CN102105605B - Method for producing a steel strip, having a dual-phase microstructure - Google Patents
Method for producing a steel strip, having a dual-phase microstructure Download PDFInfo
- Publication number
- CN102105605B CN102105605B CN200980129258.9A CN200980129258A CN102105605B CN 102105605 B CN102105605 B CN 102105605B CN 200980129258 A CN200980129258 A CN 200980129258A CN 102105605 B CN102105605 B CN 102105605B
- Authority
- CN
- China
- Prior art keywords
- microstructure
- ferrite
- subsequently
- dissolved
- strip
- 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
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- 229910000831 Steel Inorganic materials 0.000 title abstract description 17
- 239000010959 steel Substances 0.000 title abstract description 17
- 238000004519 manufacturing process Methods 0.000 title abstract description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 10
- 239000011159 matrix material Substances 0.000 claims abstract description 10
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 9
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 4
- 238000000034 method Methods 0.000 claims description 21
- 229910000859 α-Fe Inorganic materials 0.000 claims description 15
- 229910045601 alloy Inorganic materials 0.000 claims description 10
- 239000000956 alloy Substances 0.000 claims description 10
- 230000009977 dual effect Effects 0.000 claims description 8
- 238000005246 galvanizing Methods 0.000 claims description 7
- 239000000470 constituent Substances 0.000 claims description 5
- 238000007669 thermal treatment Methods 0.000 claims description 5
- 238000003801 milling Methods 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 3
- 150000004767 nitrides Chemical class 0.000 claims description 3
- 230000001105 regulatory effect Effects 0.000 claims description 3
- 238000000137 annealing Methods 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 claims 2
- 229910052742 iron Inorganic materials 0.000 claims 2
- 229910052748 manganese Inorganic materials 0.000 claims 2
- 229910052698 phosphorus Inorganic materials 0.000 claims 2
- 238000005275 alloying Methods 0.000 abstract 1
- 239000011265 semifinished product Substances 0.000 abstract 1
- 238000001816 cooling Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 239000000446 fuel Substances 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
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)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention relates to a method for producing a semi-finished product, especially steel strip, having a dual-phase microstructure and a tensile strength between 500 and 1000 MPa. The invention is characterized in that in order to establish a microstructure made of hard components such as martensite, bainite, and carbide having low percentages of residual austenite in a ferritic matrix which is substantially free of interstitially dissolved elements (IF character), the elements interstitially dissolved in the ferritic matrix such as carbon and nitrogen are bound by carbide-, nitride-, or carbon nitride-forming alloying elements such as Al, Mo, Nb, Ti, and V.
Description
The present invention relates to the method for work in-process that a kind of production has dual phase microstructure and a 500-1000MPa tensile strength especially steel band (being called for short DP steel band).
All need in a lot of fields be up to the high-strength steel sheet material at about 600 DEG C with good plasticity, microstructure stability and mechanical property.
Such as, a kind of such field is automotive industry, and it is devoted to reduce discharge by the weight of reduction chassis part, because can reduce the consumption of fuel by reducing weight on the one hand.There is such hope on the other hand, make the intensity that used sheet material reaches higher.
Finally, described sheet material also should be applicable to galvanizing.
But the adjusted steel with dual phase microstructure has such shortcoming: be heated to above at the temperature of 200 DEG C, as during galvanizing or the temperature that occur relevant to galvanizing, usually produce less desirable, obvious yield strength.
Due to there is no temperature stability within this material higher than when about 200 DEG C, therefore comprise the work in-process of DP steel, as band, sheet material, tubing and other structure unit or workpiece are unsuitable for galvanizing.
Therefore, the object of the present invention is to provide a kind of for the production of work in-process, especially the method for DP steel band, the method is low cost and adopts the method can manufacture such DP steel band, this steel band not only has the plasticity character of optimization, and has the temperature stability of about 600 DEG C at the most and be therefore also applicable to galvanizing.
