CN102965568A - Phase-change toughened low-alloy steel plate and preparation method thereof - Google Patents
Phase-change toughened low-alloy steel plate and preparation method thereof Download PDFInfo
- Publication number
- CN102965568A CN102965568A CN2012105184426A CN201210518442A CN102965568A CN 102965568 A CN102965568 A CN 102965568A CN 2012105184426 A CN2012105184426 A CN 2012105184426A CN 201210518442 A CN201210518442 A CN 201210518442A CN 102965568 A CN102965568 A CN 102965568A
- Authority
- CN
- China
- Prior art keywords
- steel
- steel plate
- temperature
- phase
- low
- 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.)
- Granted
Links
Images
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a phase-change toughened low-alloy steel plate and a preparation method thereof, belonging to the technical field of alloy steel. The steel plate comprises the following chemical compositions in percentage by weight: 0.04-0.12 wt. % of C, 0.10-0.50 wt. % of Si, 2.6-3.8 wt. % of Mn, less than 0.02 wt. % of P, and less than 0.01 wt. % of S; and on this basis, one or more of the following alloy elements can be added: 0-0.50 wt. % of Cr, 0-1.0 wt. % of Ni, 0-0.50 wt. % of Mo, 0-0.60 wt. % of Cu, 0-0.05 wt. % of Nb, 0-0.15 wt. % of V, 0-0.12 wt. % of Ti, 0-0.003 wt. % of B and 0.01-0.06 wt. % of Al, wherein the total amount of alloy elements in the steel is not greater than 5%. The phase-change toughened low-alloy steel plate and the preparation method thereof disclosed by the invention have the advantages that cheap elements such as C and Mn are adopted as main alloy elements, and dispersedly distributed metastable austenite phases are obtained in martensite through a C and Mn secondary partition process, so that the low-temperature toughness of the steel can be significantly improved. The phase-change toughened low-alloy steel plate disclosed by the invention has an obvious low-cost advantage in comparison with the traditional Ni-containing low-temperature steel, and can be applied to the fields of low-temperature vessels, oceanographic engineering, engineering machinery, and the like.
Description
Technical field
The invention belongs to the steel alloy technical field, a kind of phase toughness Low Alloy Steel Plate and preparation method thereof particularly is provided.
Background technology
Along with socioeconomic development, the demand of high-strength and high-toughness steel is increasing.The technical way that improves at present the steel obdurability is structure refinement, yet simple structure refinement also can make the even Plasticity Decreasing of steel, yield tensile ratio increase when improving obdurability, is difficult to satisfy the military service security requirement under the high intensified condition comprehensively; On the other hand, when structure refinement (effective particle size is about 5 microns) to a certain degree the time, further the difficulty of refinement enlarges markedly, requirement to processing condition is more and more harsher, depress greatly distortion etc. such as needs low temperature, and this is difficult to realize for the larger steel of some specification.That therefore, need to explore except structure refinement that other improves the steel obdurability organizes principle of adjustment and control and process means.Existing research work shows, metastable austenite an amount of in the steel has vital role for the toughness that improves steel, its principle is that metastable austenite under the stress field effect of crackle forward position martensitic transformation occurs, this phase transformation will be alleviated the stress concentration in crackle forward position, improve crack growth resistance, thereby the ductile-brittle transition temperature of decrease steel, the low-temperature flexibility of raising steel.Utilize this principle, Japan the end of the sixties in last century develop steel used at ultra-low temperature-9Ni steel and production technique thereof.Since the end of the seventies in last century, the feasibility of 5Ni steel replacement 9Ni steel that the J.W. Morris of California, USA Berkeley university has taught study group's systematic study, and further explored the feasibility that the 5Mn steel replaces the 5Ni steel, furtherd investigate on this basis the toughness reinforcing principle of metastable austenite (referring to document: J.W. Morris, Jr., Z. Guo, C.R. Krenn and Y.-H. Kim. The Limits of Strength and Toughness in Steel. ISIJ International, Vol.41 (2001), No.6, pp.599-611.).Use for reference the title of " transformation plasticity (Transformation Induced Plasticity; TRIP) steel " widely applied in the automotive industry, be called the toughness reinforcing steel of above-mentioned metastable austenite " phase toughness (Transformation Induced Toughening) steel " here.Should be noted that, the at present research work of phase toughness steel mainly concentrates on the high interalloy of a few ni content or high quality steel, such as 9Ni steel, 5Ni steel and maraging steel etc., and because the alloying cost of steel is high, complex manufacturing, their application only is confined to some specific area, such as low-temperature (low temperature) vessel, undercarriage etc., be difficult to apply in other field.Therefore, phase toughness low alloy steel is significant for the upgrading that promotes low alloy steel more widely for the cheap and Application Areas of cost of development.
