CN100357478C - Method for manufacturing a steel strip or sheet consisting mainly of MN-austenite - Google Patents
Method for manufacturing a steel strip or sheet consisting mainly of MN-austenite Download PDFInfo
- Publication number
- CN100357478C CN100357478C CNB018159508A CN01815950A CN100357478C CN 100357478 C CN100357478 C CN 100357478C CN B018159508 A CNB018159508 A CN B018159508A CN 01815950 A CN01815950 A CN 01815950A CN 100357478 C CN100357478 C CN 100357478C
- Authority
- CN
- China
- Prior art keywords
- steel
- maximum
- thin strip
- casting
- band
- 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 - Fee Related
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
-
- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- 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
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)
- Crystallography & Structural Chemistry (AREA)
- Continuous Casting (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
The method according to the invention can be used for the economic manufacture of a steel strip (W) or sheet consisting mainly of Mn-austenite which possesses enhanced strength compared with the prior art. For this purpose a steel is melted which contains at least the following alloying components (in wt. %), 15.00-24.00% Cr, 5.00-12.00% Mn, 0.10-0.60% N, 0.01-0.2% C, max. 3.00% Al and/or Si, max. 0.07% P, max. 0.05% S, max. 0.5% Nb, max. 0.5% V, max. 3.0% Ni, max. 5.0% Mo, max. 2.0% Cu as well as iron and unavoidable impurities as the remainder. This steel is cast into a thin strip (D) having a maximum thickness of 10 mm in a casting gap formed between two rotating rollers (2, 3) or rolls. The rollers (2, 3) or rolls are cooled so intensively that the thin strip (D) in the casting gap (4) is cooled at a cooling rate of at least 200 K/s.
Description
The present invention relates to main steel band or the steel-sheet preparation method who constitutes by the Mn austenite.The steel that is suitable for preparing these products is designated as AISI200, and comprises label S20100-S24000.This steel are well-known still to keep high strength after the welding even in the commissure.
These good strength propertys obtain by crystalline gap and displacement mixed hardening.Carbon and nitrogen are effective especially in this respect.Yet, should avoid carbon content higher, because this can form undesirable carbide.So, in this steel of being addressed, preferably adopt nitrogen to carry out gap mixed crystal sclerosis.But, when producing the high steel of nitrogen content, alloy constituent element wherein or to produce desired device very expensive.
In a kind of currently known methods of producing the high steel of nitrogen content, melting melt under the load of exerting pressure.At this moment, act on pressure on the melt nitrogen partial pressure when being dissolved in the suitable steel far above nitrogen.The advantage of this method is that other alloying element that does not need to add specified quantitative just can be produced the high steel of nitrogen content.Yet its weak point is the installation cost height that this method requires.
Between smelting period, come the another kind of method of dissolved nitrogen to relate to the solubleness that improves melt itself by the load of exerting pressure.This point can realize by high-load chromium and manganese.M.du Toit has edited the performance introduction of the steel with corresponding composition, its content at present on the internet www.tecnet.co.za/mags/steel/featurel.htm find at the place.This known steel can adopt traditional method rather than continuous cast method melting and cast under the condition of the load of not exerting pressure.Therefore, the cast cost height of this known steel.
By with aluminium and/or alloying with silicon, but can further improve the intensity of aforementioned conventional cast steel.These two kinds of elements promote described mixed crystal sclerosis, therefore, cause intensity further to improve.In addition, the interpolation of aluminium and silicon can influence stacking fault energy, and then again deformation process is exerted an influence.
As a result, the interpolation of aluminium causes stacking fault energy to improve, and helps by twinning deformation.Yet silicon reduces stacking fault energy, but helps by forming the martensite distortion.Because the common interpolation of silicon and aluminium, the reinforcement of material especially can be influenced between deformation phases.Martensitic formation causes high strength, the twin strengthening effect that then reduces.
The advantage of adding aluminium and silicon in described steel is ferrite formers by these two kinds of elements, and ferrite of they promotions is separated out this weak point and offset.The ferrite that is obtained can only dissolve a spot of nitrogen.
