WO2007000109A1 - Fers noirs etamables et procede de production - Google Patents

Fers noirs etamables et procede de production Download PDF

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Publication number
WO2007000109A1
WO2007000109A1 PCT/CN2006/001460 CN2006001460W WO2007000109A1 WO 2007000109 A1 WO2007000109 A1 WO 2007000109A1 CN 2006001460 W CN2006001460 W CN 2006001460W WO 2007000109 A1 WO2007000109 A1 WO 2007000109A1
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controlled
rolling
soft
temperature
annealing
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PCT/CN2006/001460
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English (en)
French (fr)
Inventor
Jun Li
Liyang Zhang
Xiuzhen Lin
Xuenan Gong
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Baoshan Iron & Steel Co., Ltd.
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Publication of WO2007000109A1 publication Critical patent/WO2007000109A1/zh

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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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/06—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the invention relates to a soft tinplate and a manufacturing method thereof, in particular to a soft tinplate with a HR30T of 49 ⁇ 3 soft tinplate (hereinafter referred to as T-1CA) and a HR30T of 53 ⁇ 3 (hereinafter referred to as T -2CA) and its manufacturing method.
  • the soft tin plate is produced by continuous annealing of titanium-IF steel, and is mainly used for producing expanded flower basket barrels, deformed can lids and stamped deformed cans. Background technique
  • the hardness (HR30T) range of tinplates with different tempering levels is shown in Table 1.
  • T-1 to T-3 are soft tinplates
  • T-4 to T-6 are hard tinplates.
  • Table 1 Hardness range of tinplates with different tempering levels
  • tinplate was mainly produced using low carbon aluminum killed steel.
  • the patent published by Japan Steel Tube Co., Ltd. on March 19, 1996 uses a low carbon aluminum killed steel to produce a soft tin plate with a hardness (HR30T) of less than or equal to T-3 hardness (HR30T of 54 to 60).
  • the chemical composition range is: 0.050 ⁇ C(%) ⁇ 0.085, preferably 0.060 ⁇ C(%) ⁇ 0.080, 0.05 ⁇ Mn(%) ⁇ 0.60, S(%): 0.020, P(%): 0.020, Al(%) ⁇ 0.10, and the atomic ratio of Al and N is greater than or equal to 15.
  • Hot rolling coiling temperature is controlled at 550 ° C ⁇ 620 ° C, annealing temperature is controlled above 650 ° C, below the transition temperature, and cooled at a cooling rate of 30 ° C / s However, it is aged at 350 ° C to 450 ° C and aged at 350 ° C to 450 ° C for more than 30 seconds.
  • low-carbon aluminum killed steel When low-carbon aluminum killed steel is used to produce tinplate, obvious aging will occur. After aging, the hardness of the product will increase, and the subsequent processing performance will be worse. The conditions of deep deformation, large expansion, severe bending and other large deformations will be met. Underneath, it is prone to cracking, resulting in slip line texture or curved surface ribs and other defects. In addition, the inevitable aging problem of low carbon steel causes the tin plate to be easily wrinkled when bent, and the slip line appears after stamping or tensile deformation, which is difficult to meet the needs of users. Moreover, the use of low carbon aluminum killed steel is not suitable for the production of very soft tinplate.
  • Japan Steel Tube Co., Ltd. which discloses a soft tinplate using the following chemical composition range, is disclosed in Japanese Patent Laid-Open No. JP7197192: C: 0.004%, Mn: ⁇ 0.6%, A1: 0.03-0.10%, N ⁇ O.004%, Nb: 0.021 ⁇ 0.050%, and the atomic ratio of Nb to C is greater than 1.0.
  • This patent uses the IF steel, which has clear requirements for the content of Nb. Due to the sensitivity of the IF steel to the production process parameters, especially to the hot rolling process parameters, the product performance is unstable, and its recrystallization temperature is high, the required annealing temperature is high, and it is necessary to organize the production of the product.
  • the patent publication discloses the use of hot-rolling coiling between 600 ° C and 800 ° C, the coiling temperature is high, and in particular, the upper limit temperature is obviously too high to be practically operated, and the patent protects The coiling temperature range is obviously unreasonable, because the steel sheet is severely oxidized when it is wound up at 800 °C, and even if it is above 630 °C, the scale is obviously thickened, which not only affects the pickling speed of the subsequent process, but also affects The surface quality of the final product.
  • the patent specification describes that it is annealed between 670 ° C and 800 ° C
  • the patent uses ⁇ IF steel to produce a soft tin plate, which is close to the annealing temperature range given by the patent.
  • 670 °C for example, 670 X: ⁇ 74 CTC
  • a qualified soft tin plate is produced, so the annealing temperature range protected by the patent is also obviously unreasonable.
