WO2013044641A1 - 一种屈服强度700MPa级高强度高韧性钢板及其制造方法 - Google Patents
一种屈服强度700MPa级高强度高韧性钢板及其制造方法 Download PDFInfo
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- WO2013044641A1 WO2013044641A1 PCT/CN2012/076052 CN2012076052W WO2013044641A1 WO 2013044641 A1 WO2013044641 A1 WO 2013044641A1 CN 2012076052 W CN2012076052 W CN 2012076052W WO 2013044641 A1 WO2013044641 A1 WO 2013044641A1
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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/30—Stress-relieving
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- 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
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- 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
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- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
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- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
Definitions
- the present invention relates to a high strength and high toughness steel sheet, and in particular to a high strength and high toughness steel sheet having a yield strength greater than 700 MPa and a method for producing the same.
- the steel plate of the invention has good low temperature toughness and is suitable for high-strength, high-toughness and impact-resistant structural steel plates in industries such as automobiles, construction machinery and ship hull structures. Background technique
- low-alloy high-strength steel is widely used in military, automobile, mining machinery, construction machinery, agricultural machinery and railway transportation.
- the complexity, large-scale and lightweight of various military and civilian equipment put forward higher requirements for this type of steel, that is, low-alloy high-strength steel sheets used to manufacture these equipments not only require more High hardness and strength, but also good toughness and formability.
- the development and application of high-strength steel sheets have developed rapidly.
- This type of steel is developed on the basis of low-alloy high-strength weldable steel.
- the service life can be several times that of traditional structural steel plates.
- the production process is relatively simple. Generally, it is directly cooled or quenched after rolling, or it is extracted offline. Fire process, or enhanced by controlled rolling and controlled cooling process.
- high-strength steel In the production of low-alloy high-strength steel sheets for automobiles, construction machinery and ship hull structures, the traditional process adds more precious alloy elements such as Cu, Ni, Cr and Mo, which is costly. At present, high-strength steel begins to be low-cost economy. Type and high cost and high performance development.
- the alloying elements added by high-strength steel produced by domestic steel mills are mostly rich in resources such as V, Ti, Cr, Si, Mn, B, RE, etc., and the addition amount is generally 3%.
- high-strength steels of ship hull structure, automobile, mining machinery, engineering machinery and other industries with higher strength level, such as 700MPa grade high-strength steel plate with yield strength it is necessary to supplement a certain amount of Cu, Ni, Cr, Mo and other elements to improve performance.
- This steel has a yield strength of up to 700 MPa, but has low temperature toughness and cannot be used for -60 °C or even -80 °C low temperature impact on military ship hull structures and civil equipment.
- high-strength steels with a yield strength of 700 MPa or more still rely mainly on imports.
- Patent documents relating to high-strength and high-toughness steel sheets having a yield strength of about 700 MPa or more such as WO 200039352 A, disclose a low-temperature steel having a low carbon content (0.03-0.12%) and a high nickel content ( The method of not less than 1.0%) produces high-strength steel with good low-temperature toughness, and its lower cooling rate (10 °C/s) can reach a tensile strength of 930 MPa or more.
- WO 9905335A whose composition has a low carbon content of 0.05-0.10%, but is alloyed with a higher content of Mn, Ni, Mo and Nb. After hot rolling, it is only quenched and tempered, and the tensile strength of the steel sheet can be achieved. Above 830 MPa, its -40 °C Xia's impact energy is at least 175J.
- An object of the present invention is to provide a high-strength and high-toughness steel sheet having a yield strength of 700 MPa or more, particularly a medium-thick steel sheet having a thickness of 6 to 25 mm.