Summary of the invention
The object of the present invention is to provide a kind of phase toughness low alloy steel and steel plate preparation method thereof, adopt the austenite stabilizer element such as cheap C and Mn as main alloy element, steel (carrying out secondary isothermal in the two-phase region scope of γ+α) under the differing temps processes, C, Mn element occur in the isothermal diffuse to γ " partition " process mutually from the α matrix, finally obtain the some amount metastable austenite phase that disperse distributes in matrix, thereby increase substantially the low-temperature flexibility of steel.
The chemical ingredients of phase toughness low alloy steel provided by the invention and content are: C:0.04～0.12wt.%, Si:0.10～0.50wt.%, Mn:2.6～3.8wt.%, P:＜0.02wt.%, S:＜0.01wt.%, and surplus is Fe and inevitable impurity; On this basis, can add in addition following one or more alloying elements: Cr:0～0.50wt.%, Ni:0～1.0wt.%, Mo:0～0.50wt.%, Cu:0～0.60wt.%, Nb:0～0.05wt.%, V:0～0.15wt.%, Ti:0～0.12wt.%, B:0～0.003wt.%, Al:0.01～0.06wt.%, the total addition level of steel interalloy element should be not more than 5%.
The effect of each element of the present invention and proportioning are according to as follows:
Carbon: carbon is austenite stabilizer element, and (it will be enriched in the austenite during two-phase region isothermal of γ+α), improve stabilization of austenite, be conducive to the final acquisition of metastable austenite; In addition, carbon also obviously improves hardening capacity and the intensity of steel.The carbon content scope of steel of the present invention is 0.04～0.12wt.%, and carbon content is lower than 0.04wt.%, and the metastable austenite quantity that obtains is very few, is difficult to play the phase toughness effect; Carbon content is higher than 0.12wt.%, then cementite may occur, and is unfavorable to toughness.
Silicon: one of deoxidant element in the steel, have simultaneously stronger solution strengthening effect, but excessive Si will worsen toughness and the welding property of steel.Comprehensive above-mentioned consideration, the silicone content scope of steel of the present invention is 0.1～0.50wt.%.
Manganese: manganese is the crucial alloying element that steel of the present invention obtains metastable austenite.Identical with the carbon effect, manganese also is austenite stabilizer element, (will enrichment in austenite during the two-phase region isothermal of γ+α), improve stabilization of austenite, be conducive to finally obtain metastable austenite; In addition, manganese obviously improves the hardening capacity of steel, has simultaneously certain solution strengthening effect.The manganese content range of steel of the present invention is 2.6～3.8.wt.%, and manganese content is lower than 2.6wt.%, and the metastable austenite quantity that obtains is few, is difficult to play the phase toughness effect; Manganese content is higher than 3.8wt.%, and then strand heart section quality obviously reduces, and plate property worsens.