As a result, nitrogen is removed with bubble form at solidificating period.Yet, in order to obtain high strength austenite steel, and keeping high nitrogen content simultaneously, austenite must be stablized.For this reason, require further to improve manganese content, this produces more problem in the time of also can making this high mangaenese steel in steel mill except increasing material cost.
Therefore, problem of the present invention provides mainly the preparation method of the steel that is made of the Mn austenite, and this steel can prepare economically, and compares with existing steel simultaneously and have higher intensity.
A kind of steel band or steel-sheet method of mainly being made of the Mn austenite of preparing solved this problem.In this method, the steel that contains following alloy constituent element (in wt.%) is carried out melting:
15.00-24.00 ％Cr，
5.00-12.00 ％Mn，
0.10-0.60 ％N，
0.01-0.2 ％C，
Maximum 3.00 %Al and/or Si,
Maximum 0.07 %P,
Maximum 0.05 %S,
Maximum 0.5 %Nb,
Maximum 0.5 %V,
Maximum 3.0 %Ni,
Maximum 5.0 %Mo,
Maximum 2.0 %Cu,
The rest is iron and unavoidable impurities,
And the casting roll gap by forming between two rotation rollers or roll pours into the thin strip that maximum ga(u)ge is 10mm with steel, and then, described roller or roll are strengthened cooling, make the speed of cooling of the thin strip in the casting roll gap be at least 200K/s.The preferred 1-5mm of the thickness of thin strip.Naturally comprise also that content is this class alloying element of 0, has only provided the highest high limit of tolerance of they content in the composition in the detailed composition of the steel that the present invention uses.
According to further refinement scheme of the present invention, the chromium content in the steel can be restricted to 17.00-21.00wt.%Cr, manganese content is restricted to 8.00-12.00wt.%Mn and/or nitrogen content is restricted to 0.40-0.60wt.%N.In addition, can there be Ni in the steel, Mo and/or Cu.
In all cases, according to the effect of these elements, be optimized being used for steel composition interalloy constituent content of the present invention.As a result, Cr, Mn, Mo, V, Nb and Al improve the solubleness of nitrogen in melt, and austenite former Ni and Cu, and Si reduces the solubleness of nitrogen.As previously mentioned, Si also plays the mixed crystal stiffening agent.In addition, this element also is used for grain refining and reduces stacking fault energy.On the other hand, aluminium improves stacking fault energy.Molybdenum also plays the mixed crystal sclerization and improves erosion resistance.Vanadium also has the grain refining effect and improves intensity.The interpolation of Nb improves intensity by precipitation-hardening.
The present invention utilizes the basic known technology of Strip casting equipment, by the casting roll gap that between two rollers of for example twin roller casting device or roll, forms steel is cast, and, strengthen cooling, convert an austenite to and solidify so that solidify by ferrite.Because the nitrogen solubility height in the austenite so just can make the nitrogen that is dissolved in the melt enter in the steel.Only when the casting roll gap wall that forms by casting roll or roll to move with the essentially identical speed of cast strip, when continuous intensive heat exchange takes place the result, can realize that this reinforcement cools off by thin cast strip in the casting roll gap between casting can be guaranteed described roll gap wall (casting roll/roll) and casting steel in the roll gap.
The reinforcement cooling of carrying out with high speed of cooling can guarantee that the nitrogen bubble that may form keeps small size when melt solidifying, and the pressure that acts on the bubble is higher.This can prevent to remove at solidificating period generation nitrogen.In addition, high ferrostatic pressure also can suppress this nitrogen and removes.High ferrostatic pressure reason occurring is at the height height of casting molten bath, roll gap place.Like this, can guarantee pressure P in any nitrogen bubble that forms
NAlways be lower than barometric point P
A, ferrostatic pressure P
FAnd 2 times of the ratio of bubble surface tension force ζ and bubble radius r and (that is: P
N＜P
A+ P
F+ 2 ζ/r).