According to the present invention, this object is achieved by the method for producing the work in-process especially steel band with dual phase microstructure and 500-1000MPa tensile strength, the method is characterized in that, by forming carbide, the alloy element such as Al of nitride or carbonitride, Mo, Nb, Ti and V limits the element such as carbon and nitrogen that are dissolved in gap in ferrite matrix, to regulate the microstructure of hard constituents, the microstructure such as martensite of described hard constituents, bainite, the residual austenite of the low number in carbide and ferrite matrix, this ferrite matrix is not substantially containing the element (IF-feature) that gap is dissolved.
Make to stoichiometric ratio the alloy content of described alloy element and ferrite content and DP microstructure with post-heating or heat treated temperature under the solubleness of carbon and nitrogen adapt.
By this way, work in-process obtained thus or structure unit part obtain in microstructure intensity, minimum unit elongation, yield strength ratio and strain-hardening index (even if in thermal treatment subsequently or heating, especially galvanizing, and optionally subsequently after integer) characteristic property of DP steel of aspect.
For producing the hot rolled band with DP microstructure, after the last milling train unit leaving milling train, described hot rolled band is cooled in two-phase region, to regulate the residual austenite of appropriate amount, and be cooled to temperature that is initial lower than martensite or end temp with accelerated manner subsequently.
In contrast, for producing the cold-strip with DP microstructure, described cold-strip being heated to regulate the residual austenite of appropriate amount in two-phase region, and being cooled to temperature that is initial lower than martensite or end temp with accelerated manner subsequently.Preferably, described thermal treatment is carried out in continuous annealing apparatus.
Embodiment
In order to get rid of the impact of N on ag(e)ing behavio(u)r of dissolving, N content should be fixed as low as far as possible and pass through to add Al and optional Ti.The V-content of corresponding raising also may be used for nitrogen to be fixed.
table 1comprise the chemical constitution that some are possible.
| Sequence number | Scheme | C | Si | Mn | P | S | Al | Mo | Ti | Nb | V | Cr | N |
| 1 | Contrast | 0.06 | 0.35 | 1.1 | 0.02 | 0.004 | 0.025 | - | - | - | - | 0.65 | Minimum |
| 2 | Mo | 0.2 | - | ||||||||||
| 3 | MoV | 0.06 | 0.35 | 1.1 | 0.02 | 0.004 | 0.025 | 0.1 | - | - | 0.05 | 0.65 | Minimum |
| 4 | V | - | 0.1 |
table 1:chemical constitution scheme IF-DP (quality %)
Drawings show:
Fig. 1 schematically illustrates the cooling curve of the steel sheets after the hot rolling for regulating dual phase microstructure; And
Fig. 2 shows the stresses typical-strain figure of DP steel, and described DP steel has low yield strength ratio (≤75%) and do not have significant yield strength.
In FIG, depict austenitic number in left side relative to time shaft, draw core (core) temperature on right side relative to time shaft.
For regulating the steel sheet cools down curve of dual phase microstructure after schematically illustrating hot rolling.
In this process, first ferrite area is cooled, make most of austenite be transformed into ferrite within very short time.Can be the hold-time after following this first cooling stages closely, or directly be cooled to the temperature lower than martensite start temperature further.In the process, the retained austenite of any reservation changes into martensite and produces the second hard phase.Make every effort to reach the coiling temperature of about 200 DEG C.
Solid line shows austenite to be increased with cooling time and decomposes.Dotted line shows core temperature also to be reduced with cooling time.Can find out, between about 600 DEG C and the maintenance temperature of 200 DEG C, cooling is accelerated.
Claims (8)
1. produce the method with the hot rolled band of dual phase microstructure and 500-1000MPa tensile strength, it is characterized in that, by forming carbide, the alloy element of nitride or carbonitride limits the element be dissolved in gap in ferrite matrix, to regulate the microstructure of hard constituents, wherein make to stoichiometric ratio the alloy content of aforementioned alloy element and ferrite content and carbon and the solubleness of nitrogen in ferrite adapt at heat treated temperature subsequently, after the last milling train unit leaving milling train, described hot rolled band is cooled in two-phase region, to regulate the residual austenite of appropriate amount in order to reach required strength grade, and it is characterized in that, temperature that is initial lower than martensite or end temp is cooled to subsequently with accelerated manner, this hot rolled band has as follows in mass: 0.06%C, 0.35%Si, 1.1%Mn, 0.02%P, 0.004%S, 0.025%Al, 0.1%Mo, 0.05%V, 0.65%Cr, surplus is Fe and N.