  • the present invention provides T-1CA and T-2CA soft tinplates having a composition (% by weight):
  • Al 0 ⁇ 025 to 0.075%, preferably Al: 0.030 to 0.060%,
  • Ti 0.03 - 0.08%, preferably Ti: 0.05 - 0.07%,
  • the balance is Fe and some unavoidable impurity elements.
  • the hardness of the soft tin plate increases, and the plasticity decreases.
  • the present invention limits the C element content to 0.006 %.
  • the addition amount of Ti must be increased correspondingly, so that the production cost is also increased, so the C content is not suitable. Too high.
  • the preferred C element content is 0.004%.
  • Mn is the main strengthening element of soft tinplate, and the higher the content, the higher the hardness of the product.
  • the price of Mn is relatively high.
  • the content is controlled below 0.20%, it can be used for the T-2CA soft tinplate which requires higher hardness. It can be easily and economically controlled to meet the requirements by increasing the flattening elongation, but
  • the content is less than 0.10%, on the one hand, the material is soft, and on the other hand, the steel originally contains a certain amount of Mn. If ⁇ is required to be lower than 0, 10%, it is necessary to reduce Mn, but the cost is extremely high.
  • the present invention limits its content to between 0.10% and 0.20%.
  • Ti is mainly used to fix free C in steel to form TiC.
  • Ti is beneficial to improve the anti-aging properties of the material, especially its stamping formability.
  • TiC also has a certain dispersion strengthening effect, which can improve the strength and hardness of the material.
  • Ti is more expensive (although much cheaper than Nb), and its content is directly related to the manufacturing cost, so its content should be strictly controlled.
  • controlling the Ti content to 0.08 % or less is sufficient, but when When the content is less than 0.03%, free C in the steel and a small amount of N cannot be fixed. Therefore, the present invention requires a content of Ti of between 0.03 % and 0.08%.
  • a preferred Ti content is between 0.05% and 0.07%.
  • A1 is a sedative element and is also a strong nitride forming element. It is mainly used to fix N atoms, which is beneficial to improve the anti-aging property of materials. At the same time, A1 is also an indispensable deoxidizer in steel making. When the content is less than 0.025, it can not meet the quality requirements. When the content is more than 0.075%, not only is the cost high, but also the growth of the annealed recrystallized grains is suppressed. Therefore, the present invention limits the content to between 0.025% and 0.075%. The preferred A1 content is limited to between 0.030% and 0,060%.
  • the present invention requires that the content be controlled to be less than 0.03 %, and when the content exceeds 0.03 %, the corrosion resistance is remarkably deteriorated.
  • the T-1CA and T-2CA soft tinplate of the invention are produced by the following processes: steelmaking, continuous casting, hot rolling, acid rolling, continuous annealing, flattening, tin plating, steel casting, continuous casting, Hot rolling ⁇ acid washing ⁇ cold continuous rolling ⁇ continuous annealing ⁇ leveling ⁇ tin plating, or steelmaking one continuous casting one hot rolling ⁇ acid washing ⁇ multiple reversible cold rolling ⁇ continuous annealing ⁇ leveling-tin plating process.
  • the molten steel is vacuum degassed by RH refining, and the corresponding measures for controlling inclusions are adopted. Finally, the continuous casting blank is produced by a conventional continuous casting process, and then hot rolled.
  • Hot rolling The method of the present invention has a slab heating temperature (i.e., furnace temperature) in the hot rolling process: 1220 ⁇ 30 ° C, and a hot rolling finishing temperature of 900 ⁇ 20 ° C.
  • a slab heating temperature i.e., furnace temperature
  • a hot rolling finishing temperature 900 ⁇ 20 ° C.
  • the hot rolling finishing temperature is controlled at 900 ⁇ 20 °C
  • the surface of the strip is oxidized lightly, and the mixed crystal structure does not appear in the strip steel, and the final product has uniform microstructure.
  • the preferred hot rolling final rolling temperature is controlled between 885 ° C and 915 ° C for more uniform performance and better surface quality.
  • the hot rolling coiling temperature of the present invention is controlled between 590 ⁇ 40 ° C. Increasing the coiling temperature can reduce the hardness of the hot-rolled substrate, thereby lowering the hardness of the final product and improving the formability of the final product. However, when the coiling temperature is greater than 630 ° C, the surface of the strip is easily thickened, and pickling is difficult. And affect the surface quality of the product.
  • the hot rolling coiling temperature is controlled at 590 ⁇ 40 ° C, and the amount of scale on the surface of the strip after coiling is measured. Less, pickling is easier, and the surface quality of the final product is good.
  • the preferred hot rolling coiling temperature is controlled between 570 ° C and 610 ° C for good plasticity and better surface quality.