As a result, the rapid solidification of cast strip provides very big degree of freedom especially for the selection of the composition of steel used according to the invention during Strip casting.As previously mentioned, because rapid solidification can dissolve a large amount of nitrogen.As a result, compare, can add the more substantial alloying element that can improve material property, and need not consider the disadvantageous effect that these elements may bring nitrogen solubility with classical production process.For example,, adopt the method according to this invention, then can eliminate the danger that removes owing to the nitrogen that slowly solidifies and the increase of ferrite formation amount accordingly exists in traditional manufacturing processed if contain more Si in the steel.And when Al content is higher, adopt quick cooling provided by the invention, then can avoid occurring the AlN that slow cooling period forms.As a result, needn't consider the harmful effect that slowly cooling brings, the present invention can carry out specific adjusted to the deformation mechanism of employed every kind of alloy by suitably selecting Al and Si content, like this, can obtain to have the finished product of optimum performance.
When handling the steel that is difficult to be out of shape of the present invention's use itself, the present invention can obtain quite significantly cost advantage.This both had been applicable to the maximum 7.5wt.% of Mn content, can adopt the steel of traditional continuous cast method casting, be applicable to that also Mn content is higher than the steel of 7.5wt.%, this steel can only adopt traditional method, be cast as ingot casting earlier, then, if necessary, adopt several passages that reheat that have to be rolled into desired final thickness.
At present, but can only be processed into the minimum thickness of 3.5mm at traditional hot rolling wide strip equipment by the hot rolled band that the continuous casting alloy is made.Have only employing process annealing, can prepare the cold-strip that target thickness is 0.8-1.2mm.But, in relating to the method according to this invention of Strip casting, no longer need process annealing, because the thinner thickness of the hot rolled band that is obtained.Because it is the thin strip of 1-3mm that Strip casting method provided by the invention can provide final thickness, therefore, under many situations, can adjust the final thickness of prepared band, like this, can save cold rolling step fully.In this case, can avoid the problem in the traditional preparation process method, brought because of Mn austenite deformation poor performance.
The method according to this invention can be used for preparing the high nitrogen-containing that particularly contains 0.4-0.6wt.%, and adopt maximum 3% the aluminium and/or the steel band or the steel sheet of alloying with silicon, and the production of steel need not to carry out or require extra high manganese content under excess pressure.Prepared product made from steel has the close grain isotropy tissue that has slight macrosegregation or small number of coarse inclusion.Because wherein Al that exists and/or the effect of Si, described product is compared intensity and the ductility with raising with currently available products.For steel band prepared in accordance with the present invention or steel sheet, can specifically adjust energy absorption between strengthening effect and deformation phases by selecting alloy.
The casting of described thin strip is preferably carried out in protective atmosphere.By in protective atmosphere, casting, can carry out specific adjusted to the degree of oxidation on surface, thereby preparation has the thin strip of modified surface easily.Like this, can avoid forming firecoat.
Then, on roll mill stand, there is not dangerous " online " hot rolling of roll bonding in the band that is obtained.Thin strip is heated to initial rolling temperature, this point particularly advantageous as before the hot rolling.Because temperature raises, and can obtain higher degree of deformation during the hot rolling.
By after hot rolling, hot rolled band being heat-treated, can specifically optimize its tissue.Thermal treatment can comprise annealing and controlled chilling subsequently.
The basis energy range, steel sheet prepared in accordance with the present invention is particularly suitable for making body of a motor car with metal steel unit, especially in the general-purpose vehicle manufacturing, especially the rigid structure members of using in the automobile making, landing gear or vehicle chassis component, wheel and fuel container.In all these were used, the outstanding especially strength property of steel sheet prepared according to the methods of the invention was very favourable.In addition, in the occasion that contacts with corrosive medium such as fuel, very favourable according to the good corrosion resistance of steel sheet of the present invention and steel band.
Next, the accompanying drawing with reference to an example showing embodiment is explained in more detail the present invention.
