WO2013044640A1 - 一种低屈强比高韧性钢板及其制造方法 - Google Patents

一种低屈强比高韧性钢板及其制造方法 Download PDF

Info

Publication number
WO2013044640A1
WO2013044640A1 PCT/CN2012/076049 CN2012076049W WO2013044640A1 WO 2013044640 A1 WO2013044640 A1 WO 2013044640A1 CN 2012076049 W CN2012076049 W CN 2012076049W WO 2013044640 A1 WO2013044640 A1 WO 2013044640A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel plate
yield ratio
high toughness
low yield
steel
Prior art date
Application number
PCT/CN2012/076049
Other languages
English (en)
French (fr)
Inventor
张爱文
焦四海
袁向前
陈钰珊
Original Assignee
宝山钢铁股份有限公司
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by 宝山钢铁股份有限公司 filed Critical 宝山钢铁股份有限公司
Priority to US14/129,052 priority Critical patent/US9683275B2/en
Priority to JP2014513889A priority patent/JP5750546B2/ja
Priority to ES12836145.8T priority patent/ES2670008T3/es
Priority to BR112013033257-3A priority patent/BR112013033257B1/pt
Priority to KR1020137035012A priority patent/KR20140017001A/ko
Priority to EP12836145.8A priority patent/EP2762598B1/en
Priority to RU2014109120/02A priority patent/RU2588755C2/ru
Publication of WO2013044640A1 publication Critical patent/WO2013044640A1/zh