  • Pickling and cold rolling It can be produced by acid rolling combined unit, or pickled first, followed by cold rolling or multiple reversible cold rolling, but it is best to use acid rolling combined unit to improve production efficiency.
  • the speed of the unit should be adjusted according to the pickling ability of the unit to ensure the pickling effect.
  • cold rolling is carried out for five-frame continuous rolling, the total reduction ratio of cold rolling is 82% to 92%.
  • the cold rolling deformation will affect the mechanical properties of the material, and the suitable cold rolling deformation is convenient for the dimensional accuracy of the rolled hard material and the shape control.
  • the amount of deformation is too small, the formability of the material is poor, and if the amount of deformation is too large, the consumption of cold rolling is increased and the shape of the rolled hard plate is poor, which affects the high-speed stable plate of the subsequent continuous retreating process.
  • the present invention uses continuous annealing to produce T-1CA soft tin plate and T-2CA soft tin plate, annealing temperature is 720 ° C ⁇ 770 ° C, holding time is 25 s ⁇ 50 s.
  • the preferred annealing temperature is 735 ° C to 765 ° C.
  • the soft tinplate can be produced by hood annealing, the mechanical properties of the large-volume, middle and tail tin-plated products produced by the hood annealing process are not uniform, and the shape and surface quality of the products are far less than that of continuous annealing. Soft tinplate.
  • the invention adopts titanium-IF steel continuous Annealing production of T-1CA soft tinplate and T-2CA soft tinplate, its mechanical properties are uniform, product surface quality is good, can better meet user requirements, and thus has a strong market competitiveness.
  • the annealing temperature is higher than 770 °C, because the strip material is soft, when the strip is wider and the thickness is thinner, the strip is prone to buckling or even breaking in the annealing furnace, and the energy consumption will also increase;
  • the annealing temperature is lower than 720 ° C, it is difficult to ensure the recrystallization of the steel sheet at the normal continuous annealing unit speed, the hardness of the product is increased, and the molding property of the product is deteriorated.
  • the invention uses the continuous annealing of titanium-IF steel to produce soft tinplate, which has lower annealing temperature than the continuous annealing of the yttrium-IF steel to produce soft tinplate (according to the simulated annealing test results, the annealing temperature of the IF steel should be 750 ° C ⁇ 800 ° C to ensure sufficient recrystallization), so in the production planning can reduce the amount of transition volume and rise and fall time, improve production efficiency, reduce production costs, and because of the temperature reduction, Reduces the chance of buckling and breaking of the strip in the annealing furnace.
  • the holding time and the annealing temperature are mutually influential.
  • Increasing the annealing temperature facilitates shortening the holding time, but the holding time cannot be less than 25 s. Otherwise, the recrystallized grain growth is insufficient, the material is hard, and the strip is easy to run when the unit production speed is too high. Partial.
  • the holding time can not be too long. When the holding time exceeds 50s, the speed of the unit is too low, on the one hand, the production efficiency is reduced, on the other hand, the grain length is too large, the material is soft and the strip is easy to scoop in the annealing furnace. The song is even broken.
  • the amount of flattening deformation after the recrystallization of Ti-IF steel has a great influence on the material properties. As the amount of deformation increases, the strength and hardness increase significantly.
  • the invention uses T-1CA soft tinplate produced by continuous annealing, and is double-stand flattened after annealing, and the flattening elongation is controlled between 0.8% and 1.8%, and for T-2CA soft tinplate, it is flattened. The elongation is controlled between 1.8% and 3.0%.
  • the above T-1CA and T-2CA flattening elongation ranges can be adjusted according to the thickness of the product. When the strip is thin, a small flat elongation is used. A thicker elongation is used when thicker.
  • Tin plating uses T-1CA soft tin plate and T-2CA soft tin plate produced by continuous annealing, and can be produced by the same tin plating process as ordinary tin plate.
  • the invention adopts titanium-IF steel to produce soft tin plate, which not only does not cause aging problems within the chemical composition range of the invention, but is also insensitive to hot rolling process parameters.
  • the soft tin plate produced by the titanium-IF steel of the invention has lower recrystallization temperature than the soft tin plate produced by the first-IF steel, and the heat energy consumption of the furnace is low, the temperature transition time is short during normal production, and the transition roll or return The amount of the roll will also be reduced, so that the production cost can be reduced, and the strip is less likely to occur when annealed in a continuous annealing furnace.
  • the bucks have good performance and the risk of breaking the belt is small.
  • the soft tin plate produced by the titanium-IF steel of the invention has more stable mechanical properties than the soft tin plate produced by the first-IF steel.
  • the soft tinplate of the present invention has a lower finish rolling temperature and a coiling temperature for hot rolling under the premise of ensuring uniform material properties, and the surface of the strip is less iron oxide after hot rolling, and the subsequent pickling is very Easy to carry out, the surface quality of the final product is good.