What accompanying drawing was showed is the synoptic diagram of Strip casting equipment 1.
For example, in this equipment, steel is handled, except common unavoidable impurities, also contained (in wt.%) 0.08%C in the described steel, 0.5%Si, 10%Mn, 19%Cr, 0.5%N, 0.3%Al the rest is iron.
Adopt unshowned refrigerating unit pair roller 2,3 during casting to strengthen cooling, mainly be frozen into austenite under the cooling rate of 200K/s being higher than so that enter the melt of casting roll gap 4, and, casting roll gap 4 left as the thick thin strip D of 1-5mm.Then, prepared thin strip D by stove 5, in stove, is heated to initial rolling temperature.
The twin roller casting device and the stove 5 that have roller 2,3 all are placed in the outer cover 6 that is full of protective gas.By thin cast strip D in protective atmosphere and in stove 5, reheat, can avoid greatly on the surface of thin strip D, forming firecoat.
The thin strip D that is heated to initial rolling temperature enters milling train 7, is hot-rolled down to final size.Because therefore initial rolling temperature height, can carry out high deformation.By having high-quality especially surface after the rolling hot rolled band W hot rolling that forms of the thin strip D that does not have firecoat substantially that enters milling train.
In milling train 7, after the hot rolling, in continuous annealing furnace 8, hot rolled band W is annealed, then, carry out controlled chilling, so that its tissue is carried out specific improvement by refrigerating unit 9.Afterwards, heat-treatment hot rolled band W is coiled into coiled material 10.
Tradition is formed and the steel band of employing traditional method preparation is compared with having, adopt the steel band of preceding method preparation to have extra high intensity, also have good deformability and same excellent energy receptivity simultaneously, this is because by the roller 2 at the twin roller casting device, cool off fast between 3, can obtain high nitrogen content.
Following table has compared according to the present invention the intensity level of the Mn austenitic steel of the traditional method preparation of the outstanding intensity level of the hot rolled band W of preparation and employing continuous casting in casting roll equipment 1.
| R p0.2 [MPa] | Rm [MPa] | A80 [％] | |
| The present invention | 550-650 | 850-900 | 35-45 |
| Traditional method | 420 | 750-800 | 50 |
Symbol
1 casting roll equipment
2,3 rollers
4 casting roll gaps
5 stoves
6 outer covers
7 milling trains
8 continuous annealing furnaces
9 refrigerating units
10 reeling machines
The D thin strip
The W hot rolled band
The S molten bath
Claims (16)
1. the steel band (W) that mainly constitutes by the Mn austenite or the preparation method of thin plate,
-wherein, the steel that contains following alloy constituent element (in wt.%) is carried out melting:
15.00-24.00％Cr，
5.00-12.00％Mn，
0.10-0.60％N，
0.01-0.2％C，
Maximum 0.07%P,
Maximum 0.05%S,
Maximum 0.5%Nb,
Maximum 0.5%V,
Maximum 3.0%Ni,
Maximum 5.0%Mo,
Maximum 2.0%Cu,
0.30-3.0%Al and/or 0.50-3.00%Si, and the total amount of Al and Si is no more than 3.00%,
The rest is iron and unavoidable impurities,
And,
-by rotating the casting roll gap that forms between rollers (2,3) or the roll, steel is poured into the thin strip that maximum ga(u)ge is 10mm (D) at two, and then, described roller (2,3) or roll are strengthened cooling, make the speed of cooling of the thin strip (D) in the casting roll gap (4) be at least 200K/s.
2. according to the method for claim 1, it is characterized in that: the thickness of thin strip (D) is 1-5mm.
3. according to the method for claim 1, it is characterized in that: contain 17.00-21.00wt.%Cr in the steel.
4. according to the method one of among the claim 1-3, it is characterized in that: contain 8.00-12.00wt.%Mn in the steel.
5. according to the method one of among the claim 1-3, it is characterized in that: contain 0.40-0.60wt.%N in the steel.
6. according to the method one of among the claim 1-3, it is characterized in that: additional Ni, Mo and/or the Cu of containing in the steel.