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a high-toughness hot-rolled steel sheet and a method for producing the same, and particularly to a low-yield ratio high-toughness steel sheet having a yield strength of 500 MPa and a method for producing the same.
  • the steel sheet of the present invention has a low yield ratio, and the conveying line made of the steel sheet is suitable for use in an earthquake-prone area and is resistant to large deformation. Background technique
  • CN101962733A discloses a low-cost, high-strength X80 grade large deformation resistant pipeline steel and a production method thereof, wherein C: 0.02-0.08%, Si ⁇ 0.40%, Mn: 1.2-2.0%, P ⁇ 0.015%, S ⁇ 0.004%, Cu ⁇ 0.40%, Ni ⁇ 0.30%, Mo: 0.10-0.30%, Nb: 0.03-0.08%, Ti: 0.005-0.03%, the production process is soaked at 1200-1250 °C, recrystallization zone The final rolling temperature is 1000-1050 °C, the finishing rolling temperature is 880-950 °C, the finishing rolling temperature is 780-850 °C, the two-stage air cooling is l-3 °C / s to Ar 3 below 20-80 °C.
  • An object of the present invention is to provide a steel sheet for a low yield ratio high toughness pipeline having a yield strength of 500 MPa or more, particularly a steel sheet having a thickness of 10 to 25 mm.
  • This steel can be used in high-incidence areas for earthquakes and steel pipes for large strain transmission lines.
  • the yield strength of the present invention is 500 MPa or more, and the low yield ratio is high toughness.
  • the weight fraction of the chemical composition of the steel plate is: C: 0.05-0.08%, Si: 0.15-0.30%, Mn: 1.55-1.85%, P ⁇ 0.015%, S 0.005%, Al: 0.015-0.04%, Nb : 0.015-0.025%, Ti: 0.01-0.02%, Cr: 0.20-0.40%, Mo: 0.18-0.30%, N: ⁇ 0.006%, 0 ⁇ 0.004%, Ca: 0.0015-0.0050%, Ni ⁇ 0.40%, Among them, Ca / S > 1.5, the balance is iron and inevitable impurities.
  • Si 0.16-0.29%.
  • Mn 1.55-1.83%.
  • N ⁇ 0.0055%, preferably, N: 0.003-0.0045%.
  • P ⁇ 0.008%, S 0.003%.
  • Al 0.02-0.035%.
  • N is 0.25%.
  • Cr 0.24-0.36%.
  • Mo 0.19-0.26%.
  • Nb 0.018-0.024%.
  • Ti 0.012-0.019%.
  • Ca 0.0030-0.0045%.
  • the steel sheet of the present invention is mainly composed of ferrite and tempered bainite and possibly a small amount of martensite.
  • Another object of the present invention is to provide a steel pipe manufactured from the above-described low yield ratio high toughness steel sheet.
  • Still another object of the present invention is to provide a method for producing a medium-thickness steel sheet having a yield strength of 500 MPa or more and a low yield ratio high toughness.
  • the method includes:
  • the method for manufacturing a low yield ratio high toughness steel sheet according to the present invention comprises the following steps:
  • the molten steel is subjected to continuous decasting or die casting after vacuum degassing, and is subjected to preliminary rolling into a slab after molding; the continuous casting billet or billet is heated at 1150-1220 ° C in the austenite recrystallization zone and the non-recrystallization zone. Multi-pass rolling, total reduction rate >80%, finishing temperature >850° ( ;
  • the steel plate After rolling, the steel plate is rapidly cooled to a temperature range of Bs-60 ° C to Bs-100 ° C at a cooling rate of 15-50 ° C / s, and then air-cooled 5-60 s;
  • the cooled steel plate enters the in-line induction furnace and is rapidly heated to Bs+20 at a rate of l-10 °C/s.
  • the bainite starting point Bs is calculated according to the following formula:
  • the reduction ratio in the recrystallization zone is > 65%, and the reduction ratio in the non-recrystallization zone is 63%.
  • the finishing temperature is 850-880 ° C, more preferably 850-860 ° C.
  • the rolled steel sheet is rapidly water-cooled to 510-550 ° C, more preferably 515-540 ° C, at a cooling rate of 15-50 ° C / s.
  • the invention obtains the low yield strength of the microstructure as ferrite + tempered bainite and possibly a small amount of martensite by suitable composition design and heating, rolling and rapid cooling after rolling and rapid heating in the short time tempering process.
  • Steel plate for high toughness pipelines The yield strength of 10-25mm thick steel plate is > 500MPa, the yield ratio is 0.75, and the elongation is A 5 . > 20%, -60 °C ⁇ A kv > 200J, excellent cold bending performance, meeting the high requirements of steel plates for large strain pipelines.
  • the low yield ratio high toughness steel plate of the invention is suitable for steel pipes for resisting large strain pipeline transportation, in particular, steel pipes for large strain pipeline transportation in high earthquake occurrence areas.
  • Fig. 1 is a photograph showing a typical metallographic structure of a 10 mm thick steel plate according to Embodiment 1 of the present invention.
  • Fig. 2 is a photograph showing a typical metallographic structure of a 25 mm thick steel plate according to Example 5 of the present invention. Detailed description of the invention
  • the chemical composition of the steel sheet is controlled as follows:
  • Carbon A key element in ensuring the strength of the steel.
  • the carbon content of steel for pipelines is less than 0.11%. Carbon improves the strength of the steel sheet by solid solution and precipitation strengthening, but carbon has obvious harmful effects on the toughness, plasticity and weldability of the steel. Therefore, the development of pipeline steel is always accompanied by a continuous decrease in carbon content.
  • the carbon content is generally less than 0.08%.
  • the present invention uses a lower carbon content of 0.05-0.08%.
  • 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 scale removal 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 effects of various aspects of silicon, the silicon content of the present invention is 0.15-0.30%, preferably Si: 0.16-0.29%.
  • Manganese In order to compensate for the loss of strength due to the reduction in carbon content, increasing the manganese content is the cheapest and straightforward method. 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 content of manganese in the present invention should be controlled to be 1.55 to 1.85%, preferably, Mn: 1.55-1.83%.
  • Nitrogen In pipeline steel, nitrogen is mainly combined with niobium to form tantalum nitride or niobium carbonitride. In order to exert the effect of inhibiting recrystallization of rhodium, it is desirable to inhibit recrystallization in a solid solution state during rolling, so that it is generally required to add no excessive nitrogen in the pipeline steel, so that the billet is at a normal heating temperature (about 1200 ° C). The carbonitride of cerium can be mostly dissolved.
  • the nitrogen content of the general pipeline steel does not exceed 60 ppm, preferably does not exceed 0.0055%, and more preferably 0.003-0.0045%.
  • Sulfur and phosphorus Sulfur is combined with manganese in steel to form a plastic inclusion manganese sulfide, especially for the transverse plasticity and toughness of steel. Therefore, 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 inevitable impurity elements and should be as low as possible. Considering the actual steelmaking level of the steel mill, the present invention requires P 0.015%, S ⁇ 0.005%, preferably, P 0.008 %, S 0.003%.
  • Aluminum is a strong deoxidizing element in the present invention. In order to ensure that the oxygen content in the steel is as low as possible, the aluminum content is controlled to be 0.015 - 0.04%.