  • Example 1-6 T-1CA soft tinplate, tantalum is produced by titanium-IF steel, molten steel is vacuum degassed by RH refining, and various measures for controlling inclusions are adopted. Finally, the continuous continuous casting process is used to produce the joint.
  • the chemical composition of the molten steel and molten steel is shown in Table 2. The steel also contains other unavoidable impurity elements, and the balance is Fe.
  • the continuous casting billet is heated to the hot rolling billet temperature before hot rolling, and is coiled after rough rolling, finish rolling and laminar cooling, and cooled by room temperature after 2 to 3 days at room temperature (cickling and cold rolling combined unit) Production of cold rolled sheets.
  • the specific process parameters are shown in Table 3: Table 3 Performance of main process parameters of examples 1 to 6
  • the cold-rolled strip was annealed and flattened in a CAPL unit (continuous annealing and flattening unit) and then subjected to conventional tin plating to produce a tinplate.
  • the annealing process parameters, the flattening elongation and the final product hardness are shown in Table 4.
  • Example 7-12 ⁇ —2CA soft tinplate, produced by titanium-IF steel.
  • the molten steel is vacuum degassed by RH refining, and various measures for controlling inclusions are used. Finally, the continuous continuous casting process is used to produce the joint.
  • the chemical composition of the molten steel and molten steel is shown in Table 6. The steel also contains other unavoidable impurity elements, and the balance is Fe.
  • the continuous casting billet is heated to the hot rolling billet temperature before hot rolling, and is coiled after rough rolling, finish rolling and laminar cooling, and cooled by room temperature after 2 to 3 days at room temperature (cickling and cold rolling combined unit) Production of cold rolled sheets.
  • the specific process parameters are shown in Table 7: Table 7 Performance of main process parameters of Examples 7-12
  • the cold-rolled strip was annealed and leveled in a CAPL unit (continuous annealing and flattening unit), and then subjected to conventional tin plating to produce a tin plate.