Molybdenum: significantly improve the hardening capacity of steel, reduce temper brittleness, improve the resistance for delayed fracture of steel.Also can improve the high temperature dimensional stability of microalloy precipitated phase when Mo and microalloy element add jointly, reduce its alligatoring speed, be conducive to improve the precipitation hardening effect.When molybdenum content surpassed 0.50wt.%, above-mentioned action effect reached capacity, and cost is higher.Therefore, steel molybdenum content of the present invention should be controlled in the 0.50wt.%.
Chromium: improve hardening capacity and the atmospheric corrosion resistance of steel, but higher Cr content is unfavorable to welding property, should be controlled in the 0.50wt.%.
Nickel: nickel is austenite stabilizer element, in that (it will enrichment in austenite during the two-phase region isothermal of γ+α), improves stabilization of austenite, is conducive to finally obtain metastable austenite; In addition, nickel improves hardening capacity and the atmospheric corrosion resistance of steel, but its price is high, should be controlled in the 1.0wt.%.
Copper: improve hardening capacity and the atmospheric corrosion resistance of steel, the nano level Cu phase particle of Precipitation has certain precipitation strength effect, but contains the Cu steel owing to the surface selectivity oxidation is easy to produce hot-short problem.Therefore Cu content is controlled in the 0.60wt.%.
Boron: strong segregation is in austenite grain boundary and other lattice defect place, add micro-B and can significantly improve hardening capacity, but it is saturated that boron content surpasses 0.003% rear above-mentioned effect, but also may form variously to hot workability and the disadvantageous B of the containing precipitated phase of toughness, so boron content should be controlled in the 0.003wt.%.
Niobium: have the effect of organizing after the stronger refinement phase transformation.By solid solution Nb and the deformation induced Nb (C, N) that separates out austenite recrystallization is produced the strongly inhibited effect, thereby obtain non-recrystallization austenite with higher defect concentration, organize after improving follow-up Nucleation rate and refinement phase transformation.In addition, solid solution Nb in austenite improves the hardening capacity successful.Steel content of niobium of the present invention is in 0.05wt.%, and it organizes further thinning effect to become not obvious and the cost raising to be higher than 0.05wt.%.
Vanadium: the VC particle dispersion of Precipitation is tiny from martensite or ferrite matrix, has significant precipitation strength effect.Steel V content of the present invention is controlled in 0.15%, and too high then precipitation strength effect improves not obvious, and cost is higher.
Titanium: when adding trace Ti in the steel (Ti content is less than 0.04wt.%), Ti mainly is combined with N, Precipitation from solid steel, and the TiN particle of formation nano-grade size, its Main Function is austenite grain size in the refinement 2 Mo Steel Slab during Heating Process; When Ti content during greater than 0.04wt.%, except forming TiN (at this moment part TiN also will separate out) from molten steel, residue Ti will be combined with C formation TiC particle, and it has stronger precipitation hardening effect.Steel Ti content of the present invention should be controlled in the 0.12wt.%, and it is not obvious to add its precipitation strength effect increase of too much Ti, and macrobead liquation TiN quantity increases the toughness plasticity of grievous injury steel.
Aluminium: aluminium is strong deoxidant element, also can be combined with N to form AlN, can play Grain refinement.The aluminium content range of steel of the present invention is 0.01～0.06wt.%.
P and s: impurity element in the steel, significantly reduce plasticity and toughness and welding property, its content should be controlled at respectively in 0.02wt.% and the 0.01wt.%.
Phase toughness Low Alloy Steel Plate manufacturing process involved in the present invention is as follows:
Adopt converter or electrosmelting, continuous casting or die casting are adopted in casting.
In process furnace, heat behind continuously cast bloom or the ingot formation, Heating temperature is 1100～1250 ℃, time is 1-5 hour, adopt plate mill to be rolled after the heating, rolling technology is: the rolling 3-8 passage of roughing, the rolling 5-14 passage of finish rolling, finishing temperature is 750～950 ℃, rolls rear direct quenching (DQ) acquisition martensitic stucture or air cooling (AC) to room temperature.