- the present invention has a high strength and high toughness medium-thickness steel plate having a yield strength of 700 MPa or more, and the chemical composition thereof has a weight percentage of C: 0.03-0.06%, Si ⁇ 0.30%, Mn: 1.0-1.5%, P. ⁇ 0.020%, S ⁇ 0.010%, Al: 0.02-0.05%, Ti: 0.005-0.025%, N ⁇ 0.006%, Ca ⁇ 0.005%, and one or more of Cr 0.75%, Ni 0.40%, and Mo 0.30% The balance is iron and inevitable impurities.
- C 0.031-0.059%.
- Si 0.03-0.30%.
- Mn 1.02-1.5%.
- P is 0.015%.
- S 0.005%.
- Al 0.02-0.046%.
- Ni 0.10-0.40, more preferably 0.13-0.36%.
- Cr 0.3-0.75%, more preferably 0.32-0.75%.
- Mo 0.10-0.30%, more preferably 0.13-0.26%.
- Ti 0.01 to 0.025%.
- N 0.005%.
- the content refers to the content by weight.
- the structure of the steel sheet is tempered martensite + dispersed carbide.
- Another object of the present invention is to provide a method for producing the above high strength and high toughness medium and thick steel plate, the method comprising:
- the molten steel is subjected to continuous decasting or die casting after vacuum degassing. After casting, it needs to be initially rolled into a slab; the continuous casting billet or billet is heated at 1100-1250 °C and then subjected to one or more passes in the austenite recrystallization zone. Secondary rolling, total reduction rate > 70%; finish rolling temperature > 860 ° ( ;
- the steel plate After rolling, the steel plate is rapidly water-cooled to 200-300 °C at 15-50 °C / s, air-cooled 5-60 s;
- the cooled steel plate enters the in-line heating furnace and is rapidly heated at 1-10 °C / s to 450-550 °C for tempering for 15-45 seconds, and then air-cooled.
- the finishing temperature is 860-900 °C.
- the cooled steel sheet enters the in-line heating furnace and is rapidly heated at -10 ° C / s to 450-500 ° C for tempering for 15-45 s, and then air-cooled.
- the in-line heating furnace is an induction heating furnace.
- the post-rolling cooling rate of the steel sheet cannot be lower than 15 °C/s.
- the purpose is to ensure that the martensite structure is obtained after cooling, avoiding the formation of bainite.
- the upper limit of the cooling rate is limited by the cooling capacity of the equipment after cooling and the final cooling temperature. Therefore, the present invention uses a cooling rate range of 15-50 ° C / s.
- the invention realizes fine grain strengthening, phase transformation strengthening and precipitation strengthening by suitable component design, heating, controlled rolling, rapid cooling and tempering after rolling, improves the strength and hardness of the steel plate, and has high low temperature toughness.
- the tissue appears as tempered martensite + dispersed carbide. 6-25mm thick steel plate yield strength > 700MPa, elongation A 5 Q > 18%, -60 °C A KV > 150J, excellent cold bending performance, meeting the high strength and high strength of industries such as automobiles, construction machinery and ship hull structure Higher requirements for ductile steel.
- Fig. 1 is a photograph showing a typical metallographic structure of a 6 mm thick high strength steel sheet according to Example 1 of the present invention.
- Fig. 2 is a photograph showing a typical metallographic structure of a 25 mm thick high strength steel sheet according to Example 5 of the present invention.
- Carbon A key element in ensuring the strength of the steel. Carbon is the most important element for obtaining a steel sheet whose structure is mostly martensite, which can significantly improve the hardenability of the steel sheet. An increase in the carbon content causes an increase in strength and hardness and a decrease in plasticity. Therefore, if the steel plate needs to obtain both high strength and high toughness, the carbon content must be considered comprehensively. In order to ensure excellent weldability and good low temperature toughness, the carbon content in the steel is reduced to less than 0.06%. For the 700 MPa strength level of the yield strength of the present invention, in order to obtain a high low temperature impact toughness, it is suitable to use a lower carbon content of 0.03 - 0.06%.
