifetime
-
2007
- 2007-05-16 JP JP2007130976A patent/JP2007262582A/en active Pending
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0254787A1 (en) * | 1986-07-28 | 1988-02-03 | Manoir Industries | Stainless, austenitic and amagnetic steel |
SE466919B (en) * | 1990-02-26 | 1992-04-27 | Sandvik Ab | Non-magnetic, non-rusting Mn-Cr-Ni-N-steel alloy |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2058415A1 (en) * | 2007-11-09 | 2009-05-13 | General Electric Company | Forged Austenitic Stainless Steel Alloy Components and Method Therefor |
Also Published As
Publication number | Publication date |
---|---|
US5951788A (en) | 1999-09-14 |
ES2154350T3 (en) | 2001-04-01 |
JP2007262582A (en) | 2007-10-11 |
SE9403749D0 (en) | 1994-11-02 |
EP0783595B1 (en) | 2000-12-20 |
JPH10508658A (en) | 1998-08-25 |
DE69519677D1 (en) | 2001-01-25 |
EP0783595A1 (en) | 1997-07-16 |
SE9403749L (en) | 1996-06-28 |
DE69519677T2 (en) | 2001-04-26 |
SE506550C2 (en) | 1998-01-12 |
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