7. according to the method one of among the claim 1-3, it is characterized in that: being cast in the protective atmosphere of thin strip (D) carried out.
8. according to the method one of among the claim 1-3, it is characterized in that: after the casting, (D) carries out continuously hot rolling to thin strip, obtains hot rolled band (W).
9. method according to Claim 8 is characterized in that: before the hot rolling, thin strip (D) is heated to the initial value temperature of rolling.
10. according to the method for claim 9, it is characterized in that: heating is carried out in protective atmosphere.
11. method according to Claim 8 is characterized in that: after the hot rolling, (W) heat-treats to hot rolled band.
12. according to the steel band of one of among the claim 1-11 method preparation as the body of a motor car metal steel unit with the application on the material.
13. according to the steel band of one of among the claim 1-11 method preparation as rigid structure members with the application on the material.
14. according to the steel band of one of among the claim 1-11 method preparation as landing gear or chassis with the application on the material.
15. according to the steel band of one of among the claim 1-11 method preparation as wheel with the application on the material.
16. according to the steel band of one of among the claim 1-11 method preparation at the case that acts as a fuel with the application on the material.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE10046181.6 | 2000-09-19 | ||
| DE10046181A DE10046181C2 (en) | 2000-09-19 | 2000-09-19 | Process for producing a steel strip or sheet consisting predominantly of Mn austenite |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1659300A CN1659300A (en) | 2005-08-24 |
| CN100357478C true CN100357478C (en) | 2007-12-26 |
Family
ID=7656678
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB018159508A Expired - Fee Related CN100357478C (en) | 2000-09-19 | 2001-09-14 | Method for manufacturing a steel strip or sheet consisting mainly of MN-austenite |
Country Status (12)
| Country | Link |
|---|---|
| US (1) | US20040025979A1 (en) |
| EP (1) | EP1319091B1 (en) |
| JP (1) | JP2004509762A (en) |
| KR (1) | KR100748256B1 (en) |
| CN (1) | CN100357478C (en) |
| AT (1) | ATE350504T1 (en) |
| AU (1) | AU2002210506A1 (en) |
| BR (1) | BR0113950A (en) |
| DE (2) | DE10046181C2 (en) |
| ES (1) | ES2279831T3 (en) |
| TW (1) | TW522060B (en) |
| WO (1) | WO2002024969A1 (en) |
Families Citing this family (20)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7485196B2 (en) * | 2001-09-14 | 2009-02-03 | Nucor Corporation | Steel product with a high austenite grain coarsening temperature |
| AT501044B8 (en) | 2004-10-29 | 2007-02-15 | Voest Alpine Ind Anlagen | METHOD FOR PRODUCING A CAST STEEL STRIP |
| AT504782B1 (en) * | 2005-11-09 | 2008-08-15 | Siemens Vai Metals Tech Gmbh | METHOD FOR PRODUCING A HOT-ROLLED STEEL STRIP AND COMBINED CASTING AND ROLLING MACHINE TO PERFORM THE METHOD |
| EP2163659B1 (en) | 2008-09-11 | 2016-06-08 | Outokumpu Nirosta GmbH | Stainless steel, cold strip made of same and method for producing cold strip from same |
| US8182963B2 (en) * | 2009-07-10 | 2012-05-22 | GM Global Technology Operations LLC | Low-cost manganese-stabilized austenitic stainless steel alloys, bipolar plates comprising the alloys, and fuel cell systems comprising the bipolar plates |
| TWI392749B (en) * | 2009-12-17 | 2013-04-11 | Ind Tech Res Inst | Easy rolling alloy material |