- Silicon Adding silicon to steel improves steel purity and deoxidation. Silicon acts as a solid solution strengthening in steel. However, if the silicon content is too high, the viscosity of the scale when the steel sheet is heated is large, and the descaling after the furnace is difficult, resulting in serious red scale on the surface of the steel sheet after rolling, and the surface quality is poor. And high silicon is not conducive to soldering performance. Considering the influence of various aspects of silicon, the silicon content of the present invention is 0.30% or less.
- Manganese stabilizes the austenitic structure. Its ability is second only to the alloying element nickel. It is an inexpensive stable austenite and strengthening alloying element. At the same time, manganese increases the hardenability of steel and reduces the critical cooling rate of martensite formation. However, manganese has a high tendency to segregation, so its content should not be too high. Generally, the manganese content of low carbon microalloyed steel does not exceed 2.0%. The amount of manganese added depends mainly on the strength level of the steel. The manganese content of the present invention should be controlled at 1.0 to 1.5%. Manganese also acts as a deoxidizer together with aluminum in steel.
- Sulfur and phosphorus Sulfur is combined with manganese in steel to form plastic inclusions, manganese sulfide, especially for the transverse plasticity and toughness of steel, so the sulfur content should be as low as possible. Phosphorus is also a harmful element in steel, which seriously damages the plasticity and toughness of the steel sheet. For the purposes of the present invention, both sulfur and phosphorus are unavoidable impurity elements and should be as low as possible. The present invention requires P 0.020%, S 0.010%, taking into account the actual steelmaking level of the steel mill.
- Aluminum Strong deoxidation. In order to ensure that the oxygen content in the steel is as low as possible, the aluminum content is controlled at
- the excess aluminum in the deoxidized aluminum and the nitrogen in the steel can form A1N precipitates, increase the strength and refine the elemental austenite grain size of the steel during heat treatment.
- Titanium is a strong carbide forming element.
- the addition of a small amount of Ti in the steel is beneficial to the fixation of N in the steel.
- the TiN formed can make the austenite grains not excessively increase when the billet is heated, and refine the original austenite grains. degree.
- Titanium can also be combined with carbon and sulfurized in steel to form TiC, TiS, Ti 4 C 2 S 2 , etc., which are present in the form of inclusions and second phase particles. These carbonitride precipitates of titanium also prevent grain growth in the heat-affected zone during welding and improve weldability.
- the titanium content of the present invention is controlled to be from 0.005 to 0.025%.
- Chromium increases the hardenability of steel and increases the tempering stability of steel. Chromium has a high solubility in austenite, stabilizes austenite, and is solid-solved in martensite after quenching. In the subsequent tempering process, carbides such as Cr 23 C 7 and Cr 7 C 3 are precipitated. The strength and hardness of steel. In order to maintain the strength level of steel, chromium can partially replace manganese, which weakens the segregation tendency of high manganese. In combination with the fine carbide precipitation of the in-line rapid induction heating tempering technique, the alloy content can be correspondingly reduced, so that the present invention can add not more than 0.75% of chromium, preferably 0.3-0.75%.
- Nickel Stabilizing austenite elements has no significant effect on strength.
- the present invention can add not more than 0.40% of nickel element, preferably 0.10-0.40. %, more preferably 0.13-0.36%.
- Molybdenum significantly refines grains and improves strength and toughness. Molybdenum can reduce the temper brittleness of steel, and at the same time, it can precipitate very fine carbides during tempering, which significantly strengthens the steel matrix. Since molybdenum is a very expensive strategic alloying element, only molybdenum of not more than 0.30% is added in the present invention, preferably 0.10 to 0.30%. More preferably, it is 0.13-0.26%.
- Calcium in steel mainly changes the form of sulfide, improving the thickness, transverse properties and cold bending properties of steel. Steels with very low sulfur content may also be treated without calcium.
- the invention can treat calcium according to the level of sulfur, and the calcium content is 0.005%.