Steel plate hot is processed, and this is the critical process that steel of the present invention obtains excellent low-temperature flexibility.For the DQ steel plate, thermal treatment process comprises intercritical annealing (L) and tempering (T) two procedures, both are all in that (γ+α) two-phase region carries out, be that Heating temperature is higher than Ar1 and is lower than Ar3, difference is that the L operation is carried out under the two-phase region comparatively high temps, corresponding austenite volume fraction is 50%-70%, and the T operation is carried out under the two-phase region lesser temps, and corresponding austenite volume fraction is 8%-20%.The concrete technology parameter is: the intercritical annealing Heating temperature is 720～780 ℃, and soaking time is 0.5-2 hour, shrend after the steel plate heating.Tempering temperature is 620～680 ℃, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after the tempering.
For rolling rear air cooling steel plate, because its original structure is not martensite, need to before intercritical annealing, add the primary quenching operation, namely adopt QLT technique.Quenching temperature will be higher than the Ar3 temperature of steel, to guarantee complete austenitizing and to quench the rear complete martensitic stucture that obtains.The concrete technology parameter is as follows: (Q) Heating temperature of quenching is 800～880 ℃, and soaking time is 0.5-2 hour, shrend after the heating; The intercritical annealing Heating temperature is 720～780 ℃, and soaking time is 0.5-2 hour, shrend after the steel plate heating; Tempering temperature is 620～680 ℃, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after the tempering.Fig. 1 is Heat Treatment Of Steel process schematic representation of the present invention.
The technology controlling and process principle of phase toughness low alloy steel involved in the present invention is:
The main purpose that steel of the present invention is heat-treated is to obtain the metastable austenite phase that in martensitic matrix disperse distributes and has high thermal stability, thereby improves the low-temperature flexibility of steel.The effect of DQ or Q is to obtain martensitic stucture, and martensite lath piece (Block) size that common DQ technique obtains is more tiny than Q technique, thereby is conducive to the obdurability raising.Process in (L) in intercritical annealing subsequently, the partial martensite lath changes austenite into, and partition occurs between martensite and austenite the austenite stabilizer element such as C, Mn, causes C in the austenite, Mn content to increase gradually.In the shrend process, above-mentioned austenite changes martensite again into after annealing, but newly form C in the martensite, the Mn constituent content is higher than matrix martensite.And for the micro-alloyed steel that contains the microalloy elements such as Nb, V, Ti, the Precipitation of microalloy carbonitride from martensitic matrix also can occur in the intercritical annealing heat-processed, it is of a size of nano level, and obvious precipitation strength effect can be provided.In drawing process, the new martensite that forms of part will change austenite again into, the partition second time of C, Mn element occurs between austenite and martensite simultaneously, make the rich Mn of the richer C of austenite, its thermostability significantly improves, and these austenites no longer undergo phase transition and remain when cooling off after the tempering.
The invention has the advantages that:
Adopt the cheap elements such as C, Mn as main alloy element, in martensite, obtain the metastable austenite phase that disperse distributes by secondary partition technique, can significantly improve the low-temperature flexibility of steel; Simultaneously, metastable austenite also has certain effect with respect to the plasticity of improving steel, fatigue property and anti-hydrogen-induced fracture performance.
Adopt plate mill to be rolled into steel plate, adopt again the critical zone thermal treatment process to heat-treat, steel plate has the cooperation of excellent intensity, toughness and plasticity: yield strength is that-100 ℃ of ballistic works of 500MPa grade steel plate can reach more than the 200J, unit elongation is about 34%, and the product of tensile strength and unit elongation (strength and ductility product) surpasses 20GPa%; Yield strength 750MPa grade steel plate-100 ℃ ballistic work surpasses 100J, and unit elongation is 23%.
