WO2016095720A1 - 一种屈服强度800MPa级别高强钢及其生产方法 - Google Patents

一种屈服强度800MPa级别高强钢及其生产方法 Download PDF

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WO2016095720A1
WO2016095720A1 PCT/CN2015/096638 CN2015096638W WO2016095720A1 WO 2016095720 A1 WO2016095720 A1 WO 2016095720A1 CN 2015096638 W CN2015096638 W CN 2015096638W WO 2016095720 A1 WO2016095720 A1 WO 2016095720A1
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steel
mpa
temperature
high strength
rolling
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PCT/CN2015/096638
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French (fr)
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刘刚
杨阿娜
李自刚
宋凤明
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宝山钢铁股份有限公司
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Priority to US15/536,200 priority Critical patent/US10961611B2/en
Priority to EP15869228.5A priority patent/EP3235923B1/en
Priority to JP2017532974A priority patent/JP6466582B2/ja
Publication of WO2016095720A1 publication Critical patent/WO2016095720A1/zh

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Definitions

  • the invention relates to a high strength steel with a yield strength of 800 MPa and a production method thereof.
  • Chinese patent 201210209649.5 discloses a production method of tensile high strength steel plate of 800MPa grade, without adding Ni element, using in-line quenching + tempering process (DQ+T) to obtain tempered martensite + tempered lower bainite structure Its yield strength is only 700MPa.
  • Chinese patent 2011100343384.3 discloses a high-strength steel for 750-880 MPa class and a production method thereof, and adopts TMCP process to take up hot-rolled high-strength steel coil at 560-600 °C.
  • the different proportions of different thickness specifications of 800MPa grade high-strength steel produced by tempered martensite + tempered bainite structure are different, the thickness of the thick gauge is low, and the performance is not suitable.
  • the precipitation-strengthened high-strength steel produced by high-temperature coiling at 560-600 °C is affected by the particle size and quantity of the precipitates.
  • the strength of the strip head, the middle and the tail fluctuate greatly, and cannot meet the impact requirement of -40 °C.
  • the object of the present invention is to provide a high strength steel with a yield strength of 800 MPa and a production method thereof, which are produced by an in-line quenching + tempering process, and the yield strength of the high strength steel is 800 to 950 MPa.
  • the tensile strength is 850-1000 MPa
  • the elongation is >12%
  • the impact energy at -40 °C is >40J.
  • the high-strength steel has a yield strength of 800 to 950 MPa, a tensile strength of 850 to 1000 MPa, an elongation of >12%, and an impact energy of -40 °C of -40 °C.
  • the microstructure of the high strength steel is tempered martensite.
  • C solid solution strengthening, adjusting the strength and plastic toughness of martensite structure
  • Si 0.10% or more of Si can perform a good deoxidation effect, and when Si exceeds 0.30%, red iron sheets are likely to be formed, and when the Si content is high, the toughness of martensitic high-strength steel is likely to be deteriorated. Therefore, the Si content of the present invention ranges from 0.10 to 0.30%.
  • Mn The Mn content is 0.8% or more, and the hardenability of the steel can be improved. When the Mn content exceeds 1.6%, segregation and inclusions such as MnS are likely to occur, and the toughness of the martensitic high-strength steel is deteriorated. Therefore, the Mn content of the present invention ranges from 0.80 to 1.60%.
  • Cr content of 0.2% or more can improve the hardenability of steel, and is advantageous for forming a martensite structure at the time of quenching.
  • Cr will form a carbide of Cr, which has the effect of resisting moderate temperature tempering and softening.
  • the Cr content exceeds 0.70%, and a large spark will occur during welding, which affects the welding quality. Therefore, the Cr content of the present invention ranges from 0.20 to 0.70%.
  • Mo 0.10% or more of Mo element can improve the hardenability of steel, which is beneficial to form a full martensite structure during quenching; at a high temperature of 400 ° C or higher, Mo reacts with C to form compound particles, which has high temperature tempering resistance. Softening and softening of the welded joint. If the Mo content is too high, the carbon equivalent will be increased, the welding performance will be deteriorated, and Mo is a precious metal, which will increase the cost. Therefore, the Mo content of the present invention ranges from 0.10 to 0.40%.