  • 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.
  • ⁇ It can significantly increase the recrystallization temperature of steel and refine grains.
  • the strain-induced precipitation of niobium during hot rolling can hinder the recovery and recrystallization of deformed austenite, and the deformation after controlled rolling and controlled cooling gives a small phase transformation product.
  • Modern pipeline steel bismuth content is generally greater than 0.02%, TMCP pipeline steel generally has a higher yield ratio and anisotropy.
  • the crucible in order to obtain a steel with high strain-to-strength resistance for large strain pipelines, the crucible uses a lower niobium content, and the strength loss caused by the reduction of niobium is compensated by Mn, Cr, Mo, and through rapid cooling and on-line rapid tempering process.
  • the precipitation of fine carbides increases the precipitation strengthening effect. Therefore, the content of ruthenium in the present invention is controlled to be 0.015 to 0.025%, preferably Nb: 0.018 to 0.024%.
  • 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 coarsened when the billet is heated, and refine the original austenite grains. degree. Titanium can also be combined with carbon and sulfur in steel to form TiC, TiS, Ti 4 C 2 S 2 , etc. They exist 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. In the present invention, the titanium content is controlled at
  • 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. The fine carbide precipitation in combination with the on-line rapid induction heating tempering technique can reduce the alloy content of Nb accordingly, so the present invention can add 0.20-0.40% of chromium, preferably 0.24-0.36%.
  • 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 0.18-0.30% of molybdenum is added in the present invention, preferably 0.19 to 0.26%.
  • Nickel Stabilizing austenite elements has no significant effect on strength.
  • the addition of nickel to steel, especially nickel in quenched and tempered steel, can greatly improve the toughness of steel, especially low temperature toughness.
  • the present invention can selectively add not more than 0.40% of nickel element, preferably not exceeding 0.25%.
  • the calcium treatment of the pipeline steel of the present invention mainly changes the sulfide form and improves the thickness, transverse properties and cold bending properties of the steel. For steels with very low sulfur content, it is also not treated with calcium.
  • the calcium content of the present invention depends on the sulfur content, and the control ⁇ & / 8 ratio is > 1.5, Ca: 0.0015 - 0.0050%, more preferably Ca: 0.0030 - 0.0045%.
  • the above-mentioned steel sheet for low yield ratio high toughness pipeline is manufactured according to the following process:
  • 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.
  • Continuous casting or die casting Ensure that the internal components of the slab are well-joined and the surface quality is good.
  • the molded steel ingot needs to be rolled into a slab.
  • Heating and rolling The continuous casting billet or billet is heated at a temperature of 1150-1220 °C to obtain a homogenous austenitic structure on the one hand, and a compound part of an alloying element such as tantalum, titanium, chromium or molybdenum on the other hand. Dissolved. Multi-pass rolling in austenite recrystallization zone and non-recrystallization zone, recrystallization zone reduction rate > 65%, non-recrystallization zone reduction rate 63%, total reduction ratio > 80%, finishing temperature > 850 °C, preferably 850-880 °C;
  • Rapid cooling After rolling, the steel plate is rapidly water-cooled to a temperature range of Bs-60°C to Bs-100°C at a cooling rate of 15-50 ° C / s, air cooling for 5-60 s; during the rapid cooling process, most of the alloying elements It is solidified into martensite.
  • the cooled steel plate enters the in-line induction furnace and is rapidly heated to Bs+20°C at a rate of 1 -10 °C / s, tempered for 40-60 seconds, and then air-cooled. Tempering helps to eliminate the strengthening of the steel sheet during rapid cooling and improve the strong molding, toughness and cold bending properties.
  • the ultra-fast cold and fast online tempering process can effectively reduce the yield ratio and anisotropy of pipeline steel.
  • the online heat treatment (tempering) process is mainly to improve the performance of the steel sheet originally produced by the TMCP process, especially to solve the problem that the microalloyed steel is not recrystallized and rolled.
  • the anisotropy and yield ratio are too high, which creates conditions for the production of highly deformable pipeline steels and high-strength construction steels with low yield ratios and steel sheets requiring high performance.
  • the invention realizes the precise control of the microstructure type of the steel plate by the interval control of the cooling final cooling temperature and the short-time tempering and temperature selection of the on-line rapid induction heating, thereby obtaining a lower yield ratio; and the internal carbide of the steel plate Fine dispersion and precipitation, a good match between strength and toughness is obtained.
  • the invention obtains microstructure as ferrite (F) + bainite (B) and possibly a small amount of martensite by suitable composition design and heating, rolling and rapid cooling after rolling and rapid heating in the short time tempering process.
  • (MA) Low toughness ratio steel plate for high toughness pipelines. 10-25mm thick steel plate yield strength> 500MPa, yield ratio 0.75, elongation A 5Q >20%, -60°C A kv >200J, excellent cold bending performance, meeting the higher requirements of steel plates for large strain pipelines .
  • 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 10mm the total reduction rate is 88%, the final rolling temperature is 860 °C, then water cooled to 535 °C at 35 °C / s, and then quickly heated to 640 ° C online. Tempering, then air cooling to room temperature;
  • FIG. 1 is a view showing the metallographic structure of a 10 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 ferrite and tempered bainite and a small amount of martensite.
  • Other embodiments can also obtain similar metallographic texture maps.
  • the steel sheets obtained by the composition design, heating and rolling process, rapid cooling and on-line rapid heating and tempering process of the present invention achieve fine grain strengthening, phase transformation strengthening, precipitation strengthening, and improvement.
  • the strength and hardness of the steel plate have high low temperature toughness, especially for the steel plate to obtain a lower yield ratio, the microstructure appears as ferrite and tempered bainite and possibly a small amount of martensite and dispersed carbide reinforcement. .
  • the longitudinal and transverse yield strength of the 10-25mm thick steel plate is > 500MPa, the yield ratio is 0.75, and the elongation is A 5 . > 20%, -60 °C A kv > 200J, excellent cold bending performance, meeting the requirements for steel for large strain pipeline transportation.
  • Table 1 it can be seen from Table 1 that the steel of the present invention has a lower Ceq and a lower Pcm value, indicating that the steel sheet of the present invention has better weldability and crack resistance resistance.