  • the annealing process parameters, flat elongation and product hardness are shown in Table 8.

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  • Engineering & Computer Science (AREA)
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Description

软质镀锡原板及其制造方法
技术领域
本发明涉及软质镀锡板及其制造方法， 特别涉及 HR30T为 49± 3软 质镀锡板 （以下称为 T-1CA) 和 HR30T为 53 ±3的软质镀锡板 （以下称 为 T-2CA)及其制造方法， 该软质镀锡板采用钛一 IF钢连续退火的方法生 产， 主要用于生产扩径花篮桶， 变形较复杂的罐盖和冲压变形的罐。 背景技术
根据日本工业标准 JIS G 3303 , 不同调质度级别镀锡板的硬度 (HR30T)范围如表 1所示。 其中从 T-1到 T-3为软质镀锡板， T-4到 T-6 为硬质镀锡板。 表 1 不同调质度级别镀锡板的硬度范围
Figure imgf000003_0001
以前， 镀锡板主要使用低碳铝镇静钢生产。 日本钢管株式会社于 1996 年 3 月 19 日公开的专利 （NO.JP8073943 ) 采用低碳铝镇静钢生产硬度 ( HR30T) 小于等于 T-3硬度 （HR30T为 54〜60) 的软质镀锡板。 其化 学成份范围为： 0.050^C(%)^0.085 , 最好是 0.060^C(%)^0.080, 0.05 ^Mn(%)^ 0.60, S(%): 0.020， P(%): 0.020， Al(%)^ 0.10, 且 Al 和 N的原子个数比大于等于 15。 热轧卷取温度控制在 550°C〜620°C， 退 火温度控制在 650°C以上， ,转变温度以下， 并以 30°C/s的冷却速度冷 却到 350°C〜450°C， 在 350°C〜450°C时效处理 30秒以上。
采用低碳铝镇静钢生产镀锡板时， 会发生明显的时效， 时效后其产品 硬度将增高， 而后续加工性能则变差， 在深冲、 大扩径、 剧烈弯曲等大变 形量的条件下，很容易出现开裂、产生滑移线网紋或弯曲表面起棱等缺陷。 此外低碳钢不可避免的时效问题导致镀锡板弯曲时很容易皱折起棱， 冲压 或拉伸变形后出现滑移线，难以满足用户的需求。而且， 采用低碳铝镇静钢 不适合生产很软的镀锡板。
随着 IF钢生产技术的进步，在国外，发达国家早就开始大批量采用添 加铌 （Nb) 的 IF钢生产镀锡产品。 由于 IF钢固有的良好成形性能和抗时 效性能， 使得 IF钢镀锡产品已显示强大的市场竞争力。
日本钢管株式会社于 1995年 8月 1日公开的专利特开平 NO.JP7197192 中采用以下化学成分范围生产软质镀锡板： C: 0.004 %， Mn: ^0.6 % , A1: 0.03-0.10 % , N^O.004 % , Nb: 0.021〜0.050 %， 且 Nb与 C的原子 数量比大于 1.0。该专利采用的是铌一 IF钢， 对 Nb元素的含量都提出了明 确的要求。 由于铌一 IF钢对生产工艺参数敏感， 特别是对热轧工艺参数敏 感， 使产品性能不稳定， 而且其再结晶温度高， 所需的退火温度高， 在组 织该产品的生产时， 需要使用较多的过渡料和较长的过渡时间， 特别是在 连续退火炉内容易产生瓢曲甚至发生断带， 因而通板性能差， 同时热能消 耗大， 加上合金元素铌价格昂贵， 故其生产成本相对较高。 另外， 铌一 IF 钢塑性差， 虽然各向异性不大， 但其总体力学性能较钛一 IF钢差。 最后， 铌在开采和冶炼时有一定的放射性，添加铌的镀锡板（主要用于食品行业） 是否对人体有害也还有争议。
同时， 尽管该专利公开说明采用在 600°C〜800°C之间进行热轧卷取， 但该卷取温度偏高， 特别是上限温度明显过高， 无法进行实际操作， 该专 利所保护的卷取温度范围明显不合理， 因为在接近 800°C卷取时， 钢板氧 化严重， 即使是在 630°C以上氧化铁皮就明显增厚了， 这不仅影响后工序 的酸洗速度， 而且会影响最终产品的表面质量。 另外， 尽管该专利公幵说 明釆用在 670°C〜800°C之间退火， 但由于该专利采用的是铌 IF钢生产软 质镀锡板，在该专利给定的退火温度范围内接近 670°C时退火时（例如 670 X：〜 74CTC ) ， 钢板很难在正常的机组速度下完成再结晶， 即不可能生产 出合格的软质镀锡板，因此，该专利所保护的退火温度范围也明显不合理 发明内容
本发明的目的是提供使用钛一IF钢连续退火生产的 T-1CA和 T-2CA 软质镀锡板。