2. produce the method with the cold-strip of dual phase microstructure and 500-1000MPa tensile strength, it is characterized in that, by forming carbide, the alloy element of nitride or carbonitride limits the element be dissolved in gap in ferrite matrix, to regulate the microstructure of hard constituents, wherein make to stoichiometric ratio the alloy content of aforementioned alloy element and ferrite content and carbon and the solubleness of nitrogen in ferrite adapt at heat treated temperature subsequently, wherein described cold-strip is heated in two-phase region to adjust the residual austenite of appropriate amount, and be cooled to temperature that is initial lower than martensite or end temp with accelerated manner subsequently, this cold-strip has as follows in mass: 0.06%C, 0.35%Si, 1.1%Mn, 0.02%P, 0.004%S, 0.025%Al, 0.1%Mo, 0.05%V, 0.65%Cr, surplus is Fe and N.
3. according to the method for claim 1 or 2, it is characterized in that, the element be dissolved in ferrite matrix is selected from carbon and nitrogen.
4. according to the method for claim 1 or 2, it is characterized in that, described alloy element is selected from Al, Mo, Nb, Ti and V.
5. according to the method for claim 1 or 2, it is characterized in that, the microstructure of described hard constituents is selected from the residual austenite of the low number in martensite, bainite, carbide and ferrite matrix, and this ferrite matrix is not substantially containing the element that gap is dissolved.
6. according to the method for claim 1 or 2, it is characterized in that, thermal treatment is subsequently galvanizing or heating.
7. method according to claim 2, is characterized in that, carries out the thermal treatment for regulating the DP microstructure in cold-strip in continous way annealing device.
8., according to the method for aforementioned any one of claim 1,2 or 7, it is characterized in that, described thermal treatment is at 400 DEG C and A
3between carry out.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102008038865A DE102008038865A1 (en) | 2008-08-08 | 2008-08-08 | Process for the production of semi-finished products, in particular steel strip, with dual-phase structure |
| DE102008038865.3 | 2008-08-08 | ||
| PCT/DE2009/001136 WO2010015251A2 (en) | 2008-08-08 | 2009-08-07 | Method for producing a semi-finished product, especially steel strip, having a dual-phase microstructure |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102105605A CN102105605A (en) | 2011-06-22 |
| CN102105605B true CN102105605B (en) | 2015-04-15 |
Family
ID=41353805
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200980129258.9A Expired - Fee Related CN102105605B (en) | 2008-08-08 | 2009-08-07 | Method for producing a steel strip, having a dual-phase microstructure |
Country Status (10)
| Country | Link |
|---|---|
| US (1) | US20110146850A1 (en) |
| EP (1) | EP2318556A2 (en) |
| JP (1) | JP2011530649A (en) |
| KR (1) | KR20110036928A (en) |
| CN (1) | CN102105605B (en) |
| BR (1) | BRPI0917007A2 (en) |
| CA (1) | CA2732495C (en) |
| DE (1) | DE102008038865A1 (en) |
| RU (1) | RU2475545C2 (en) |
| WO (1) | WO2010015251A2 (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1172505A (en) * | 1994-12-06 | 1998-02-04 | 埃克森研究工程公司 | Dual-phase high strength steel sheet with good toughness and weldability |
| EP1391526A2 (en) * | 2002-08-20 | 2004-02-25 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Dual phase steel sheet with good bake-hardening properties |