Abstract

一种低屈强比高韧性钢板，钢板化学成分的重量百分比为：C：0.05-0.08%，Si：0.15-0.30%，Mn：1.55-1.85%，P≤0.015%，S≤0.005%，Al：0.015-0.04%，Nb：0.015-0.025%，Ti：0.01-0.02%，Cr：0.20-0.40%，Mo：0.18-0.30%，N：≤0.006%，O≤0.004%，Ca：0.0015-0.0050%，Ni≤0.40%，其中，Ca/S≥1.5，余量为铁和不可避免杂质。

Description

一种低屈强比高韧性钢板及其制造方法 发明领域
本发明涉及一种高韧性热轧钢板及其制造方法，具体地涉及一种屈服 强度 500MPa级、 低屈强比高韧性钢板及其制造方法。 本发明钢板具有较 低的屈强比， 以此钢板制造的输送用管线适合用于地震高发区， 可以抵抗 较大变形。 背景技术
传统油气管线输送用钢较多釆用 Nb合金化和控轧， 导致管线用钢的 屈强比较高， 通常大于等于 0.85 , 此类管线钢不适合制作用于地震多发区 的输送管线。
CN101962733A公开了一种低成本、高强韧的 X80级抗大变形管线钢 及其生产方法，其中 C: 0.02-0.08%, Si < 0.40%, Mn: 1.2-2.0%, P < 0.015%, S < 0.004%, Cu < 0.40%, Ni < 0.30%, Mo: 0.10-0.30%, Nb: 0.03-0.08%, Ti: 0.005-0.03%, 其生产工艺釆用 1200-1250 °C均热， 再结晶区的终轧温 度 1000-1050 °C , 精轧开轧温度 880-950 °C , 终轧温度 780-850 °C , 两阶段 空冷 l-3 °C /s至 Ar3以下 20-80 °C获得 20-40%铁素体， 以 15-30 °C/s层流冷 却至 250-450 °C , 获得铁素体（20-40% ) +贝氏体 +马氏体（ 1-3% ) , 屈服 强度为 530-630MPa, 抗拉强度为 660-800MPa, uEL > 10%, 屈强比 0.80 的钢板。 其屈强比和延伸率等性能还不能满足地震高发区， 可以抵抗较大 变形的输送用管线的要求。
目前仍需要一种低屈强比高韧性钢板， 以制造适合用于地震高发区， 可以抵抗较大变形的输送用管线。 发明概述
本发明的目的在于提供一种屈服强度在 500MPa以上的低屈强比高韧 性管线用钢板， 特别是厚度为 10-25mm的钢板。 这种钢可用于地震高发 区以及抗大应变输送管线用钢管。
为实现上述目的， 本发明的屈服强度在 500MPa以上低屈强比高韧性 钢板， 其化学成分的重量白分比为： C: 0.05-0.08%, Si: 0.15-0.30%, Mn: 1.55-1.85%, P < 0.015%, S 0.005%, Al: 0.015-0.04%, Nb : 0.015-0.025%, Ti: 0.01-0.02%, Cr: 0.20-0.40%, Mo: 0.18-0.30%, N: < 0.006%, 0< 0.004%, Ca: 0.0015-0.0050%, Ni<0.40%, 其中， Ca/S >1.5, 余量为铁和不可避免杂质。
优选地， Si: 0.16-0.29%。
优选地， Mn: 1.55-1.83%。
优选地， N< 0.0055%, 优选地， N: 0.003-0.0045%。
优选地， P< 0.008%, S 0.003%。
优选地， Al: 0.02-0.035%。
优选地， N 0.25%。
优选地， Cr: 0.24-0.36%。
优选地， Mo: 0.19-0.26%。
优选地， Nb: 0.018-0.024%。
优选地， Ti: 0.012-0.019%。
优选地， Ca: 0.0030-0.0045%。
本发明中， 除非另有指明， 含量均为重量百分比含量。
本发明的所述钢板的组织主要为铁素体和回火贝氏体以及可能的少 量马氏体。
本发明的另一个目的是提供一种由上述低屈强比高韧性钢板制造的 钢管。
本发明的又一目的在于提供所述屈服强度在 500MPa以上、低屈强比 高韧性中厚钢板的制造方法。 该方法包括：
本发明所述低屈强比高韧性钢板的制造方法包括以下步骤：
钢水经真空脱气处理后进行连铸或模铸， 模铸后需经初轧成钢坯； 连铸坯或钢坯于 1150- 1220 °C加热后在奥氏体再结晶区和未再结晶区 进行多道次轧制， 总压下率>80%, 终轧温度> 850°( ；
轧后钢板以 15-50°C/s的冷却速度， 快速水冷至 Bs-60°C至 Bs-100°C 温度区间， 再空冷 5-60s;
冷却的钢板进入在线感应加热炉以 l-10°C/s的速度快速加热至 Bs+20
°C, 回火 40-60s, 然后出炉空冷。 根据本发明， 贝氏体开始点 Bs按照以下公式计算：
Bs = 830-270C-90Mn-37Ni-70Cr-83Mo„
优选地， 多道次轧制中， 再结晶区压下率> 65%, 未再结晶区压下率 63%。
优选地， 终轧温度为 850-880 °C , 更优选为 850-860 °C。
优选地， 轧后钢板以 15-50 °C/s的冷却速度， 快速水冷至 510-550 °C , 更优选为 515-540 °C。
本发明通过合适的成分设计和加热、轧制及轧后快速冷却和在线快速 加热短时间回火工艺， 获得组织为铁素体 +回火贝氏体以及可能的少量马 氏体的低屈强比高韧性管线用钢板。 10-25mm厚钢板屈服强度> 500MPa, 屈强比 0.75 , 延伸率 A5。> 20%, -60 °C^々Akv > 200J, 冷弯性能优良， 满 足抗大应变管线用钢板的较高要求。 本发明的低屈强比高韧性钢板， 适合 用于抗大应变管线输送用钢管，特别是地震高发区的抗大应变管线输送用 钢管。 附图说明
图 1是本发明实施例 1的 10mm厚钢板的典型金相组织照片。
图 2是本发明实施例 5的 25mm厚钢板的典型金相组织照片。 发明的详细说明
下面， 通过结合实施例对本发明的特点和性质进行较为详细的说明。 为了实现本发明的提供一种屈服强度在 500MPa以上的低屈强比高韧 性管线用钢板的目的， 对钢板的化学成分进行如下控制：
碳： 确保钢板强度的关键元素。 一般管线用钢碳含量小于 0.11%。 碳 通过固溶和析出强化来提高钢板强度， 但碳对钢的韧性、 塑性和焊接性有 明显的害处， 因此管线钢的发展总是伴随着碳含量的不断降低。 对于韧性 要求较高的管线用钢， 一般碳含量低于 0.08%。 为了获得较高的低温冲击 韧性， 本发明釆用较低的碳含量 0.05-0.08%。
硅： 钢中加硅能提高钢质纯净度和脱氧。 硅在钢中起固溶强化作用。 但硅含量过高会使钢板加热时的氧化皮粘度较大， 出炉后除鳞困难， 导致 轧后钢板表面红色氧化皮严重， 表面质量较差。 且高硅不利于焊接性能。 综合考虑硅各方面的影响， 本发明硅含量 0.15-0.30% , 优选地， Si : 0.16-0.29%。
锰： 为了补偿碳含量的降低导致的强度损失， 提高锰含量是最廉价直 接的办法。 但锰具有较高的偏析倾向， 所以其含量不能太高， 一般低碳微 合金钢中锰含量不超过 2.0%。 锰的加入量主要取决于钢的强度级别。 本 发明锰的含量应控制在 1.55-1.85%, 优选地， Mn: 1.55-1.83%。
氮： 在管线钢中氮主要与铌复合形成氮化铌或碳氮化铌析出强化。 为 了发挥铌的抑制再结晶的作用， 希望在轧制时铌以固溶形态抑制再结晶， 故管线钢中一般要求不添加过多的氮， 使得钢坯在常规加热温度下（ 1200 °C左右）铌的碳氮化物能大部分溶解。一般管线钢中氮含量不超过 60ppm, 优选不超过 0.0055%, 更优选为 0.003-0.0045%。
硫和磷： 硫在钢中与锰等化合形成塑性夹杂物硫化锰， 尤其对钢的横 向塑性和韧性不利，因此硫的含量应尽可能地低。磷也是钢中的有害元素， 严重损害钢板的塑性和韧性。 对于本发明而言， 硫和磷均是不可避免的杂 质元素， 应该越低越好， 考虑到钢厂实际的炼钢水平， 本发明要求 P 0.015%、 S < 0.005%, 优选地， P 0.008%、 S 0.003%。
铝： 本发明中铝作为强脱氧元素。 为了保证钢中的氧含量尽量地低， 铝的含量控制在 0.015 - 0.04 %。脱氧后多余的铝和钢中的氮元素能形成 A1N 析出物， 提高强度并且在热处理加热时能细化钢的元素奥氏体晶粒度。 优 选地， A1: 0.02-0.035%。