| CN101812646B (en) * | 2010-04-22 | 2011-09-07 | 河北工业大学 | High-speed steel alloy casting process used for roll |
| CN103614659A (en) * | 2013-10-22 | 2014-03-05 | 芜湖市鸿坤汽车零部件有限公司 | An austenite alloy steel material used for an internal combustion engine and a preparation method of the alloy steel material |
| KR101622705B1 (en) * | 2014-08-06 | 2016-05-23 | 한국기계연구원 | Austenite stainless steel having excellent pitting corrosion resistance |
| US9975170B2 (en) * | 2014-12-11 | 2018-05-22 | Posco | Method for manufacturing duplex stainless steel sheet having high nitrogen content and good surface quality |
| DE102015005742A1 (en) | 2015-05-05 | 2016-11-10 | Dbi Gas- Und Umwelttechnik Gmbh | Process for the production of sheet from a stainless, austenitic CrMnNi steel |
| DE102016211411A1 (en) * | 2016-06-24 | 2017-12-28 | Thyssenkrupp Ag | Vehicle wheel and use |
| US10960487B2 (en) * | 2017-09-21 | 2021-03-30 | United States Steel Corporation | Weldability improvements in advanced high strength steel |
| CN108179364B (en) * | 2017-12-28 | 2019-05-31 | 钢铁研究总院 | A kind of structural alloy steel and preparation method thereof with high impact absorption energy |
| CN109865806A (en) * | 2018-06-08 | 2019-06-11 | 江苏沙钢集团有限公司 | A kind of thin strap continuous casting 345MPa grades of weathering steels and its production method |
| CN110484833A (en) * | 2019-08-21 | 2019-11-22 | 首钢集团有限公司 | Low Mn austenitic steel of a kind of high chromium and preparation method thereof |
| CN111876670B (en) * | 2020-06-30 | 2021-11-09 | 九牧厨卫股份有限公司 | High-hardness scratch-resistant stainless steel, stainless steel water tank and preparation method thereof |
| CN112974532B (en) * | 2021-02-05 | 2023-01-31 | 山西太钢不锈钢股份有限公司 | Rolling method of ultrahigh nitrogen austenitic stainless steel hot continuous rolling coiled plate |
| CN115368760A (en) * | 2022-07-20 | 2022-11-22 | 江苏甬金金属科技有限公司 | Processing technology of antibacterial austenitic stainless steel strip |
| EP4316727A1 (en) | 2022-08-05 | 2024-02-07 | Outokumpu Oyj | Filler metal for welding of dissimilar welds |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4946644A (en) * | 1989-03-03 | 1990-08-07 | Baltimore Specialty Steels Corporation | Austenitic stainless steel with improved castability |
| JPH0790471A (en) * | 1993-09-17 | 1995-04-04 | Nippon Steel Corp | High mn and high n austenitic stainless steel cast slab and its production |
| CN1129259A (en) * | 1995-07-12 | 1996-08-21 | 南京三钢(集团)股份有限公司 | Nickel-chromium-saved nitrogen-contained austenite stainless steel |
| CN1212189A (en) * | 1997-05-29 | 1999-03-31 | 于西纳公司 | Process for manufacturing thin strip of ferritic stainless steel, and thin strip thus obtained |
| EP0969113A1 (en) * | 1998-07-02 | 2000-01-05 | Ugine S.A. | Stainless austenitic steel with low nickel content |
| DE19900199A1 (en) * | 1999-01-06 | 2000-07-13 | Ralf Uebachs | High strength light constructional steel for pre-stressed concrete reinforcements or automobile body components has high manganese and aluminum contents |
| CN1260740A (en) * | 1997-06-19 | 2000-07-19 | 阿奇亚斯佩丝阿里特尔尼公司 | Continuous casting process for producing low carbon steel strips and strips obtained with good as cast mechanical properties |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE2163511C3 (en) * | 1971-12-21 | 1980-09-25 | Armco Steel Corp., Middletown, Ohio (V.St.A.) | Use of an austenitic ferritic stainless steel as a material for the production of cold-upset fasteners, weldments in pure chrome steels and for other applications in which magnetic steels with high ductility, good weldability and good resistance to stress cracking in chloride media are required |