Contain the Ni low-temperature steel with tradition and compare, the low-cost advantage of steel of the present invention is obvious, can be applied to the fields such as low-temperature (low temperature) vessel, oceanographic engineering, engineering machinery.
Description of drawings
Fig. 1 is the rolling process schematic representation of steel plate hot of the present invention.
Fig. 2 is steel plate heat treatment process synoptic diagram of the present invention.
Fig. 3 is the XRD figure spectrum of 2# steel.
Fig. 4 is the XRD figure spectrum of 4# steel.
Fig. 5 is 2# transmission electron microscope bright field image, has shown pattern and the distribution of metastable austenite.
Fig. 6 is 4# steel transmission electron microscope dark field image, has shown pattern and the distribution of metastable austenite and precipitated phase.
Fig. 7 is 4# steel transmission electron microscope bright field image, has shown the pattern of precipitated phase.
Embodiment
Steel of the present invention is smelted by the laboratory vacuum induction furnace, totally 5 stoves, wherein 3 stoves are C-Mn-Nb micro-alloyed steel (1#, 2#, 3#), 2 stoves are for adding an amount of Ti and Mo again on C-Mn-Nb composition basis, purpose is further to improve the intensity of steel by the Precipitation of (Ti, Mo) C.Concrete chemical ingredients is as shown in table 1.Above-mentioned steel ingot casting is become the 50kg billet, and then hammer cogging is swaged into and is of a size of 50mm(thickness) * 60mm(width) * 80mm(length) steel billet.Above-mentioned steel billet behind 1200 ℃ of insulation 2h, is rolled into the steel plate that thickness is 11mm through the laboratory reversable mill.Adopt two stage rolling techniques, the roughing finishing temperature is 1020 ℃, rolling 2 passages, and 50mm is compressed to 36mm from thickness; The finish rolling start rolling temperature is 920 ℃, and finishing temperature is 850 ℃, rolling 5 passages.Roll rear water-cooled to room temperature, obtain martensitic stucture.
Thermal treatment process is: steel plate 750 ℃ of insulations after 1 hour (L) in this process, finish the partition first time of C, Mn element, shrend is to room temperature after the insulation, then steel plate is finished the partition second time of C, Mn element 650 ℃ of tempering 1 hour, is cooled to room temperature after the tempering.
Table 1 steel chemical composition of the present invention (wt.%), surplus are Fe
Measured the tensile property of steel plate after the thermal treatment and summer under the differing temps than v-notch ballistic work, the result is as shown in table 2.By table as seen, steel of the present invention has shown the cooperation of excellent intensity, toughness and plasticity.For the C-Mn-Nb component steel, its yield strength is about 500MPa, and-100 ℃ of ballistic works can reach more than the 200J, and unit elongation surpasses 30%, and the product of tensile strength and unit elongation (strength and ductility product) surpasses 20GPa%, and having reached the TRIP rigidity can level.It can also be seen that in addition, improve carbon content and can damage to a certain extent toughness.For the C-Mn-Nb-Mo-Ti component steel, because the precipitation strength effect of (Ti, Mo) C particle, yield strength is brought up to more than the 750MPa, and ℃ ballistic work is still higher simultaneously-100, surpasses 100J.
The tensile property of table 2 steel of the present invention and lower summer of differing temps are than v-notch ballistic work
Adopt X-ray diffraction to survey the XRD figure spectrum of 2# steel and 4# steel, the result diffraction peak of austenite phase occurred as shown in Figures 2 and 3 in the visible diffraction spectra, and quantitative analysis shows that its austenitic volume fraction is respectively 8.77% and 13.50%.Fig. 4 is the transmission electron microscope bright field image of 2# steel, and the part metastable austenite marks with " A ", and visible austenite is sheet, is distributed between the former martensite lath, and its thickness is approximately the 0.1-0.2 micron; In addition, former martensite its dislocation desity after the thermal treatment of critical zone obviously reduces, but still has substantially kept panel construction.Fig. 5 is the transmission electron microscope dark field image of 4# steel, and wherein metastable austenite is shown as light tone mutually, and its shape is similar to the 2# steel to distribution characteristics.Can also see in addition the precipitated phase that a large amount of disperses distribute, its size is about 10nm, they be in the intercritical annealing process from martensitic matrix the microalloy carbonitride of Precipitation.Fig. 6 has provided 4# steel transmission electron microscope bright field image, has further shown the shape characteristic of nano level precipitated phase.