为达到上述目的， 本发明提供 T-1CA和 T-2CA软质镀锡板， 其成分 为 （重量百分比） ：
C^O.006%, 最好为 C^O.004%,
Μη: 0·10〜0.20%，
Al: 0·025〜0.075%， 最好为 Al: 0.030〜0.060%，
Si^O.03%,
Ti: 0.03— 0.08%, 最好为 Ti: 0.05— 0.07%,
P^ O.015%,
S^O.015%,
N^O.003%,
O 0.004%，
余量为 Fe和一些不可避免的杂质元素。
以下是本发明专利主要元素的作用及其限定说明-
C: 0.006%,
随着 C元素含量的增加， 一方面软质镀锡板的硬度增加， 塑性下降， 为了把硬度 HR30T稳定控制在 56以下， 并保证材料的成型性能， 本发明 将 C 元素含量限定在 0.006 % , 以获得合适的硬度和优良的成型性能； 另一方面， C含量增加之后， 为了确保软质镀锡板的抗时效性能， 必须相 应增加 Ti的添加量， 使得生产成本也增加， 因此 C含量不宜太高。 优选 的 C元素含量 0.004%。
Mn: 0.10〜0.20%，
Mn是软质镀锡板的主要强化元素， 其含量越高产品硬度越高。但 Mn 价格较高， 为了节约成本， 在满足性能的前提下， 用量越少越经济， 当其 含量控制在 0.20%以下时对于要求较高硬度的 T一 2CA软质镀锡板而言， 可以通过提高平整延伸率即可很方便也非常经济进行控制来满足要求， 但 当其含量低于 0.10 %时， 一方面材质偏软， 另外一方面钢中本来就含有一 定量的 Mn。 如果要求 Μη低于 0, 10 %则需要降 Mn， 反而成本极高。 因而 本发明将其含量限定在 0.10 %〜0.20 %之间。
Ti: 0.03〜 0.08%,
Ti主要用于固定钢中的游离 C, 使其形成 TiC， 同时 Ti有利于提高材 料的抗时效性能， 尤其是其冲压成型性， 同时 TiC也有一定的弥散强化作 用， 能提高材料的强度和硬度。 但 Ti价格较贵 （虽然比 Nb便宜得多） ， 其含量的多少直接关系到制造成本， 故应严格控制其含量， 在本发明中， 把 Ti含量控制在 0.08 %以下足以满足要求， 但当其含量低于 0.03%时， 无 法将钢中的游离 C及少量的 N全部固定， 因此， 本发明要求 Ti的含量在 0.03 %〜0.08 %之间。 优选的 Ti含量在 0.05 %〜0.07%之间。
A1: 0.025〜0.075%，
A1是镇静元素， 也是强氮化物形成元素， 主要用来固定 N原子， 对 提高材料的抗时效性能有利， 同时 A1 也是炼钢时不可缺少的脱氧剂， 其 含量小于 0.025时， 无法满足质量要求， 而其含量高于 0.075 %时， 不仅成 本较高， 而且会抑制退火再结晶晶粒的长大， 因此， 本发明将其含量限定 在 0.025 %〜0.075 %之间。 优选的 A1含量限定在 0.030%〜0,060 %之间。
Si: 0.03%，
Si虽有一定的强化作用但恶化耐蚀性， 故越低越好， 本发明要求将其 含量控制在 0.03 %以下， 当其含量超过 0.03 %时， 明显恶化耐蚀性能。
其它元素： P (P^O.015%)、 S ( S^O.015%)、 N ( N^O.003%) 、 O ( O 0.004%) ， 是有害杂质元素， 应严格控制， 越低越好， 否则影响 软质镀锡板的力学性能及耐蚀性。 这些杂质元素， 只要在本发明的限定范 围内， 都可生产出满足要求的软质镀锡板。
本发明的 T-1CA和 T-2CA软质镀锡板采用以下工序生产： 炼钢一连 铸一热轧→酸轧联合—连续退火→平整→镀锡， 也可以采用炼钢一连铸一 热轧→酸洗→冷连轧→连续退火→平整→镀锡， 或炼钢一连铸一热轧→酸 洗→多次可逆冷轧→连续退火→平整—镀锡工艺生产。
以下是主要工序的关键点：
炼钢： 钢水经 RH精炼真空脱气处理， 并采用相应的控制夹杂物的措 施， 最后经常规连铸工艺生产连铸坯， 然后进行热轧。
热轧：本发明的方法在热轧工序板坯加热温度（即出炉温度）为： 1220 ± 30°C， 热轧终轧温度为 900 ± 20°C。 理论和生产实践均已证明终轧温度 大于 920°C时， 带钢表面氧化严重， 产品表面质量差， 但当终轧温度低于 880 °C时， 热轧带钢进入两相区轧制易出现混晶组织， 并导致最终产品组 织性能的不均。 而热轧终轧温度控制在 900 ± 20°C时， 使带钢表面氧化较 轻， 在带钢中也不出现混晶组织， 最终产品组织性能均匀。 优选的热轧终 轧温度控制在 885 °C〜915 °C之间， 以获得更均匀的性能和更好的表面质 本发明热轧卷取温度控制在 590 ±40°C之间。 提高卷取温度可以降低 热轧基板的硬度， 进而降低最终产品的硬度， 提高最终产品的成形性能， 但是当卷取温度大于 630°C时， 带钢表面氧化铁皮容易增厚， 酸洗困难， 且影响产品表面质量。 当卷取温度低于 550°C时， 热轧中间产品晶粒过小， 并影响到成品组织和性能， 使最终成品的晶粒细小， 强度和硬度增加， 塑 性变差。所以对于本发明使用连续退火生产的 T- 1CA软质镀锡板和 T-2CA 软质镀锡板， 热轧卷取温度控制在 590 ± 40°C时， 卷取后带钢表面氧化铁 皮量较少， 酸洗较为容易， 而且最终产品的表面质量好。 优选的热轧卷取 温度控制在 570°C〜610°C之间， 以获得良好的塑性和更佳的表面质量。