| US5092393A (en) * | 1989-03-14 | 1992-03-03 | Nippon Steel Corporation | Process for producing cold-rolled strips and sheets of austenitic stainless steel |
| JP2863541B2 (en) * | 1989-03-29 | 1999-03-03 | 新日本製鐵株式会社 | Method for producing Cr-based stainless steel sheet using thin casting method |
| JPH0698460B2 (en) * | 1990-10-11 | 1994-12-07 | 日本冶金工業株式会社 | Casting method of iron-based alloy containing Cr and Ni by twin roll type continuous casting machine |
| JPH06322440A (en) * | 1993-05-12 | 1994-11-22 | Nippon Steel Corp | Method for rolling high manganese nonmagnetic steel slab |
| JP3190319B2 (en) * | 1994-04-04 | 2001-07-23 | 新日本製鐵株式会社 | Twin roll continuous casting machine |
| JPH09168844A (en) * | 1995-12-19 | 1997-06-30 | Mitsubishi Heavy Ind Ltd | Twin roll continuous casting method |
| JP4207137B2 (en) * | 1998-02-16 | 2009-01-14 | 日立金属株式会社 | High hardness and high corrosion resistance stainless steel |
| FR2783443B1 (en) * | 1998-09-21 | 2000-10-27 | Usinor | PROCESS FOR THE MANUFACTURE OF A STAINLESS STEEL THIN STRIP |
| JP2000107803A (en) * | 1998-10-07 | 2000-04-18 | Mitsubishi Heavy Ind Ltd | Manufacture of steel sheet |
| FR2796083B1 (en) * | 1999-07-07 | 2001-08-31 | Usinor | PROCESS FOR MANUFACTURING IRON-CARBON-MANGANESE ALLOY STRIPS, AND STRIPS THUS PRODUCED |
-
2000
- 2000-09-19 DE DE10046181A patent/DE10046181C2/en not_active Expired - Fee Related
-
2001
- 2001-09-14 DE DE50111818T patent/DE50111818D1/en not_active Expired - Lifetime
- 2001-09-14 EP EP01978372A patent/EP1319091B1/en not_active Expired - Lifetime
- 2001-09-14 ES ES01978372T patent/ES2279831T3/en not_active Expired - Lifetime
- 2001-09-14 WO PCT/EP2001/010645 patent/WO2002024969A1/en active IP Right Grant
- 2001-09-14 KR KR1020037003946A patent/KR100748256B1/en active IP Right Grant
- 2001-09-14 JP JP2002529559A patent/JP2004509762A/en active Pending
- 2001-09-14 AU AU2002210506A patent/AU2002210506A1/en not_active Abandoned
- 2001-09-14 CN CNB018159508A patent/CN100357478C/en not_active Expired - Fee Related
- 2001-09-14 AT AT01978372T patent/ATE350504T1/en not_active IP Right Cessation
- 2001-09-14 US US10/380,792 patent/US20040025979A1/en not_active Abandoned
- 2001-09-14 BR BR0113950-9A patent/BR0113950A/en active Search and Examination
- 2001-09-19 TW TW090123064A patent/TW522060B/en not_active IP Right Cessation
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4946644A (en) * | 1989-03-03 | 1990-08-07 | Baltimore Specialty Steels Corporation | Austenitic stainless steel with improved castability |
| JPH0790471A (en) * | 1993-09-17 | 1995-04-04 | Nippon Steel Corp | High mn and high n austenitic stainless steel cast slab and its production |
| CN1129259A (en) * | 1995-07-12 | 1996-08-21 | 南京三钢(集团)股份有限公司 | Nickel-chromium-saved nitrogen-contained austenite stainless steel |
| CN1212189A (en) * | 1997-05-29 | 1999-03-31 | 于西纳公司 | Process for manufacturing thin strip of ferritic stainless steel, and thin strip thus obtained |
| CN1260740A (en) * | 1997-06-19 | 2000-07-19 | 阿奇亚斯佩丝阿里特尔尼公司 | Continuous casting process for producing low carbon steel strips and strips obtained with good as cast mechanical properties |
| EP0969113A1 (en) * | 1998-07-02 | 2000-01-05 | Ugine S.A. | Stainless austenitic steel with low nickel content |
| DE19900199A1 (en) * | 1999-01-06 | 2000-07-13 | Ralf Uebachs | High strength light constructional steel for pre-stressed concrete reinforcements or automobile body components has high manganese and aluminum contents |