  • the Ni:Ni element has a function of refining the martensite structure and improving the toughness of the steel. If the Ni content is too high, the carbon equivalent is increased, the weldability is deteriorated, and Ni is a precious metal, which increases the cost. Therefore, the Ni content of the present invention ranges from 0 to 0.30%.
  • Nb, Ti and V are microalloying elements, forming nanoscale precipitates with elements such as C and N, inhibiting the growth of austenite grains during heating; Nb can increase the non-recrystallization critical temperature Tnr , enlarge the production window; fine precipitate particles of Ti can improve the welding performance; V reacts with N and C during the tempering process to precipitate nano-scale V(C,N) particles, which can increase the strength of steel; the Nb content range of the present invention It is 0.01 to 0.03%, the Ti content is in the range of 0.01 to 0.03%, and the V content is in the range of 0.01 to 0.05%.
  • B A trace amount of B can improve the hardenability of the steel and increase the strength of the steel. If more than 0.0030% of B is likely to cause segregation, a boron-boron compound is formed, which seriously deteriorates the toughness of the steel. Therefore, the B content of the present invention ranges from 0.0005 to 0.0030%.
  • Al is used as a deoxidizer.
  • the addition of 0.02% or more of Al to the steel can refine the crystal grains and improve the impact toughness.
  • the Al content of the present invention ranges from 0.02 to 0.06%.
  • the Ca content of the present invention ranges from 0.001 to 0.004%.
  • N The present invention requires strict control of the content range of the N element. During the tempering process, more than 0.002% of the N element can react with V and C to form nano-sized V(C,N) particles, which acts as a precipitation strengthening agent, and can also resist the heat-affected zone by precipitation strengthening during the welding process. Softening; when the N content exceeds 0.005%, it tends to cause coarse precipitate particles to form and deteriorate the toughness. Therefore, the N content of the present invention ranges from 0.002 to 0.005%.
  • P, S and O P, S and O as impurity elements affect the plasticity and toughness of the steel.
  • the control range of the four elements of the present invention is P ⁇ 0.02%, S ⁇ 0.01%, and O ⁇ 0.008%.
  • the invention controls 0.7% ⁇ Mo + 0.8Ni + 0.4Cr + 6V ⁇ 1.1%, and is mainly used for ensuring equal-strength matching welding of 800MPa high-strength steel, adjusting strength and low-temperature toughness of the heat affected zone of the welding, and achieving strength with the base steel plate and The best match for low temperature toughness.
  • Mo, Ni and Cr can reduce the critical cooling rate of steel, improve the hardenability of steel and improve the strength of welded joints; Mo reacts with C to form compounds at high temperature, which has the effect of resisting the softening of welded joints; Mo and Ni elements have fine structure and improve toughness; V and N react to form nano-scale V(C,N) particles to resist joint softening; Mo, Ni, Cr and V elements can be adjusted according to the strength of the base material to adjust welding heat. The strength and toughness of the affected zone.
  • the invention requires that the composite addition amount of Mo, Ni, Cr and V should satisfy 0.7% ⁇ Mo + 0.8Ni + 0.4Cr + 6V ⁇ 1.1%, and when the ratio is less than 0.70%, the strength and low temperature toughness of the welded joint are low; At 1.1%, the strength of the welded joint is high, and weld cracks are likely to occur.
  • the invention controls 3.7 ⁇ Ti / N ⁇ 7.0, can protect B atoms in the steel, so that B is fully solid solution and improves hardenability.
  • the invention controls 1.0 ⁇ Ca/S ⁇ 3.0, can spheroidize the sulfide of the steel, and improve the low temperature toughness and the welding performance of the steel.
  • the method for producing high strength steel with a yield strength of 800 MPa of the present invention comprises the following steps:
  • steel is converted by a converter or an electric furnace, refined, and cast into a slab;
  • the slab is heated in a furnace at 1150 ⁇ 1270°C, and the core of the slab is heated until the temperature is warmed up, and the holding time is >1.5h;
  • Tempering heat treatment tempering temperature is 400 ⁇ 550 ° C, the heart of the steel plate after the furnace temperature begins to heat, insulation 20 ⁇ 180min.