酸洗和冷轧： 可以采用酸轧联合机组生产， 或者先酸洗， 后进行冷连 轧或多次可逆冷轧， 但最好采用酸轧联合机组生产， 以提高生产效率。 酸 洗时应根据机组的酸洗能力， 调整机组速度， 保证酸洗效果。 冷轧为五机 架连轧时， 冷轧总压下率为 82 %〜92 %。冷轧变形量将影响材料的力学性 能， 而且适宜的冷轧变形量便于轧硬材尺寸精度的保证和板形的控制。 变 形量太小则材料成型性差， 变形量太大则冷轧生产消耗增加且轧硬材板形 差， 影响后续连退工序的高速稳定通板。
连续退火： 本发明使用连续退火生产 T-1CA软质镀锡板和 T-2CA软 质镀锡板， 退火温度为 720°C〜770°C， 保温时间为 25s〜50s。 优选的退火 温度为 735 °C〜765 C。虽然采用罩式退火也能生产出软质镀锡板， 但罩式 退火工艺生产的镀锡产品大卷头、 中、 尾的力学性能不均匀， 其产品板形 和表面质量远不如连续退火生产的软质鍍锡板。本发明采用钛一 IF钢连续 退火生产 T-1CA软质镀锡板和 T-2CA软质镀锡板， 其产品力学性能均匀， 产品表面质量好，可以较好地满足用户要求，因而具有较强的市场竞争力。 当退火温度高于 770°C时， 由于带钢材质软， 当带钢较宽且厚度又较薄时， 带钢在退火炉内很容易发生瓢曲甚至断带， 同时能量消耗也将增加； 退火 温度低于 720°C时， 在正常的连续退火机组速度下难以确保钢板完成再结 晶， 产品硬度增高， 同时产品成型性能变差。 本发明使用钛 -IF 钢连续退 火生产软质镀锡板， 比使用铌一 IF钢连续退火生产软质镀锡板的退火温度 要低 （根据模拟退火试验结果， 铌一 IF 钢的退火温度应达到 750°C〜800 °C才能确保充分再结晶） ， 因此在生产计划编排时可以减少过渡卷的用量 和升、 降温的时间， 提高生产效率， 降低生产成本， 而且由于温度的降低， 大幅度降低了带钢在退火炉内发生瓢曲和断带的几率。 保温时间和退火温 度是相互影响的， 提高退火温度便于缩短保温时间， 但是保温时间不能小 于 25s， 否则再结晶晶粒长大不充分， 材质偏硬， 同时机组生产速度太高 时带钢容易跑偏。 保温时间又不能太长， 保温时间超过 50s时， 由于连退 机组速度太低， 一方面生产效率降低， 另一方面晶粒长得太大， 材质偏软 而且在退火炉内带钢很容易瓢曲甚至断带。
平整： Ti一 IF钢再结晶完成之后的平整变形量对材质性能影响很大， 随着变形量的增加， 强度和硬度明显增加。 本发明使用连续退火生产的 T-1CA软质镀锡板，退火后采用双机架平整，平整延伸率控制在 0.8%〜1.8 %之间， 而对于 T-2CA软质镀锡板， 其平整延伸率控制在 1.8%〜3.0%之 间， 上述 T-1CA和 T-2CA平整延伸率范围可以根据产品的厚薄再作适当 的调整， 带钢较薄时采用较小的平整延伸率， 带钢较厚时采用较大的平整 延伸率。
镀锡： 本发明使用连续退火生产的 T-1CA软质镀锡板和 T-2CA软质 镀锡板， 采用与普通镀锡板相同的镀锡工艺即可生产。
本发明采用钛一 IF钢生产软质镀锡板，在本发明的化学成份范围内不 仅不会发生时效问题， 而且对热轧工艺参数不敏感。 本发明采用钛一 IF钢 生产的软质镀锡板比用铌一 IF钢生产的软质镀锡板再结晶温度低，不仅炉 子热能消耗低， 正常生产时温度过渡时间短， 过渡卷或返回卷的用量也将 减少， 因此可以降低生产成本， 而且带钢在连续退火炉内退火时不易发生 瓢曲， 通板性能好， 断带风险小。 本发明釆用钛一 IF钢生产的软质镀锡板 比用铌一 IF钢生产的软质镀锡板具有更稳定的力学性能。 另外， 本发明的 软质镀锡板， 在保证材质性能均匀的前提条件下热轧釆用较低的终轧温度 和卷取温度， 热轧后带钢表面氧化铁皮少， 随后的酸洗很容易进行， 最终 产品的表面质量好。 具体实施方式
以下是本发明生产软质镀锡板的实例说明。
实例 1一 6: T— 1CA软质镀锡板， 釆用钛一 IF钢生产， 钢水经 RH精 炼真空脱气处理， 并采用了多种控制夹杂物的措施， 最后经常规连铸工艺 生产连铸坯， 钢水的化学成分如表 2所示， 钢中还含有其它不可避免的杂 质元素， 余量为 Fe。
表 2 实例 1一 6的基板化学成分实绩， Wt%
Figure imgf000009_0001
连铸坯在热轧前加热到热轧开坯温度， 经粗轧、 精轧及层流冷却后卷 取， 经 2〜3天室温冷却后经 CDCM机组 （酸洗和冷连轧联合机组） 生产 冷轧板。 具体工艺参数见表 3 : 表 3 实例 1一 6的主要工艺参数实绩
Figure imgf000010_0001