Claims (3)
1. phase toughness Low Alloy Steel Plate, it is characterized in that, adopt converter or electrosmelting, the weight percentage of each composition is in the steel plate: C:0.04～0.12wt.%, Si:0.10～0.50wt.%, Mn:2.6～3.8wt.%, P:＜0.02wt.%, S:＜0.01wt.%, and surplus is Fe and inevitable impurity; Be weight percentage.
2. phase toughness Low Alloy Steel Plate according to claim 1 is characterized in that, on the basis of mentioned component, adds following one or more alloying elements: Cr:0～0.50wt.%, Ni:0～1.0wt.%, Mo:0～0.50wt.% again; Cu:0～0.60wt.%, Nb:0～0.05wt.%, V:0～0.15wt.%; Ti:0～0.12wt.%, B:0～0.003wt.%, Al:0.01～0.06wt.%, the total addition level of alloying element should be not more than 5%; Be weight percentage.
3. the manufacture method of a claim 1 or 2 described phase toughness Low Alloy Steel Plates is characterized in that:
(1) will heat in the process furnace of packing into behind continuously cast bloom or the ingot formation, Heating temperature is 1100-1250 ℃, and the time is 1-5 hour, is rolled after the heating;
(2) plate mill is rolling
The plate mill rolling technology is: the rolling 3-8 passage of roughing, and the rolling 5-14 passage of finish rolling, finishing temperature is 750-950 ℃, rolls rear direct quenching DQ acquisition martensitic stucture or air cooling AC to room temperature;
(3) steel plate hot is processed
For the DQ steel plate, thermal treatment process comprises intercritical annealing L and tempering T two procedures, and wherein intercritical annealing Heating temperature is 720～780 ℃, and soaking time is 0.5-2 hour, shrend after the steel plate heating;
Tempering temperature is 620～680 ℃, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after the tempering;
For rolling rear air cooling steel plate, need to before intercritical annealing, add the primary quenching operation, namely adopt QLT technique, the concrete technology parameter is as follows: quenching Q Heating temperature is 800～880 ℃, soaking time is 0.5-2 hour, shrend after the heating; The intercritical annealing Heating temperature is 720～780 ℃, and soaking time is 0.5-2 hour, shrend after the steel plate heating; Tempering temperature is 620～680 ℃, and soaking time is 0.5-5 hour, air cooling or be cooled to room temperature after the tempering.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210518442.6A CN102965568B (en) | 2012-12-05 | 2012-12-05 | Phase toughness Low Alloy Steel Plate and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210518442.6A CN102965568B (en) | 2012-12-05 | 2012-12-05 | Phase toughness Low Alloy Steel Plate and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102965568A true CN102965568A (en) | 2013-03-13 |
| CN102965568B CN102965568B (en) | 2016-03-02 |
Family
ID=47796003
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201210518442.6A Active CN102965568B (en) | 2012-12-05 | 2012-12-05 | Phase toughness Low Alloy Steel Plate and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102965568B (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103710622A (en) * | 2013-12-20 | 2014-04-09 | 钢铁研究总院 | 690MPa-yield-strength low-yield-tensile-ratio antiseismic steel and manufacturing method thereof |
| CN104120349A (en) * | 2014-07-23 | 2014-10-29 | 舞阳钢铁有限责任公司 | F-grade large-thickness weldable steel plate with high pureness and high low-temperature toughness and production method thereof |
| CN104195470A (en) * | 2014-07-29 | 2014-12-10 | 锐展(铜陵)科技有限公司 | Automobile hub alloy steel and manufacturing process thereof |