铌： 能显著提高钢的再结晶温度和细化晶粒。 热轧过程中铌的碳化物 应变诱导析出能阻碍形变奥氏体的回复和再结晶，经控轧和控冷后的形变 奥氏体组织得到细小的相变产物。 现代管线钢铌含量一般大于 0.02%, TMCP管线钢一般具有较高的屈强比和各向异性。本发明中为了得到低屈 强比的抗大应变管线用钢， 釆用较低的铌含量， 铌减少引起的强度损失由 Mn、 Cr、 Mo来补偿， 并通过快速冷却和在线快速回火工艺析出弥散细小 的碳化物增加析出强化效果。因此，本发明中铌含量控制在 0.015-0.025%, 优选 Nb: 0.018-0.024%。
钛： 钛是强碳化物形成元素， 钢中加入微量的 Ti有利于固定钢中的 N, 形成的 TiN能使钢坯加热时奥氏体晶粒不过分粗化， 细化原始奥氏体 晶粒度。 钛在钢中还可分别与碳和硫化合， 生成 TiC、 TiS、 Ti4C2S2等， 它们以夹杂物和第二相粒子的形式存在。钛的这些碳氮化物析出物在焊接 时还可阻止热影响区晶粒长大， 改善焊接性能。 本发明中钛含量控制在
0.01-0.02%, 优选地， Ti: 0.012-0.019%。
铬： 铬提高钢的淬透性， 增加钢的回火稳定性。 铬在奥氏体中溶解度 很大， 稳定奥氏体， 淬火后在马氏体中大量固溶， 并在随后的回火过程中 会析出 Cr23C7、 Cr7C3等碳化物， 提高钢的强度和硬度。 为了保持钢的强 度级别， 铬可以部分代替锰， 减弱高锰的偏析倾向。 配合在线快速感应加 热回火技术的细小碳化物析出， 可相应降低 Nb的合金含量， 故本发明可 添加 0.20-0.40%的铬, 优选 0.24-0.36%。
钼：钼能显著地细化晶粒，提高强度和韧性。钼能减少钢的回火脆性， 同时回火时还能析出非常细小的碳化物， 显著强化钢的基体。 由于钼是非 常昂贵的战略合金元素， 所以本发明中仅添加 0.18-0.30%的钼， 优选 0.19-0.26%。
镍： 稳定奥氏体的元素， 对提高强度没有明显的作用。 钢中加镍尤其 是在调质钢中加镍能大幅提高钢的韧性尤其是低温韧性，同时由于镍属于 贵重合金元素， 所以本发明可选择性添加不超过 0.40%的镍元素， 优选不 超过 0.25%。
钙： 本发明的管线钢进行钙处理主要是改变硫化物形态， 改善钢的厚 向、 横向性能和冷弯性能。 对于硫含量很低的钢亦可不进行钙处理。 本发 明钙含量的高低视硫含量而定， 控制〇&/8比> 1.5 , Ca: 0.0015-0.0050%, 更优选 Ca: 0.0030-0.0045%。
上述低屈强比高韧性管线用钢板， 按照如下工艺制造：
转炉吹炼和真空处理： 目的是确保钢液的基本成分要求， 去除钢中的 氧、 氢等有害气体， 并加入锰、 钛等必要的合金元素， 进行合金元素的调 整。
连铸或模铸： 保证铸坯内部成分均勾和表面质量良好， 其中模铸的钢 锭需轧制成钢坯。
加热和轧制： 连铸坯或钢坯在 1150-1220 °C的温度下加热， 一方面获 得均勾的奥氏体化组织， 另一方面使铌、 钛、 铬、 钼等合金元素的化合物 部分溶解。 在奥氏体再结晶区和未再结晶区进行多道次轧制， 再结晶区压 下率 > 65%, 未再结晶区压下率 63%, 总压下率> 80%, 终轧温度> 850 °C, 优选为 850-880 °C;
快速冷却： 轧后钢板以 15-50°C/s的冷却速度快速水冷至 Bs-60°C至 Bs-100°C温度区间， 空冷 5-60s; 在快速冷却过程中， 大部分的合金元素 被固溶到马氏体中。
在线回火：冷却的钢板进入在线感应加热炉以 1 -10 °C /s的速度快速加 热至 Bs+20°C, 回火 40-60s, 然后出炉空冷。 回火有助于消除快冷时钢板 物强化， 提高强塑型、 韧性和冷弯性能。
超快冷和快速在线回火工艺可以有效降低管线钢的屈强比和各向异 性。 在线热处理（回火）工艺除了可以缩短工艺流程， 节省能源外， 更主 要的是使原先用 TMCP 工艺生产的钢板性能得到充分的提高， 特别是解 决了微合金钢由于未再结晶轧制导致的各向异性和屈强比过高的弊病，从 而为生产可大变形的管线钢和低屈强比的高强度建筑用钢以及要求高性 能的钢板创造了条件。
本发明通过对冷却终冷温度的区间控制以及在线的快速感应加热短 时间回火及温度的适当选择， 使得钢板的组织类型得到精确控制， 因而获 得较低的屈强比； 并且钢板内部碳化物细小弥散析出， 获得了强度与韧性 的良好匹配。
本发明通过合适的成分设计和加热、轧制及轧后快速冷却和在线快速 加热短时间回火工艺， 获得组织为铁素体（F) +贝氏体（B) 以及可能的 少量马氏体（MA) 的低屈强比高韧性管线用钢板。 10-25mm厚钢板屈服 强度 > 500MPa, 屈强比 0.75, 延伸率 A5Q>20%, -60°C的 Akv >200J, 冷弯性能优良， 满足了抗大应变管线用钢板的较高要求。 实施例
实施例 1
将按表 1配比冶炼完成的钢水经真空脱气处理后进行连铸或模铸，板 坯厚度 80mm, 所得坯料于 1200°C加热后， 在奥氏体再结晶温度范围内经 多道次轧制， 轧制成厚度为 10mm的钢板， 总压下率为 88%, 终轧温度为 860 °C, 然后以 35°C/s的速度水冷至 535°C, 再在线快速加热至 640°C回 火， 然后空冷至室温； 实施例 2-5的详细成分见表 1 ,工艺过程如实施例 1 ,工艺参数见表 2。 表 1 本发明实施例 1-5的化学成分、 Ceq ( wt% ) 、 Pcm
Figure imgf000009_0001
* Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/14
* * Pcm=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/l 0+5B 表 2 本发明实施例 1-5的工艺参数及钢板厚度
Figure imgf000009_0002
试验例 1 : 力学性能
按照 GB/T228-2002金属材料室温拉伸试验方法、 GB 2106-1980金属 夏比 V型缺口冲击试险方法， GB/T 8363-2007落锤撕裂试验标准测定本 发明实施例 1-5钢板的各项力学性能， 其结果见表 3。
表 3本发明实施例钢板的力学性能
实施 Rto Rm 屈强 A50 Ecvn SA%— i yc 例 /MPa /MPa 比 /% 冲击值 /J SA% 50%FATT DWTT
1 535 760 0.70 21 21 1 100 <-60°C 100
2 553 785 0.71 24.8 240 100 <-60°C 100 3 580 795 0.73 26 235 100 <-60 °C 100
4 583 800 0.73 25.8 205 100 <-60 °C 100
5 575 805 0.71 28 221 100 <-60 °C 100
Ecvn-60r： -60 °C夏比 V型缺口试样冲击功
SA0/0-i5r： -15 °C DWTT断裂试样断口剪切面积
DWTT: 落锤撕裂试验
50%FATT: 50%韧脆转变温度 试验例 2: 弯曲性能
按照 GB/T 232-2010金属材料弯曲试验方法， 对本发明实施例 1-5钢 板进行横向冷弯 d=2a,180° 试验， 其结果全部实施例钢板完好， 均无表面 裂紋。 试马全例 3 : 金相组织
图 1是本发明实施例 1的 10mm厚钢板的金相组织图。
图 2是本发明实施例 5的 25mm厚钢板的金相组织图。
从图中可见， 钢板的组织为铁素体和回火贝氏体以及少量的马氏体。 其他实施例也能得到类似的金相组织图。 从以上实施例结果可以看出， 釆用本发明的成分设计、加热和轧制工 艺、 快冷及在线的快速加热回火工艺得到的钢板实现了细晶强化、相变强 化、 析出强化， 提高了钢板的强度、 硬度， 具有很高的低温韧性， 尤其是 使钢板获得较低的屈强比，组织呈现为铁素体和回火贝氏体以及可能的少 量马氏体和弥散碳化物强化。 10-25mm厚钢板的纵向、 横向屈服强度 > 500MPa, 屈强比 0.75 , 延伸率 A5。> 20%, -60 °C的 Akv > 200J, 冷弯性 能优良， 满足了抗大应变管线输送用钢要求。 另外， 从表 1中可见本发明 钢的 Ceq较低以及 Pcm值较低， 说明本发明钢板的焊接性和抗裂紋敏感 性能比较好。