  • the step (2) of the invention is heated to 1150 to 1270 ° C, the core holding time is > 1.5 h: the heating temperature is greater than 1150 ° C, and the core holding time is > 1.5 h to ensure sufficient solid solution of the alloying elements; the heating temperature exceeds 1270 ° C, The austenite grains grow excessively, causing the intergranular bonding force to weaken, and cracks are easily generated during rolling. In addition, when the heating temperature exceeds 1270 °C, the surface of the slab is decarburized, which affects the mechanical properties of the finished product.
  • the step (3) of the present invention has a finishing rolling temperature greater than Ar 3 in order to ensure rolling in the austenite region, and the finishing rolling temperature is less than Tnr in order to ensure rolling in the austenite non-recrystallization zone, in the austenite
  • the recrystallization zone rolling can refine the austenite grains and the cooled structure, thereby improving the toughness of the steel.
  • the final rolling reduction rate is >15%, and the large reduction ratio rolling is to form sufficient deformation energy in the non-recrystallization region, and induce austenite in the temperature range of Ar 3 to Tnr. Crystallize and refine grains.
  • Step (5) tempering heat treatment of the present invention when the steel tempering temperature of the component system exceeds 400 ° C and the steel core is maintained at a tempering temperature for more than 20 minutes, the supersaturated carbon atoms in the quenched martensite are desolvated to form a spherical shape.
  • Fe 3 C cementite, alloys Mo and V will react with C at this temperature and form fine alloy carbides, which can improve the plasticity and toughness of steel, and effectively remove the internal stress of steel;
  • the tempering temperature exceeds 550 ° C or If the high holding time is too long, the spherical Fe 3 C cementite and alloy carbide will coarsen, which will deteriorate the toughness of the steel and reduce the strength of the steel.
  • the tempering temperature and tempering time the strongest and toughness can be guaranteed. Good match.
  • Ar 3 901-325C-92Mn-126Cr-67Ni-149Mo;
  • Tnr 887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si;
  • the element symbol in the above formula indicates the weight percentage of the corresponding element ⁇ 100.
  • the invention adopts controlled rolling and controlled cooling and on-line quenching + tempering process, and controls from chemical composition design, base metal structure, quenching heating temperature and tempering heating temperature to ensure good extension while achieving ultra high strength. Rate, low temperature impact toughness and other properties.
  • the 800MPa high-strength steel produced by the composition and process of the invention has uniform tempered martensite structure, different thickness specifications, steel coil (steel plate) head, middle and tail performance fluctuations; low temperature impact toughness There has also been a substantial increase.
  • FIG. 1 is a metallographic structure diagram of a steel embodiment 1 of the present invention.
  • Figure 2 is a metallographic structure diagram of the steel embodiment 5 of the present invention.
  • Fig. 3 is a view showing the metallographic structure of the steel embodiment 8 of the present invention.
  • the smelting was carried out using a 50 kg vacuum electric furnace, and the steel composition of the present invention was carried out as shown in Table 1.
  • the molten steel smelted in a 50 kg electric furnace was cast into a slab of 120 mm thick, heated in an electric furnace, and the slab was rolled into a target thickness of 10 mm in multiple passes.
  • the finishing temperature is 820-920 °C, and the finishing rolling temperature Tf satisfies: Ar 3 ⁇ Tf ⁇ Tnr; the final pass reduction rate is set to 17%; after rolling, on-line quenching, quenching cooling rate V>e (5.3-2.53) C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B) °C / s; final cooling temperature is (Ms ⁇ 150) ° C or less; tempering heat treatment process: tempering temperature is 400 ⁇ 550 ° C, tempering time is The core of the steel plate reaches 20 to 180 minutes after reaching the tempering temperature.
  • Table 2 The specific process conditions are shown in Table 2.
  • the steel sheets after in-line quenching and tempering were subjected to longitudinal stretching and longitudinal impact tests.
  • Test samples The corresponding performance of the board is shown in Table 3.
  • the present invention can produce high-strength quenched and tempered steel with a yield strength of 8000 MPa or more, and has a tensile strength of 850 to 1000 MPa, an elongation of >12%, and an impact energy of -40 °C of -40 °C.