- Converter blowing and vacuum treatment The purpose is to ensure the basic composition requirements of the molten steel, remove harmful gases such as oxygen and hydrogen in the steel, and add necessary alloying elements such as manganese and titanium to adjust the alloying elements.
- Heating and rolling The continuous casting billet or billet is heated at a temperature of 1100-1250 °C to obtain a homogenous austenitic structure on the one hand and partially dissolve the compound of an alloying element such as titanium, chromium or molybdenum on the other hand. Rolling into steel sheets in one or more passes in the austenite recrystallization temperature range, the total reduction rate is not less than 70%, and the finishing temperature is not lower than 860 ° C;
- Rapid cooling After rolling, the steel plate is rapidly cooled to 15-50 °C / s to 200-300 °C air-cooling 5-60s; during rapid cooling, most of the alloying elements are solid-dissolved into martensite.
- the cooled steel plate enters the in-line heating furnace and is rapidly heated at 1-10 °C/s to 450-550 °C for tempering for 15-45 seconds, and then air-cooled. Tempering helps to eliminate internal stresses generated during quenching and to eliminate microcracks in or between martensite laths, to diffuse part of the carbide strengthening, and to improve the strong molding, toughness and cold bending properties.
- the invention realizes fine grain strengthening, phase transformation strengthening and precipitation strengthening by suitable component design, heating, controlled rolling, rapid cooling after rolling and self-tempering, thereby improving the strength and hardness of the steel plate and having high low temperature. Toughness, the structure appears as tempered martensite + dispersed carbide.
- the yield strength of 6-25mm thick steel plate is >700MPa, and the elongation is A 5 . >18%, -60°C A kv > 150J, excellent cold bending performance, meeting the high requirements of high strength and high toughness steel plates in industries such as automobiles, construction machinery and ship hull structures.
- the molten steel smelted according to the ratio of Table 1 is subjected to vacuum degassing treatment, and then continuous casting or die casting, the thickness of the slab is 80 mm, and the obtained billet is heated at 1200 ° C, and then subjected to multi-pass rolling in the austenite recrystallization temperature range. , rolled into a steel plate with a thickness of 6mm, the total reduction rate is 94%, the final rolling temperature is 880 °C, then water cooled to 220 °C at 50 °C / s and then rapidly heated to 450 °C on the line to temper, then Air cooled to room temperature;
- Fig. 1 The metallographic structure of part of the steel plate of this embodiment is shown in Fig. 1.
- Figure 1 is a metallographic structure diagram of a 6 mm thick steel plate according to Embodiment 1 of the present invention.
- Fig. 2 is a view showing the metallographic structure of a 25 mm thick steel plate according to Example 5 of the present invention.
- the structure of the steel sheet is tempered martensite and dispersed carbide.
- ⁇ is processed by the above-mentioned components and process parameters, and the yield strength of the 6-25 mm thick finished steel sheet is > 700 MPa, and the elongation is A 5 . > 18%, -60 °C A kv > 150J, excellent cold bending performance, the structure appears as tempered martensite + dispersed carbide.
- the steel plate meets the high requirements of high-strength and high-toughness steel plates in related industries. The products are suitable for the production of ship hull structure, automobile and engineering machinery, etc., with wide application value and market prospects.