Claims

权 利 要 求 书
1. 一种低屈强比高韧性钢板， 其化学成分的重量百分比为： C : 0.05-0.08%, Si: 0.15-0.30%, Mn: 1.55-1.85%, P < 0.015%, S < 0.005%, Al: 0.015-0.04%, Nb: 0.015-0.025%, Ti: 0.01-0.02%, Cr: 0.20-0.40%, Mo: 0.18-0.30% , N: < 0.006%, 0 < 0.004% , Ca: 0.0015-0.0050%, Ni 0.40%, 其中， Ca/S > 1.5 , 余量为铁和不可避免杂质。
2. 如权利要求 1 所述的低屈强比高韧性钢板， 其特征在于， Si: 0.16-0.29%。
3. 如权利要求 1或 2所述的低屈强比高韧性钢板，其特征在于， Mn:
1.55-1.83%。
4.如权利要求 1-3任一所述的低屈强比高韧性钢板，其特征在于， N < 0.0055%, 优选地， N: 0.003-0.0045%。
5. 如权利要求 1-4任一所述的低屈强比高韧性钢板， 其特征在于， P < 0.008%, S 0.003%。
6. 如权利要求 1-5任一所述的低屈强比高韧性钢板， 其特征在于， A1: 0.02-0.035%。
7. 如权利要求 1-6任一所述的低屈强比高韧性钢板， 其特征在于， Ni < 0.25%。
8. 如权利要求 1-7任一所述的低屈强比高韧性钢板， 其特征在于，
Cr: 0.24-0.36%。
9. 如权利要求 1-8任一所述的低屈强比高韧性钢板， 其特征在于， Mo: 0.19-0.26%。
10. 如权利要求 1-9任一所述的低屈强比高韧性钢板， 其特征在于， Nb: 0.018-0.024%。
11. 如权利要求 1-10任一所述的低屈强比高韧性钢板， 其特征在于， Ti: 0.012-0.019%。
12. 如权利要求 1-11任一所述的低屈强比高韧性钢板， 其特征在于， Ca: 0.0030-0.0045%。
13. 如权利要求 1-11 任一所述的低屈强比高韧性钢板， 其组织主要 为铁素体和回火贝氏体以及可能的少量马氏体。
14. 如权利要求 1-13 任一所述的低屈强比高韧性钢板， 厚度为 10-25mm, 屈服强度> 500MPa, 屈强比 0.75, 延伸率 A5Q>20%, -60 °C 的 Akv>200J。
15. 如权利要求 1-14任一所述的低屈强比高韧性钢板的制造方法， 包括：
钢水经真空脱气处理后进行连铸或模铸， 模铸后需经初轧成钢坯； 连铸坯或钢坯于 1150- 1220 °C加热后在奥氏体再结晶区和未再结晶区 进行多道次轧制， 总压下率>80%, 终轧温度> 850°( ；
轧后钢板以 15-50°C/s的冷却速度， 快速水冷至 Bs-60°C至 Bs-100°C 温度， 再空冷 5-60s;
冷却的钢板进入在线感应加热炉以 l-10°C/s的速度快速加热至 Bs+20 °C, 回火 40-60s, 然后出炉空冷；
其中贝氏体开始点 Bs为: Bs = 830-270C-90Mn-37Ni-70Cr-83Mo„
16. 如权利要求 15所述的方法， 其特征在于， 多道次轧制中， 再结 晶区压下率 > 65%, 未再结晶区压下率 63%。
17.如权利要求 15或 16所述的方法，其特征在于，终轧温度为 850-880
°C。
18.如权利要求 15-17任一所述的方法，其特征在于，轧后钢板以 15-50 °C/s的冷却速度， 快速水冷至 510-550°C。
PCT/CN2012/076049 2011-09-26 2012-05-25 一种低屈强比高韧性钢板及其制造方法 WO2013044640A1 (zh)

Priority Applications (7)

Application Number Priority Date Filing Date Title
US14/129,052 US9683275B2 (en) 2011-09-26 2012-05-25 Steel plate with low yield-tensile ratio and high toughness and method of manufacturing the same
JP2014513889A JP5750546B2 (ja) 2011-09-26 2012-05-25 低降伏比高靭性鋼板及びその製造方法
ES12836145.8T ES2670008T3 (es) 2011-09-26 2012-05-25 Chapa de acero con una baja razón de fluencia-tracción y alta tenacidad y método de fabricación de la misma
BR112013033257-3A BR112013033257B1 (pt) 2011-09-26 2012-05-25 Placa de aço com razão elástica baixa e tenacidade alta, e seu método de fabricação
KR1020137035012A KR20140017001A (ko) 2011-09-26 2012-05-25 낮은 항복 인장 비 및 고인성을 갖는 강판 및 이의 제조 방법
EP12836145.8A EP2762598B1 (en) 2011-09-26 2012-05-25 Steel plate with low yield ratio high toughness and manufacturing method thereof
RU2014109120/02A RU2588755C2 (ru) 2011-09-26 2012-05-25 Стальная полоса с низким отношением предела текучести к пределу прочности и высокой ударной вязкостью и способ ее производства

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201110287965.X 2011-09-26
CN201110287965.XA CN103014554B (zh) 2011-09-26 2011-09-26 一种低屈强比高韧性钢板及其制造方法

Publications (1)

Publication Number Publication Date
WO2013044640A1 true WO2013044640A1 (zh) 2013-04-04

Family

ID=47963664

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2012/076049 WO2013044640A1 (zh) 2011-09-26 2012-05-25 一种低屈强比高韧性钢板及其制造方法

Country Status (9)

Country Link
US (1) US9683275B2 (zh)
EP (1) EP2762598B1 (zh)
JP (1) JP5750546B2 (zh)
KR (1) KR20140017001A (zh)
CN (1) CN103014554B (zh)
BR (1) BR112013033257B1 (zh)
ES (1) ES2670008T3 (zh)
RU (1) RU2588755C2 (zh)
WO (1) WO2013044640A1 (zh)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2015183279A (ja) * 2014-03-26 2015-10-22 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れる船舶用、海洋構造物用および水圧鉄管用厚鋼板およびその製造方法
CN115584436A (zh) * 2022-09-26 2023-01-10 武汉钢铁有限公司 一种经济型氢气输送管线钢及生产方法