Abstract

一种屈服强度为800MPa级别的高强钢及其生产方法，其成分重量百分比为：C 0.06～0.14％，Si 0.1～0.3％，Mn 0.8～1.6％，Cr 0.2～0.7％，Mo 0.1～0.4％，Ni 0～0.3％，Nb 0.01～0.03％，Ti 0.01～0.03％，V 0.01～0.05％，B 0.0005～0.0030％，Al 0.02～0.06％，Ca 0.001～0.004％，N 0.002～0.005％，P≤0.02％，S≤0.01％，O≤0.008％，其余为Fe及不可避免的杂质；且，0.40％<Ceq<0.50％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.7％≤Mo+0.8Ni+0.4Cr+6V≤1.1％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0。

Description

一种屈服强度800MPa级别高强钢及其生产方法 技术领域
本发明涉及一种屈服强度800MPa级别高强钢及其生产方法。
背景技术
采用高强度、易焊接结构钢制造工程机械的梁结构、起重机的吊臂和自卸车的车体等移动设备的构件，都会减轻设备自重，减少燃料消耗，提高工作效率。随着国际竞争的加剧，采用高强度易焊接结构钢制造港口机械、矿山机械、挖掘机、装载机的梁结构、起重机的吊臂和自卸车的车体等移动设备的构件已经成为趋势。由于工程机械高性能、大型化、轻量化的发展要求，工程机械用钢的强度级别不断攀升，从500～600MPa级快速上升到700MPa、800MPa乃至1000MPa以上。由于工程机械用超高强钢苛刻的使用环境和受力条件，所以对钢材质量有严格的要求，包括强度性能、冲击性能、折弯性能、焊接性能和板形等。
目前，国内生产屈服800MPa级别的高强度钢板的企业很少。中国专利201210209649.5公开了一种抗拉800MPa级别高强度钢板的生产方法，不添加Ni元素，采用在线淬火+回火工艺(DQ+T)，得到回火马氏体+回火下贝氏体组织，其屈服强度只有700MPa。中国专利2011100343384.3公开了一种750～880MPa级车辆用高强钢及其生产方法，采用TMCP工艺在560-600℃卷取生产热轧高强钢卷。
目前，采用回火马氏体+回火下贝氏体组织生产的800MPa级高强钢不同厚度规格的各项组织比例差异较大，厚规格强度较低，容易出现性能不合。采用560～600℃高温卷取生产的析出强化型高强钢，受析出物颗粒大小和数量的影响，带钢头、中、尾强度波动较大，不能满足-40℃冲击要求。
发明内容
本发明的目的是提供一种屈服强度800MPa级别高强钢及其生产方法，采用在线淬火+回火工艺生产，该高强钢的屈服强度为800～950MPa， 抗拉强度为850～1000MPa，延伸率>12％，-40℃冲击功>40J。
为达到上述目的，本发明的技术方案是：
一种屈服强度800MPa级别高强钢，其成分重量百分比为：C：0.06～0.14％，Si：0.10～0.30％，Mn：0.80～1.60％，Cr：0.20～0.70％，Mo：0.10～0.40％，Ni：0～0.30％，Nb：0.010～0.030％，Ti：0.010～0.030％，V：0.010～0.050％，B：0.0005～0.0030％，Al：0.02～0.06％，Ca：0.001～0.004％，N：0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免的杂质；且上述元素同时需满足如下关系：0.40％<Ceq<0.50％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.7％≤Mo+0.8Ni+0.4Cr+6V≤1.1％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0。
进一步，所述高强钢的屈服强度为800～950MPa，抗拉强度为850～1000MPa，延伸率>12％，-40℃冲击功>40J。
所述高强钢的的显微组织为回火马氏体。
在本发明钢的成分设计中：
C：固溶强化，调整马氏体组织的强度和塑韧性，低碳马氏体的在线淬火态抗拉强度与C含量呈如下关系：Rm＝2940C(％)+820(MPa)，Rm为抗拉强度，C含量在0.06％以上可以保证淬火态抗拉强度大于900MPa，再通过回火进一步调整、降低抗拉强度到850MPa以上，改善韧性；C含量较高会导致整体C当量的提高，焊接时容易产生裂纹。因此，本发明的C含量范围为0.06～0.14％。