| CN1782116A (en) * | 2004-11-29 | 2006-06-07 | 宝山钢铁股份有限公司 | 800MPa cold rolled and hot zinc plated double phase steel and its producing method |
| CN101165201A (en) * | 2006-10-18 | 2008-04-23 | 株式会社神户制钢所 | High-strength steel plate and method for manufacturing the same |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5839736A (en) * | 1981-09-01 | 1983-03-08 | Kobe Steel Ltd | Manufacture of composite structure type high tensile cold rolled steel plate |
| DE19936151A1 (en) * | 1999-07-31 | 2001-02-08 | Thyssenkrupp Stahl Ag | High-strength steel strip or sheet and process for its manufacture |
| JP4010131B2 (en) * | 2000-11-28 | 2007-11-21 | Ｊｆｅスチール株式会社 | Composite structure type high-tensile cold-rolled steel sheet excellent in deep drawability and manufacturing method thereof |
| JP4062118B2 (en) * | 2002-03-22 | 2008-03-19 | Ｊｆｅスチール株式会社 | High-tensile hot-rolled steel sheet with excellent stretch characteristics and stretch flange characteristics and manufacturing method thereof |
| US6811624B2 (en) * | 2002-11-26 | 2004-11-02 | United States Steel Corporation | Method for production of dual phase sheet steel |
| JP4214006B2 (en) * | 2003-06-19 | 2009-01-28 | 新日本製鐵株式会社 | High strength steel sheet with excellent formability and method for producing the same |
| US20080178972A1 (en) * | 2006-10-18 | 2008-07-31 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) | High strength steel sheet and method for producing the same |
| CN101802230B (en) * | 2007-07-19 | 2012-10-17 | 塔塔钢铁艾默伊登有限责任公司 | A strip of steel having a variable thickness in length direction |
-
2008
- 2008-08-08 DE DE102008038865A patent/DE102008038865A1/en not_active Withdrawn
-
2009
- 2009-08-07 EP EP09736097A patent/EP2318556A2/en not_active Ceased
- 2009-08-07 RU RU2011108570/02A patent/RU2475545C2/en active
- 2009-08-07 WO PCT/DE2009/001136 patent/WO2010015251A2/en active Application Filing
- 2009-08-07 US US13/058,085 patent/US20110146850A1/en not_active Abandoned
- 2009-08-07 CN CN200980129258.9A patent/CN102105605B/en not_active Expired - Fee Related
- 2009-08-07 BR BRPI0917007A patent/BRPI0917007A2/en not_active Application Discontinuation
- 2009-08-07 CA CA2732495A patent/CA2732495C/en not_active Expired - Fee Related
- 2009-08-07 KR KR1020117002936A patent/KR20110036928A/en active Search and Examination
- 2009-08-07 JP JP2011521437A patent/JP2011530649A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1172505A (en) * | 1994-12-06 | 1998-02-04 | 埃克森研究工程公司 | Dual-phase high strength steel sheet with good toughness and weldability |
| EP1391526A2 (en) * | 2002-08-20 | 2004-02-25 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Dual phase steel sheet with good bake-hardening properties |
| CN1782116A (en) * | 2004-11-29 | 2006-06-07 | 宝山钢铁股份有限公司 | 800MPa cold rolled and hot zinc plated double phase steel and its producing method |
| CN101165201A (en) * | 2006-10-18 | 2008-04-23 | 株式会社神户制钢所 | High-strength steel plate and method for manufacturing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| CA2732495A1 (en) | 2010-02-11 |
| CA2732495C (en) | 2015-01-20 |
| DE102008038865A1 (en) | 2010-02-11 |
| BRPI0917007A2 (en) | 2016-02-16 |
| WO2010015251A2 (en) | 2010-02-11 |
| RU2475545C2 (en) | 2013-02-20 |
| US20110146850A1 (en) | 2011-06-23 |
| WO2010015251A3 (en) | 2010-07-01 |
| KR20110036928A (en) | 2011-04-12 |
| RU2011108570A (en) | 2012-09-20 |
| JP2011530649A (en) | 2011-12-22 |
| EP2318556A2 (en) | 2011-05-11 |
| CN102105605A (en) | 2011-06-22 |
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