Families Citing this family (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013061652A1 (ja) * 2011-10-25 2013-05-02 新日鐵住金株式会社 鋼板
CN103215504B (zh) * 2013-05-13 2015-02-18 湖南华菱湘潭钢铁有限公司 一种易成型高强度中厚钢板的生产方法
CN103215501B (zh) * 2013-05-13 2015-02-18 湖南华菱湘潭钢铁有限公司 一种易成型高强度中厚钢板的生产方法
CN103215502B (zh) * 2013-05-13 2015-02-18 湖南华菱湘潭钢铁有限公司 一种易成型高强度中厚钢板的生产方法
CN103215503B (zh) * 2013-05-13 2015-02-18 湖南华菱湘潭钢铁有限公司 一种易成型高强度中厚钢板的生产方法
CN103320692B (zh) * 2013-06-19 2016-07-06 宝山钢铁股份有限公司 超高韧性、优良焊接性ht550钢板及其制造方法
CN103343300B (zh) * 2013-07-26 2015-12-09 武汉钢铁(集团)公司 厚度＞26mm及纵向屈服强度≥500MPa的工程用钢及生产方法
US11001905B2 (en) 2015-03-26 2021-05-11 Jfe Steel Corporation Steel plate for structural pipes or tubes, method of producing steel plate for structural pipes or tubes, and structural pipes and tubes
CN106319387B (zh) * 2015-06-16 2018-08-31 鞍钢股份有限公司 一种x80抗大变形管线钢及制造方法
EP3375900A4 (en) * 2016-03-22 2019-07-17 Nippon Steel Corporation ELECTRIC RESISTANT WELDED STEEL TUBE FOR A TUBE
JP6969125B2 (ja) * 2017-03-22 2021-11-24 セイコーエプソン株式会社 用紙搬送装置、及び、印刷装置
CN108624810B (zh) * 2017-06-26 2020-06-23 宝山钢铁股份有限公司 一种低成本高强度高抗硫油井管及其制造方法
RU2688077C1 (ru) * 2018-08-17 2019-05-17 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Способ производства низколегированного хладостойкого листового проката
RU2690398C1 (ru) * 2018-08-17 2019-06-03 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Способ производства низколегированного хладостойкого свариваемого листового проката
CN109055864B (zh) * 2018-10-08 2019-09-20 鞍钢股份有限公司 高强韧性低屈强比热煨弯管用宽厚钢板及其生产方法
CN110284066B (zh) * 2019-07-24 2021-04-16 宝钢湛江钢铁有限公司 一种薄规格低屈强比管线钢及其制造方法
CN110453157A (zh) * 2019-08-01 2019-11-15 江阴兴澄特种钢铁有限公司 一种低屈强比薄规格管线钢的制造方法
CN111748737B (zh) * 2020-06-28 2021-10-22 武汉钢铁有限公司 一种冷裂纹敏感系数≤0.25的易焊接超高强钢及生产方法
CN113106346B (zh) * 2021-04-12 2022-03-01 达力普石油专用管有限公司 一种高强度无缝管线管及其制备方法
CN114411053B (zh) * 2021-12-29 2022-12-20 日钢营口中板有限公司 一种高效低成本抗大变形x70m管线钢板及其制造方法
CN114892102B (zh) * 2022-05-28 2023-08-15 日钢营口中板有限公司 一种经济型大厚度管件用钢板及其制造方法
CN115261581B (zh) * 2022-07-26 2023-10-20 张家港宏昌钢板有限公司 非调质高强度钢板及其生产方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005036295A (ja) * 2003-07-17 2005-02-10 Kobe Steel Ltd 耐ガス切断割れ性および大入熱溶接継手靭性に優れ且つ音響異方性の小さい低降伏比高張力鋼板
WO2009048838A1 (en) * 2007-10-10 2009-04-16 Nucor Corporation Complex metallographic structured steel and method of manufacturing same
CN101962733A (zh) 2010-10-29 2011-02-02 北京科技大学 一种低成本、高强韧x80抗大变形管线钢及生产方法
CN101985725A (zh) * 2010-11-27 2011-03-16 东北大学 一种780MPa级低屈强比建筑用钢板及其制造方法
CN102021494A (zh) * 2009-09-23 2011-04-20 宝山钢铁股份有限公司 一种耐候厚钢板及其制造方法

Family Cites Families (36)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS57134514A (en) 1981-02-12 1982-08-19 Kawasaki Steel Corp Production of high-tensile steel of superior low- temperature toughness and weldability
JP2913426B2 (ja) 1991-03-13 1999-06-28 新日本製鐵株式会社 低温靱性の優れた厚肉高張力鋼板の製造法
JPH0995731A (ja) * 1995-10-02 1997-04-08 Nkk Corp 低温用建築向け鋼材の製造方法
JP3371699B2 (ja) * 1996-07-22 2003-01-27 日本鋼管株式会社 耐火性に優れた耐震性建築鋼材の製造方法
BR9811051A (pt) 1997-07-28 2000-08-15 Exxonmobil Upstream Res Co Placa de aço, e, processo para preparar a mesma
JPH1180832A (ja) 1997-09-09 1999-03-26 Nippon Steel Corp 溶接性および低温靭性の優れた低降伏比高張力鋼の製造方法
JP3375554B2 (ja) * 1998-11-13 2003-02-10 川崎製鉄株式会社 強度一延性バランスに優れた鋼管
TNSN99233A1 (fr) 1998-12-19 2001-12-31 Exxon Production Research Co Aciers de haute resistance avec excellente tenacite de temperature cryogenique
JP2003193188A (ja) * 2001-12-25 2003-07-09 Jfe Steel Kk 伸びフランジ性に優れた高張力合金化溶融亜鉛めっき冷延鋼板およびその製造方法
JP4305216B2 (ja) * 2004-02-24 2009-07-29 Ｊｆｅスチール株式会社 溶接部の靭性に優れる耐サワー高強度電縫鋼管用熱延鋼板およびその製造方法
CN100494451C (zh) 2005-03-30 2009-06-03 宝山钢铁股份有限公司 屈服强度960MPa以上超高强度钢板及其制造方法
CN100372962C (zh) 2005-03-30 2008-03-05 宝山钢铁股份有限公司 屈服强度1100Mpa以上超高强度钢板及其制造方法
JP4437972B2 (ja) * 2005-04-22 2010-03-24 株式会社神戸製鋼所 音響異方性の少ない母材靭性に優れた厚鋼板およびその製造方法
JP4502950B2 (ja) * 2005-12-28 2010-07-14 株式会社神戸製鋼所 耐食性および疲労亀裂進展抵抗性に優れた船舶用鋼材
JP4977876B2 (ja) * 2007-03-30 2012-07-18 Ｊｆｅスチール株式会社 母材および溶接部靱性に優れた超高強度高変形能溶接鋼管の製造方法
CN101289728B (zh) * 2007-04-20 2010-05-19 宝山钢铁股份有限公司 低屈强比可大线能量焊接高强高韧性钢板及其制造方法
JP5217556B2 (ja) * 2007-08-08 2013-06-19 Ｊｆｅスチール株式会社 耐座屈性能及び溶接熱影響部靭性に優れた低温用高強度鋼管およびその製造方法
KR101018131B1 (ko) * 2007-11-22 2011-02-25 주식회사 포스코 저온인성이 우수한 고강도 저항복비 건설용 강재 및 그제조방법
JP5076959B2 (ja) * 2008-02-22 2012-11-21 Ｊｆｅスチール株式会社 耐延性き裂発生特性に優れる低降伏比高強度鋼板とその製造方法
JP5146051B2 (ja) 2008-03-27 2013-02-20 Ｊｆｅスチール株式会社 靭性および変形能に優れた板厚：２５ｍｍ以上の高強度鋼管用鋼材およびその製造方法
CN101649420B (zh) 2008-08-15 2012-07-04 宝山钢铁股份有限公司 一种高强度高韧性低屈强比钢、钢板及其制造方法
KR101091306B1 (ko) 2008-12-26 2011-12-07 주식회사 포스코 원자로 격납 용기용 고강도 강판 및 그 제조방법
JP5487682B2 (ja) 2009-03-31 2014-05-07 Ｊｆｅスチール株式会社 強度−伸びバランスに優れた高靭性高張力鋼板およびその製造方法
CN101864542B (zh) * 2009-04-16 2011-09-28 上海梅山钢铁股份有限公司 高频电阻直缝焊油井管用钢及其制造方法
KR101313957B1 (ko) 2009-05-27 2013-10-01 신닛테츠스미킨 카부시키카이샤 피로 특성과 연신 및 충돌 특성이 우수한 고강도 강판, 용융 도금 강판, 합금화 용융 도금 강판 및 그들의 제조 방법
BR112012004577A2 (pt) * 2009-09-02 2016-04-05 Nippon Steel Corp chapa de aço para oleoduto de alta resistência e aço para uso em oleoduto de alta resistência com excelente tenacidade a baixa temperatura
JP5353573B2 (ja) 2009-09-03 2013-11-27 新日鐵住金株式会社 成形性及び疲労特性に優れた複合組織鋼板並びにその製造方法
JP5532800B2 (ja) * 2009-09-30 2014-06-25 Ｊｆｅスチール株式会社 耐歪時効特性に優れた低降伏比高強度高一様伸び鋼板及びその製造方法
JP5482205B2 (ja) 2010-01-05 2014-05-07 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法
JP5425702B2 (ja) * 2010-02-05 2014-02-26 株式会社神戸製鋼所 落重特性に優れた高強度厚鋼板
CN101906569B (zh) * 2010-08-30 2013-01-02 南京钢铁股份有限公司 一种热处理方法制备的抗大变形管线钢及其制备方法
CN101985722B (zh) * 2010-09-20 2012-07-25 南京钢铁股份有限公司 低屈强比细晶粒高强管线钢板及其生产方法
JP5533729B2 (ja) * 2011-02-22 2014-06-25 新日鐵住金株式会社 局部変形能に優れ、成形性の方位依存性の少ない延性に優れた高強度熱延鋼板及びその製造方法
JP5158272B2 (ja) * 2011-03-10 2013-03-06 新日鐵住金株式会社 伸びフランジ性と曲げ加工性に優れた高強度鋼板およびその溶鋼の溶製方法
TWI447236B (zh) * 2011-03-28 2014-08-01 Nippon Steel & Sumitomo Metal Corp 熱軋鋼板及其製造方法
KR101587968B1 (ko) * 2011-07-29 2016-01-22 신닛테츠스미킨 카부시키카이샤 합금화 용융 아연 도금층 및 그것을 가진 강판 및 그 제조 방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005036295A (ja) * 2003-07-17 2005-02-10 Kobe Steel Ltd 耐ガス切断割れ性および大入熱溶接継手靭性に優れ且つ音響異方性の小さい低降伏比高張力鋼板
WO2009048838A1 (en) * 2007-10-10 2009-04-16 Nucor Corporation Complex metallographic structured steel and method of manufacturing same
CN102021494A (zh) * 2009-09-23 2011-04-20 宝山钢铁股份有限公司 一种耐候厚钢板及其制造方法
CN101962733A (zh) 2010-10-29 2011-02-02 北京科技大学 一种低成本、高强韧x80抗大变形管线钢及生产方法
CN101985725A (zh) * 2010-11-27 2011-03-16 东北大学 一种780MPa级低屈强比建筑用钢板及其制造方法