Si：0.10％以上的Si可以起到较好的脱氧作用，Si超过0.30％容易产生红铁皮，Si含量较高时容易恶化马氏体高强钢的韧性。因此，本发明的Si含量范围为0.10～0.30％。
Mn：Mn含量在0.8％以上可以提高钢的淬透性，Mn含量超过1.6％容易产生偏析和MnS等夹杂物，恶化马氏体高强钢的韧性。因此，本发明的Mn含量范围为0.80～1.60％。
Cr：Cr含量在0.2％以上可以提高钢的淬透性，有利于在淬火时形成全马氏体组织。在回火温度400～550℃范围内，Cr会形成Cr的碳化物，具有抗中温回火软化的作用，Cr含量超过0.70％，在焊接时会出现较大的火花，影响焊接质量。因此，本发明的Cr含量范围为0.20～0.70％。
Mo：0.10％以上的Mo元素可提高钢的淬透性，有利于在淬火时形成全马氏体组织；在400℃以上的高温下，Mo会与C反应形成化合物颗粒，具有抗高温回火软化和焊接接头软化的作用，Mo含量太高会导致碳当量提高，恶化焊接性能，同时Mo属于贵金属，会提高成本。因此，本发明的Mo含量范围为0.10～0.40％。
Ni：Ni元素具有细化马氏体组织、改善钢的韧性的作用，Ni含量太高会导致碳当量提高，恶化焊接性能，同时Ni属于贵金属，会提高成本。因此，本发明的Ni含量范围为0～0.30％。
Nb、Ti和V：Nb、Ti和V为微合金元素，与C、N等元素形成纳米级析出物，在加热时抑制奥氏体晶粒的长大；Nb可以提高未再结晶临界温度Tnr，扩大生产窗口；Ti的细小析出物颗粒可以改善焊接性能；V在回火过程中与N和C反应析出纳米级V(C,N)颗粒，可以提高钢的强度；本发明的Nb含量范围为0.01～0.03％，Ti含量范围为0.01～0.03％，V含量范围为0.01～0.05％。
B：微量的B可以提高钢的淬透性，提高钢的强度，超过0.0030％的B容易产生偏析，形成碳硼化合物，严重恶化钢的韧性。因此，本发明的B含量范围为0.0005～0.0030％。
Al：Al用作脱氧剂，钢中加入0.02％以上的Al可细化晶粒，提高冲击韧性，Al含量超过0.06％容易产生Al的氧化物夹杂缺陷。因此，本发明的Al含量范围为0.02～0.06％。
Ca：在钢冶炼过程中，超过0.001％的微量Ca元素可以起到净化剂作用，改善钢的韧性；Ca含量超过0.004％时，容易形成尺寸较大的Ca的化合物，反而会恶化韧性。因此，本发明Ca含量范围为0.001～0.004％。
N：本发明要求严格控制N元素的含量范围。在回火过程中，0.002％以上的N元素可以与V和C反应形成纳米级的V(C，N)粒子，起到析出强化的作用，在焊接过程中也可以通过析出强化抵抗热影响区软化；N含量超过0.005％则容易导致形成粗大的析出物颗粒，恶化韧性。因此，本发明N含量范围为0.002～0.005％。
P、S和O：P、S和O作为杂质元素影响钢的塑、韧性，本发明的这四种元素的控制范围为P≤0.02％，S≤0.01％，O≤0.008％。
对于在线淬火型屈服800MPa高强钢的碳当量Ceq需满足：0.40％<Ceq<0.50％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/150，Ceq太低容易出现焊接接头软化，Ceq太高容易出现焊接微裂纹。
本发明控制0.7％≤Mo+0.8Ni+0.4Cr+6V≤1.1％，主要用于保证800MPa高强钢的等强匹配焊接，调节焊接热影响区的强度和低温韧性，达到与母材钢板强度和低温韧性的最佳匹配。其中，Mo、Ni和Cr元素都可以降低钢的临界冷却速度，提高钢的淬透性，提高焊接接头的强度；Mo在高温下与C反应形成化合物，具有抵抗焊接接头软化的作用；Mo和Ni元素都具有细化组织，改善韧性的作用；V与N反应生成纳米级V(C，N)颗粒可以抵抗接头软化；Mo、Ni、Cr和V元素的搭配可以根据母材强度调节焊接热影响区的强度和韧性。本发明要求Mo、Ni、Cr和V的复合添加量应满足0.7％≤Mo+0.8Ni+0.4Cr+6V≤1.1％，低于0.70％时，焊接接头的强度和低温韧性都较低；高于1.1％时，焊接接头强度偏高，容易产生焊接裂纹。
本发明控制3.7≤Ti/N≤7.0，可以保护钢中的B原子，使得B充分固溶，提高淬透性。
本发明控制1.0≤Ca/S≤3.0，可以使钢种的硫化物球化，改善钢的低温韧性和焊接性能。
本发明的屈服强度800MPa级别高强钢的生产方法，其包括如下步骤：
1)冶炼、铸造
按上述成分采用转炉或电炉炼钢，精炼，铸造成铸坯；
2)铸坯加热