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Abstract
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Priority Applications (7)
Application Number | Priority Date | Filing Date | Title |
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KR1020147000186A KR20140026600A (ko) | 2011-09-26 | 2012-05-25 | 700MPa의 항복 강도를 갖는 고-강도 및 고-인성 강판 및 이의 제조방법 |
JP2014517406A JP5750547B2 (ja) | 2011-09-26 | 2012-05-25 | 降伏強さが700MPa級の高強度高靭性鋼板及びその製造方法 |
EP12836495.7A EP2762594B1 (en) | 2011-09-26 | 2012-05-25 | High-strength and high-toughness steel plate with yield strength being 700 mpa and manufacturing method thereof |
BR112013032424-4A BR112013032424B1 (pt) | 2011-09-26 | 2012-05-25 | PLACA DE AÇO COM ALTA RESISTÊNCIA E ALTA TENACIDADE COM LIMITE DE ESCOAMENTO DE 700Mpa, E MÉTODO PARA SUA PRODUÇÃO |
US14/129,103 US9771639B2 (en) | 2011-09-26 | 2012-05-25 | High-strength and high-toughness steel plate with yield strength of 700 MPa and method of manufacturing the same |
RU2014110117/02A RU2593567C2 (ru) | 2011-09-26 | 2012-05-25 | Высокопрочная стальная полоса с высокой ударной вязкостью и пределом текучести 700 мпа и способ ее производства |
ES12836495.7T ES2610246T3 (es) | 2011-09-26 | 2012-05-25 | Plancha de acero de alta resistencia y alta tenacidad siendo el límite elástico de 700 MPa y método de fabricación de la misma |
Applications Claiming Priority (2)
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CN201110288952.4 | 2011-09-26 | ||
CN201110288952.4A CN103014539B (zh) | 2011-09-26 | 2011-09-26 | 一种屈服强度700MPa级高强度高韧性钢板及其制造方法 |
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WO2013044641A1 true WO2013044641A1 (zh) | 2013-04-04 |
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PCT/CN2012/076052 WO2013044641A1 (zh) | 2011-09-26 | 2012-05-25 | 一种屈服强度700MPa级高强度高韧性钢板及其制造方法 |
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US (1) | US9771639B2 (zh) |
EP (1) | EP2762594B1 (zh) |
JP (1) | JP5750547B2 (zh) |
KR (1) | KR20140026600A (zh) |
CN (1) | CN103014539B (zh) |
BR (1) | BR112013032424B1 (zh) |
ES (1) | ES2610246T3 (zh) |
RU (1) | RU2593567C2 (zh) |
WO (1) | WO2013044641A1 (zh) |
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US9499890B1 (en) | 2012-04-10 | 2016-11-22 | The United States Of America As Represented By The Secretary Of The Navy | High-strength, high-toughness steel articles for ballistic and cryogenic applications, and method of making thereof |
CN103614624B (zh) * | 2013-11-27 | 2018-09-04 | 内蒙古包钢钢联股份有限公司 | 一种含高密度析出相低合金高强度钢板带及轧制工艺 |
CN105506494B (zh) * | 2014-09-26 | 2017-08-25 | 宝山钢铁股份有限公司 | 一种屈服强度800MPa级高韧性热轧高强钢及其制造方法 |
CN104532157A (zh) * | 2014-12-19 | 2015-04-22 | 宝山钢铁股份有限公司 | 一种屈服强度900~1000MPa级调质高强钢及其生产方法 |
CN105714199A (zh) * | 2016-05-04 | 2016-06-29 | 芜湖市爱德运输机械有限公司 | 一种斗式提升机 |
KR102065276B1 (ko) * | 2018-10-26 | 2020-02-17 | 주식회사 포스코 | 극저온 인성 및 연성이 우수한 압력용기용 강판 및 그 제조 방법 |
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US9771639B2 (en) | 2017-09-26 |
CN103014539A (zh) | 2013-04-03 |
BR112013032424B1 (pt) | 2019-06-25 |
JP5750547B2 (ja) | 2015-07-22 |
KR20140026600A (ko) | 2014-03-05 |
EP2762594A1 (en) | 2014-08-06 |
JP2014523487A (ja) | 2014-09-11 |
US20140116578A1 (en) | 2014-05-01 |
EP2762594B1 (en) | 2016-11-23 |
CN103014539B (zh) | 2015-10-28 |
ES2610246T3 (es) | 2017-04-26 |
RU2014110117A (ru) | 2015-09-20 |
EP2762594A4 (en) | 2015-08-12 |
RU2593567C2 (ru) | 2016-08-10 |
BR112013032424A2 (pt) | 2017-01-17 |
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