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2015183279A (ja) * 2014-03-26 2015-10-22 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れる船舶用、海洋構造物用および水圧鉄管用厚鋼板およびその製造方法
CN115584436A (zh) * 2022-09-26 2023-01-10 武汉钢铁有限公司 一种经济型氢气输送管线钢及生产方法

Also Published As

Publication number Publication date
JP5750546B2 (ja) 2015-07-22
BR112013033257B1 (pt) 2019-06-25
RU2014109120A (ru) 2015-11-10
KR20140017001A (ko) 2014-02-10
JP2014520208A (ja) 2014-08-21
BR112013033257A2 (pt) 2017-03-01
US9683275B2 (en) 2017-06-20
ES2670008T3 (es) 2018-05-29
US20140144556A1 (en) 2014-05-29
CN103014554A (zh) 2013-04-03
EP2762598A1 (en) 2014-08-06
RU2588755C2 (ru) 2016-07-10
CN103014554B (zh) 2014-12-03
EP2762598B1 (en) 2018-04-25
EP2762598A4 (en) 2015-11-11

Similar Documents

Publication Publication Date Title
WO2013044640A1 (zh) 一种低屈强比高韧性钢板及其制造方法
JP6460292B1 (ja) 高Ｍｎ鋼およびその製造方法
JP6048626B1 (ja) 厚肉高靭性高強度鋼板およびその製造方法
JP4946092B2 (ja) 高張力鋼およびその製造方法
WO2014038200A1 (ja) 溶接熱影響部ｃｔｏｄ特性に優れた厚肉高張力鋼およびその製造方法
WO2013044641A1 (zh) 一种屈服强度700MPa级高强度高韧性钢板及其制造方法
CN113549827B (zh) 一种低温韧性优异的fh690级海工钢及其制造方法
KR100843844B1 (ko) 균열성장 저항성이 우수한 초고강도 라인파이프용 강판 및그 제조방법
WO2001057286A1 (fr) Tube en acier sans soudure a haute resistance et endurance pour tuyau de canalisation
JP5692305B2 (ja) 大入熱溶接特性と材質均質性に優れた厚鋼板およびその製造方法
JPWO2020166538A1 (ja) 高Ｍｎ鋼およびその製造方法
CN108474089B (zh) 具有优异的低温韧性和抗氢致开裂性的厚钢板及其制造方法
JP2008075107A (ja) 高強度・高靭性鋼の製造方法
KR20160078624A (ko) 저온인성 및 강도가 우수한 강관용 열연강판 및 그 제조방법
JP7411072B2 (ja) 低温衝撃靭性に優れた高強度極厚物鋼材及びその製造方法
JP4770415B2 (ja) 溶接性に優れた高張力厚鋼板およびその製造方法
CN115572901B (zh) 一种630MPa级高调质稳定性低碳低合金钢板及其制造方法
JP2004124113A (ja) 非水冷型薄手低降伏比高張力鋼およびその製造方法
JP4133175B2 (ja) 靭性に優れた非水冷型薄手低降伏比高張力鋼およびその製造方法
JPWO2019050010A1 (ja) 鋼板およびその製造方法
KR101899736B1 (ko) 저온인성 및 수소유기균열 저항성이 우수한 후판 강재 및 그 제조방법
JP4105990B2 (ja) 大入熱溶接部ｈａｚの低温靭性に優れた高強度溶接構造用鋼とその製造方法
JP2705946B2 (ja) 耐ｓｓｃ性の優れた高張力鋼板の製造法
KR20150002956A (ko) 라인파이프용 후강판 및 그 제조 방법
CN114752724B (zh) 一种低内应力焊接性能优良的750MPa级桥梁钢及其制备方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 12836145

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2014513889

Country of ref document: JP

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 2012836145

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 14129052

Country of ref document: US

ENP Entry into the national phase

Ref document number: 20137035012

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2014109120

Country of ref document: RU

Kind code of ref document: A

REG Reference to national code

Ref country code: BR

Ref legal event code: B01A

Ref document number: 112013033257

Country of ref document: BR

ENP Entry into the national phase

Ref document number: 112013033257

Country of ref document: BR

Kind code of ref document: A2

Effective date: 20131223