将铸坯于1150～1270℃的炉中加热，待铸坯心部到温后开始保温，保温时间>1.5h；
3)轧制
采用单机架往复轧制或多机架热连轧将铸坯轧至目标厚度，终轧温度为820～920℃，同时终轧温度Tf满足：Ar3<Tf<Tnr，其中，Ar3为亚共析钢奥氏体向铁素体转变开始温度：Ar3＝901-325C-92Mn-126Cr-67Ni-149Mo，Tnr为未再结晶临界温度：Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si；轧制最后一道次轧制压下率>15％；
4)淬火热处理工艺
轧后在线淬火至(Ms-150)℃以下；Ms为马氏体转变开始温度，Ms＝539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo；层流冷却系统控制冷却速度V>e(5.3-2.53c-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s，保证形成全马氏体组织。
5)回火热处理工艺
回火热处理：回火温度为400～550℃，钢板心部达到炉温后开始保温，保温20～180min。
在本发明的生产方法中：
本发明步骤(2)铸坯加热至1150～1270℃，心部保温时间>1.5h：加热温度大于1150℃、心部保温时间>1.5h可以保证合金元素充分固溶；加热温度超过1270℃，奥氏体晶粒过度长大，引起晶间结合力减弱，在轧制时容易产生裂纹；另外加热温度超过1270℃容易引起钢坯表面脱碳，对成品力学性能造成影响。
本发明步骤(3)轧制的终轧温度大于Ar3是为了保证在奥氏体区轧制，终轧温度小于Tnr是为了保证在奥氏体未再结晶区轧制，在奥氏体未再结晶区轧制可以细化奥氏体晶粒和冷却后的组织，从而改善钢的强韧性。
本发明步骤(3)轧制最后一道次压下率>15％，大压下率轧制是为了在未再结晶区形成足够的变形能，在Ar3～Tnr温度范围内诱发奥氏体再结晶，细化晶粒。
本发明步骤(5)回火热处理：该成分体系的钢回火温度超过400℃并保持钢板心部达到回火温后保温20min以上时，淬火马氏体中的过饱和碳原子脱溶形成球状Fe3C渗碳体，合金Mo和V在该温度下会与C反应并形成细小的合金碳化物，可以改善钢的塑性和韧性，同时有效去除钢的内应力；回火温度超过550℃或高保温时间过长，球状Fe3C渗碳体和合金碳化物发生粗化，反而会恶化钢的韧性，并降低钢的强度；通过调整回火温度和回火时间可以保证强、韧性实现最佳匹配。
本发明涉及的关系式：
0.40％<Ceq<0.50％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.7％≤Mo+0.8Ni+0.4Cr+6V≤1.1％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0中元素符号表示对应元素的重量百分含量。
本发明涉及的计算公式：
Ar3＝901-325C-92Mn-126Cr-67Ni-149Mo；
Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si；
Ms＝539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo；
e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)；
上述公式中元素符号表示对应元素的重量百分含量×100。
本发明的有益效果：
本发明采用控轧控冷和在线淬火+回火工艺，从化学成分设计、母材组织、淬火加热温度、回火加热温度等方面进行控制，保证在实现超高强度的同时，获得良好的延伸率、低温冲击韧性等性能。
与现有工艺相比，采用本发明的成分、工艺生产的800MPa高强钢具有均一的回火马氏体组织，不同厚度规格、钢卷(钢板)头、中、尾性能波动小；低温冲击韧性也有大幅提高。
附图说明
图1为本发明钢实施例1的金相组织图；
图2为本发明钢实施例5的金相组织图；
图3为本发明钢实施例8的金相组织图。
具体实施方式
下面结合实施例对本发明做进一步说明
采用50kg真空电炉进行冶炼，本发明钢成分的实施例如表1所示。将50kg电炉冶炼的钢水浇注成120mm厚的钢坯，放入电炉中加热，采用多道次将钢坯轧制成目标厚度10mm。终轧温度为820～920℃，同时终轧温度Tf满足：Ar3<Tf<Tnr；末道次压下率设定17％；轧后进行在线淬火，淬火冷却速度V>e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s；终冷温度为(Ms～150)℃以下；回火热处理工艺：回火温度为400～550℃，回火时间为钢板心部达到回火温度后20～180min。具体工艺条件如表2所示。