| CN105422590A (en) * | 2015-11-18 | 2016-03-23 | 宁波金鹏高强度紧固件有限公司 | Nut plate |
| CN106755774A (en) * | 2016-12-06 | 2017-05-31 | 上海电机学院 | A kind of heat treatment method of low-carbon and low-alloy high-strength steel |
| CN108385037A (en) * | 2018-03-23 | 2018-08-10 | 东北大学 | A kind of ocean platform Ti microalloying medium managese steel cut deals and preparation method thereof |
| CN109609848A (en) * | 2018-12-24 | 2019-04-12 | 钢铁研究总院 | High tough antifatigue nano-scaled precipitate enhancing Ma-Austria's Multiphase Steel and preparation method thereof |
| CN111041165A (en) * | 2019-12-26 | 2020-04-21 | 钢铁研究总院 | Medium manganese oil well pipe steel and preparation method thereof |
| CN112853224A (en) * | 2021-01-06 | 2021-05-28 | 东北大学 | High-strength high-plasticity low-carbon medium-manganese TRIP steel and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6348108B1 (en) * | 1998-03-04 | 2002-02-19 | National Research Institute For Metals | High toughness steel and a method for manufacturing the same |
| CN101270455A (en) * | 2007-03-23 | 2008-09-24 | 宝山钢铁股份有限公司 | 1000MPa grade nickel-saving type metastable austenite stainless steel |
| CN101638749A (en) * | 2009-08-12 | 2010-02-03 | 钢铁研究总院 | Automobile steel with low cost and high strength ductility balance and preparation method thereof |
-
2012
- 2012-12-05 CN CN201210518442.6A patent/CN102965568B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6348108B1 (en) * | 1998-03-04 | 2002-02-19 | National Research Institute For Metals | High toughness steel and a method for manufacturing the same |
| CN101270455A (en) * | 2007-03-23 | 2008-09-24 | 宝山钢铁股份有限公司 | 1000MPa grade nickel-saving type metastable austenite stainless steel |
| CN101638749A (en) * | 2009-08-12 | 2010-02-03 | 钢铁研究总院 | Automobile steel with low cost and high strength ductility balance and preparation method thereof |
Non-Patent Citations (3)
| Title |
|---|
| 史学星: "临界区热处理对5NiCrMo钢性能与组织的影响", 《中国优秀硕士学位论文全文数据库 工程科技I辑》, no. 09, 15 September 2008 (2008-09-15), pages 022 - 9 * |
| 沈继刚等: "轧后直接淬火技术在高强度中厚板生产中的应用", 《宽厚板》, vol. 16, no. 5, 31 October 2010 (2010-10-31), pages 14 - 17 * |
| 赵先存等: "《高强度超高强度不锈钢》", 31 May 2008, article "利用亚稳奥氏体使钢韧化", pages: 26 * |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103710622A (en) * | 2013-12-20 | 2014-04-09 | 钢铁研究总院 | 690MPa-yield-strength low-yield-tensile-ratio antiseismic steel and manufacturing method thereof |
| CN104120349A (en) * | 2014-07-23 | 2014-10-29 | 舞阳钢铁有限责任公司 | F-grade large-thickness weldable steel plate with high pureness and high low-temperature toughness and production method thereof |
| CN104195470A (en) * | 2014-07-29 | 2014-12-10 | 锐展(铜陵)科技有限公司 | Automobile hub alloy steel and manufacturing process thereof |
| CN105422590A (en) * | 2015-11-18 | 2016-03-23 | 宁波金鹏高强度紧固件有限公司 | Nut plate |
| CN106755774A (en) * | 2016-12-06 | 2017-05-31 | 上海电机学院 | A kind of heat treatment method of low-carbon and low-alloy high-strength steel |
| CN108385037A (en) * | 2018-03-23 | 2018-08-10 | 东北大学 | A kind of ocean platform Ti microalloying medium managese steel cut deals and preparation method thereof |
| CN108385037B (en) * | 2018-03-23 | 2020-05-19 | 东北大学 | Ti microalloyed medium manganese steel medium plate for ocean platform and preparation method thereof |
| CN109609848A (en) * | 2018-12-24 | 2019-04-12 | 钢铁研究总院 | High tough antifatigue nano-scaled precipitate enhancing Ma-Austria's Multiphase Steel and preparation method thereof |