将冷轧带钢在 CAPL机组 （连续退火和平整机组） 进行退火、 平整 然后进行常规镀锡生产镀锡板， 退火工艺参数、 平整延伸率和最终产品 硬度如表 4所示。
表 4 实例 1一 6的退火工艺参数、 平整延伸率和产品硬度实绩
Figure imgf000010_0002
最终产品的力学性能如表 5所示。 表 5 实例 1一 6的力学性能实绩
Figure imgf000011_0001
实例 7-12: Τ— 2CA软质镀锡板， 采用钛一 IF钢生产， 钢水经 RH精 炼真空脱气处理， 并釆用了多种控制夹杂物的措施， 最后经常规连铸工艺 生产连铸坯， 钢水的化学成分如表 6所示， 钢中还含有其它不可避免的杂 质元素， 余量为 Fe。
表 6 实例 7-12的基板化学成分实绩， Wt%
Figure imgf000011_0002
连铸坯在热轧前加热到热轧开坯温度， 经粗轧、 精轧及层流冷却后卷 取， 经 2〜3天室温冷却后经 CDCM机组 （酸洗和冷连轧联合机组） 生产 冷轧板。 具体工艺参数见表 7 : 表 7 实例 7-12的主要工艺参数实绩
Figure imgf000012_0001
将冷轧带钢在 CAPL机组 （连续退火和平整机组） 进行退火、 平整， 然后进行常规镀锡生产镀锡板， 退火工艺参数、 平整延伸率和产品硬度如 表 8所示。
表 8 实例 7-12的退火工艺参数、 平整延伸率和产品硬度实绩
Figure imgf000012_0002
最终产品的力学性能如表 9所示。 表 9 实例 7-12的力学性能实绩
条件应 均匀延 镀锡板成品 编 抗拉强度 屈服延伸 断裂延
力 0 0.2 伸率 硬度 表面 号 (MPa) 率 YPE1(% ) 伸率（％)
(Mpa) (% ) HRT30T 质量
7 275 363 22 0 38 53.1 更优
261 359 23 0 39 52.8 更优
270 357 23 0 39 53.6 优 0 278 367 21 0 37 54.6 优
1 1 273 359 22 0 38 54.6 优
12 279 368 21 0 37 55.1 优

Claims

权 利 要 求
1.软质镀锡板， 其成分为 （重量百分比） ：
0.006%,
Μη: 0· 10〜0.20%，
Al : 0.025— 0.075%,
Si^ O.03%,
Ti: 0.03〜0.08%，
P^ O.015%,
S^ O.015%,
N^ O.003% ,
0 0.004%，
余量为 Fe和不可避免的杂质元素。
2.根据权利要求 1所述的镀锡板， 其特征在于， C含量为 0.004%。
3.根据权利要求 1 所述的镀锡板， 其特征在于， 所述 A1 含量为
0.030%〜 0.060%。
4.根据权利要求 1所述的镀锡板，其特征在于，所述 Ti含量为 0.05%〜 0.07%。
5.根据权利要求 1所述的镀锡板， 其特征在于， 用连续退火的方法来 生产所述镀锡板。
6.根据权利要求 1所述的软质镀锡板的制造方法， 包括如下步骤： 炼 钢→连铸 ~ 热轧→酸轧联合→连续退火→平整→镀锡。
7.根据权利要求 6所述的方法， 其特征在于， 所述酸轧联合的步骤通 过釆用酸洗和冷连轧联合机组完成。
8.根据权利要求 6所述的方法， 其特征在于， 所述酸轧联合的步骤可 由先酸洗后进行冷连扎或多次可逆冷轧的步骤代替。
9.根据权利要求 6-8任意一项所述的方法， 其特征在于， 在所述热轧 步骤中， 板坯出炉温度控制在 1 190°C〜1250°C之间， 终轧温度控制在 880
°C〜920°C之间； 卷取温度控制在 550°C〜630°C之间。
10.根据权利要求 9所述的方法， 其特征在于， 在所述热轧步骤中， 终 轧温度控制在 885 °C〜915 °C之间； 卷取温度控制在 570°C〜610°C之间。
11.根据权利要求 6-8任意一项所述的方法， 其特征在于， 在所述冷轧 的步骤中， 冷轧变形量控制在 82%〜92%之间。
12. 根据权利要求 6-8任意一项所述的方法， 其特征在于， 在所述连 续退火的步骤中， 退火温度控制在 720°C〜770°C之间， 保温时间控制在 25s〜50s之间。
13. 根据权利要求 12所述的方法， 其特征在于， 所述退火温度控制在 735°C〜765°C之间。
14. 根据权利要求 6-8任意一项所述的方法， 其特征在于， 所述平整 步骤采用单机架或双机架完成。
15. 根据权利要求 6-8任意一项所述的方法， 其特征在于， 在所述平 整步骤中， 平整延伸率为 0.8%〜3.0%。
16. 根据权利要求 15所述的方法， 其特征在于， 生产硬度 HR30T为 49±3的软质镀锡板时， 所述平整延伸率控制在 0.8%〜1.8%之间。
17. 根据权利要求 15所述的方法， 其特征在于， 生产硬度 HR30T为 53±3的软质镀锡板时， 所述平整延伸率控制在 1.8%〜3.0%之间。
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