将在线淬火+回火后的钢板进行纵向拉伸和纵向冲击试验。各试验样 板对应的性能如表3所示。从表3可以看出，本发明可以制造出屈服强度8000Mpa以上的高强度调质钢，其抗拉强850～1000MPa，延伸率>12％，-40℃冲击功>40J。
图1～图3给出了实施例1、5、8试验钢的金相组织图，可以看出，成品钢板的金相组织为均一的板条状回火马氏体，且组织细密。
表1本发明实施例的化学成分    单位
Figure PCTCN2015096638-appb-000001
表2本发明实施例的轧制工艺条件
Figure PCTCN2015096638-appb-000002
Figure PCTCN2015096638-appb-000003
表3本发明实施例的力学性能
Figure PCTCN2015096638-appb-000004

Claims (6)

  1. 一种屈服强度800MPa级别高强钢，其成分重量百分比为：C：0.06～0.14％，Si：0.10～0.30％，Mn：0.80～1.60％，Cr：0.20～0.70％，Mo：0.10～0.40％，Ni：0～0.30％，Nb：0.010～0.030％，Ti：0.010～0.030％，V：0.010～0.050％，B：0.0005～0.0030％，Al：0.02～0.06％，Ca：0.001～0.004％，N：0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免的杂质；且上述元素同时需满足如下关系：0.40％<Ceq<0.50％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.7％≤Mo+0.8Ni+0.4Cr+6V≤1.1％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0。
  2. 根据权利要求1所述的屈服强度800MPa级别高强钢，其特征在于，所述高强钢的显微组织为回火马氏体。
  3. 根据权利要求1或2所述的屈服强度800MPa级别高强钢，其特征在于，所述高强钢的屈服强度为800～950MPa，抗拉强度为850～1000MPa，延伸率>12％，-40℃冲击功>40J。
  4. 如权利要求1所述的屈服强度800MPa级别高强钢的生产方法，包括如下步骤：
    1)冶炼、铸造
    按上述权利要求1所述成分采用转炉或电炉炼钢，精炼，铸造成铸坯；
    2)板坯加热
    将铸坯于1150～1270℃的炉中加热，待铸坯心部达到炉温后开始保温，保温时间>1.5h；
    3)轧制
    采用单机架往复轧制或多机架热连轧将铸坯轧至目标厚度，终轧温度为820～920℃，同时终轧温度Tf满足：Ar3<Tf<Tnr，其中，Ar3为亚共析钢奥氏体向铁素体转变开始温度：Ar3＝901-325C-92Mn-126Cr-67Ni-149Mo，Tnr为未再结晶临界温度：Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si；轧制最后一道次轧制压下率>15％；
    4)淬火热处理工艺
    轧后在线淬火至(Ms-150)℃以下；Ms为马氏体转变开始温度，Ms＝539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo；层流冷却系统控制冷却速度V>e(5.3-2.53c-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s，保证形成全马氏体组织；
    5)回火热处理工艺
    回火热处理：回火温度为400～550℃，钢板心部达到炉温后开始保温，保温20～180min。
  5. 根据权利要求4所述的屈服强度800MPa级别高强钢的生产方法，其特征在于，该生产方法获得的高强钢的显微组织为回火马氏体。
  6. 根据权利要求4或5所述的屈服强度800MPa级别高强钢的生产方法，其特征在于，该生产方法获得的高强钢的屈服强度为800～950MPa，抗拉强度为850～1000MPa，延伸率>12％，-40℃冲击功>40J。
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