Non-Patent Citations (1)
| Title |
|---|
| Coulé e continue de bandes d'acier J.P. BIRAT.TECHNIQUES DE L'INGé RIAUX Mé TALLIQUES,No.7816. 2000 * |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2002024969A1 (en) | 2002-03-28 |
| ATE350504T1 (en) | 2007-01-15 |
| TW522060B (en) | 2003-03-01 |
| KR100748256B1 (en) | 2007-08-10 |
| BR0113950A (en) | 2003-07-22 |
| CN1659300A (en) | 2005-08-24 |
| AU2002210506A1 (en) | 2002-04-02 |
| ES2279831T3 (en) | 2007-09-01 |
| DE10046181A1 (en) | 2002-04-04 |
| DE10046181C2 (en) | 2002-08-01 |
| EP1319091A1 (en) | 2003-06-18 |
| EP1319091B1 (en) | 2007-01-03 |
| DE50111818D1 (en) | 2007-02-15 |
| JP2004509762A (en) | 2004-04-02 |
| US20040025979A1 (en) | 2004-02-12 |
| KR20030051660A (en) | 2003-06-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100357478C (en) | Method for manufacturing a steel strip or sheet consisting mainly of MN-austenite | |
| US6328826B1 (en) | Method of fabricating “TRIP” steel in the form of thin strip, and thin strip obtained in this way | |
| US20090010793A1 (en) | Method For Producing High Strength Steel Strips or Sheets With Twip Properties, Method For Producing a Component and High-Strength Steel Strip or Sheet | |
| CN102002628B (en) | Method for manufacturing low-carbon steel sheets | |
| CN101845599B (en) | Weathering steel and manufacturing method thereof | |
| CN103328120A (en) | Method for producing a hot-rolled flat steel product | |
| US5762725A (en) | Steel for the manufacture of forging having a bainitic structure and process for manufacturing a forging | |
| WO1995007780A1 (en) | Method of manufacturing thin cast piece through continuous casting | |
| CN111545720A (en) | Forming process for reducing carburized gear steel band-shaped structure | |
| KR20060130745A (en) | High copper low alloy steel sheet | |
| CN1064566C (en) | Centrifugal casting method for producing composite high-speed steel rollers | |
| KR20070085757A (en) | High-strength steel strip or sheet exhibiting twip properties and method for producing said strip by direct strip casting | |
| EP4033000A1 (en) | Martensitic steel strip and manufacturing method therefor | |
| CA2267564C (en) | Method of manufacturing microalloyed structural steel | |
| CN110592475A (en) | Large-size high-carbon silicon-manganese steel and manufacturing method thereof | |
| JP3975600B2 (en) | Outer layer material for rolling roll made by centrifugal casting, rolling roll and manufacturing method thereof | |
| US20070175608A1 (en) | Thin cast steel strip with reduced microcracking | |
| US5405460A (en) | Fe-Cr-Al alloy steel sheet and process for producing the same | |
| JPH04350113A (en) | Production of case hardening steel free from coarsening of crystalline grain at the time of carburizing heat treatment | |
| KR100489018B1 (en) | Method of Manufacturing High Manganese Steel Strip With Twin Roll Strip Casting Apparatus | |
| CN115233081B (en) | Method for producing 30CrMo hot rolled thin strip steel based on double-roller casting and rolling | |
| NL2030436B1 (en) | High-aluminum ferrite heat-resistant steel and preparation method thereof | |
| JPS59129719A (en) | Production of high chromium roll | |
| JPH04259349A (en) | Manufacture of hot forged non-heat treated steel free from coarsening of structure at the time of hot forging | |
| CN117327984A (en) | Low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20071226 Termination date: 20091014 |