| CN111041165A (en) * | 2019-12-26 | 2020-04-21 | 钢铁研究总院 | Medium manganese oil well pipe steel and preparation method thereof |
| CN112853224A (en) * | 2021-01-06 | 2021-05-28 | 东北大学 | High-strength high-plasticity low-carbon medium-manganese TRIP steel and preparation method thereof |
| CN112853224B (en) * | 2021-01-06 | 2021-11-05 | 东北大学 | High-strength high-plasticity low-carbon medium-manganese TRIP steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102965568B (en) | 2016-03-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102965568B (en) | Phase toughness Low Alloy Steel Plate and preparation method thereof | |
| CN103014554B (en) | Low-yield-ratio high-tenacity steel plate and manufacture method thereof | |
| CN106244918B (en) | A kind of 1500MPa grades of high strength and ductility automobile steel and its manufacture method | |
| CN103060678B (en) | A kind of warm-working nanometer austenite strengthens plasticising steel and preparation method thereof | |
| CN101649420B (en) | Ultra-strength, high toughness and low yield ratio steel and steel plate and manufacturing method thereof | |
| CN103320717B (en) | Ultra high-strength high titanium steel plate with yield strength of 960 MPa and preparing method of same | |
| CN102758133B (en) | 1000MPa-level automobile steel with high product of strength and elongation and manufacturing method thereof | |
| CN108728743B (en) | Ocean engineering steel with good low-temperature fracture toughness and manufacturing method thereof | |
| CN103255341B (en) | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof | |
| CN103080357B (en) | High-strength cold-rolled steel sheet having excellent stretch flange properties, and process for production thereof | |
| CN110484834B (en) | Cr and Mn alloyed TRIP steel and preparation method thereof | |
| CN103710622A (en) | 690MPa-yield-strength low-yield-tensile-ratio antiseismic steel and manufacturing method thereof | |
| CN106319390B (en) | X70 large deformation resistant pipeline steel and manufacturing method thereof | |
| CN102952994B (en) | Refractory anti-seismic construction steel and production method thereof | |
| CN102618793B (en) | Steel plate with yield strength of 960MPa and manufacturing method thereof | |
| CN108018484A (en) | A kind of tensile strength is in more than 1500MPa and the cold rolling high-strength steel and its manufacture method that have excellent moldability | |
| CN101928875A (en) | High-strength cold-rolled steel sheet with good forming performance and preparation method thereof | |
| CN103060703A (en) | 780MPa grade cold rolling biphase strip steel and manufacturing method thereof | |
| CN105274432A (en) | 600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof | |
| CN104513927A (en) | High-strength high-rigidity steel plate with tensile strength of 800 MPa and preparation method thereof | |
| CN105112782A (en) | Low-temperature ferrite LT-FH40 steel plate applied to hot-rolled ships and production method thereof | |
| CN102691018A (en) | Low-compression ratio super-strength steel plate for ocean engineering and manufacturing method thereof | |
| CN102605252A (en) | Steel plate with yield strength grade of 1030MPa and manufacturing method thereof | |
| CN104711482A (en) | Nitrogen-controlled martensitic stainless steel and manufacturing method thereof | |
| CN103320701A (en) | Ferrite bainite advanced high strength steel plate and manufacturing method thereof |
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 |