WO2014015822A1 - 一种搪玻璃用高强度钢板及其制造方法 - Google Patents

一种搪玻璃用高强度钢板及其制造方法 Download PDF

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WO2014015822A1
WO2014015822A1 PCT/CN2013/080153 CN2013080153W WO2014015822A1 WO 2014015822 A1 WO2014015822 A1 WO 2014015822A1 CN 2013080153 W CN2013080153 W CN 2013080153W WO 2014015822 A1 WO2014015822 A1 WO 2014015822A1
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steel sheet
steel
strength steel
glass
strength
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French (fr)
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孙全社
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/04—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a steel grade and a method of manufacturing the same, and more particularly to a steel sheet for glass lining and a method of producing the same. Background technique
  • high-strength steel sheets for glass-lined glass are mainly used in the fields of chemical industry, petroleum, medicine, pesticides, food and water environment, and their main purpose is to serve as a substrate for glass-lined equipment in these fields.
  • a vitreous enamel containing a high silica component is first coated on the surface of a steel substrate, and then after high-temperature sintering, the enamel is firmly adhered to the surface of the steel substrate to become a composite product, and the composite product is Glassware.
  • the glass-lined equipment has the dual advantages of glass stability and metal toughness, has good wear resistance, and has good corrosion resistance to various acidic solutions and organic solvents, and also has an alkaline solution. Certain corrosion resistance.
  • Scale explosion is a defect that often occurs in the process of glass boring.
  • the scale explosion is mainly caused by the fact that the crystallization glass of the enamel glass is reacted with iron and carbon on the surface of the steel sheet to form atomic hydrogen, and the hydrogen atoms diffuse into the steel.
  • the solubility of hydrogen in the steel drops sharply. If there is not enough hydrogen absorption place in the steel, the hydrogen will escape in a large amount, and the surface area of the steel plate will gather to a certain extent to break the surface of the enamel with great pressure, resulting in scale explosion. Peel off.
  • the scale explosion is caused by the release of hydrogen on the surface of the steel plate during the cooling of the coating. There are many factors that can cause scale explosion in enamel products, but the quality of the steel plate itself has a great influence on the scale explosion.
  • the poor adhesion is mainly manifested by the small bonding force between the steel plate and the porcelain layer, and the porcelain layer is easily peeled off. Due to the different crystal structure of the steel sheet and the porcelain layer, especially for the bismuth glass, the higher the silica component in the enamel makes the adhesion between the steel sheet and the porcelain layer more difficult. Poor adhesion can affect the service life of glass-lined equipment to a large extent. There are many factors that can affect the adhesion performance, including the steel sheet itself, the composition of the enamel and the firing process, which have a significant impact on the adhesion properties. Pinhole defects are caused by bubbles generated at the interface between the steel sheet and the porcelain layer during the calcination process, which also impairs the corrosion resistance and insulation of the glass-lined equipment.
  • Japanese Patent Publication No. JP2006037215A published on Feb. 9, 2006, entitled "An Enamel Steel Sheet with Good Adhesion Enamel, Manufacturing Method and Enamel Product", discloses a cold seal with good adhesion.
  • Rolled enamel steel the main chemical composition mass distribution ratio is: C 0.07%, Si 0.50, Mn: 0.010-0.95%, P ⁇ O.020%, 0.080%, Al ⁇ 0.20%, N ⁇ O.070%
  • the enamel steel is designed with a low carbon content and is added with more than one of precious metals such as copper, cobalt, molybdenum and/or nickel, and the precious metal is added in a relatively high amount.
  • the publication number is CN1966753A, and the publication date is May 23, 2007.
  • the Chinese patent document entitled "A hot-rolled double-sided enamel steel sheet and a manufacturing method thereof" discloses a steel sheet for hot-rolled enamel, by adding titanium, And control it to: 0.08 ⁇ 0.20%, and Ti/C: 2.2 ⁇ 5, and optionally add 0.015 ⁇ 0.060% of V and / or: 0.05 ⁇ 0.20% of Cr, which is mainly characterized by adding higher content. Titanium controls the ratio of titanium to carbon.
  • the announcement number is CN 101586210A, and the publication date is November 25, 2009.
  • the Chinese patent document entitled "High-strength enamel steel and its production and burning process" relates to a high-strength enamel steel, which uses 0.020. ⁇ 0.050% bismuth and 0.05 ⁇ 0.30% molybdenum alloying elements, and control the ratio of bismuth and molybdenum addition, ⁇ lONb ⁇ Mo and 0.30 10Nb+Mo 0.50, the enamel steel is suitable for making utensils, Sanitary ware and home appliance industry.
  • the steel plate for adding titanium enamel in the prior art mainly relies on adding a relatively high content of titanium, generally the addition amount of titanium is more than 0.05%, and titanium nitride, titanium carbide, etc. are formed in the steel to improve the anti-scale explosion performance.
  • An object of the present invention is to provide a high-strength steel sheet for bismuth glass and a method for producing the same, which should have good resistance to scale explosion, adhesion and weldability, and should have high strength and good plasticity. .
  • the present invention provides a high-strength steel sheet for bismuth glass, which is designed to have a chemical element mass percentage of: C: 0.06 to 0.15%, Si: 0.15 to 0.50%, Mn: 0.5 to 1.5%, P ⁇ O.02%, S: 0 ⁇ 008 ⁇ 0 ⁇ 035%, A1: 0 ⁇ 001 ⁇ 0 ⁇ 05%, ⁇ : 0 ⁇ 003 ⁇ 0 ⁇ 015%, 0: 0 ⁇ 001 ⁇ 0 ⁇ 035%, Ti: 0 ⁇ 001 ⁇ 0 ⁇ 05%, Cu ⁇ O.10%, Cr ⁇ O.10%, Ni ⁇ O.10%, Mo 0.10%, the balance is Fe and other unavoidable impurities, of which Ti (%) XN (%) 3 X 10
  • the high-strength steel sheet for bismuth glass further includes at least one of Ca and Mg elements, and satisfies Ca + Mg 0.005 wt%.
  • the high-strength steel sheet for the bismuth glass has an A1 element content of 0.001 to 0.03%.
  • the microstructure of the high-strength steel sheet for bismuth glass according to the present invention is ferrite + pearlite, or ferrite + pearlite + celite, or ferrite + bainite, and has steel Finely dispersed titanium-containing compounds.
  • composition principle of each chemical element in the high-strength steel sheet for bismuth glass according to the present invention is as follows: Carbon: Carbon is a key element for ensuring the strength of the steel sheet. The increase in carbon content can increase the strength of the steel sheet, but it will reduce the plasticity and toughness of the steel sheet. For the technical solution, if the microstructure of ferrite + pearlite, ferrite + pearlite + bainite or ferrite + bainite is to be obtained, the carbon content should not be too low or too high. Guarantee the proper amount.
  • the carbon content is controlled to be 0.06 to 0.15%.
  • Silicon plays a role in solid solution strengthening in steel. Silicon can also improve the resistance to high temperature deformation, which is beneficial to improve the softening resistance of steel sheets during high temperature enamel firing. However, when the silicon content is too high, not only the plasticity of the steel is poor, but also the subsequent welding process. Therefore, the silicon content of the present invention is set to 0 ⁇ 15 to 0 ⁇ 50%.
  • Manganese is an inexpensive strengthening matrix element. The main purpose of adding manganese is to increase the strength of the steel, but too high a manganese content will seriously reduce the plasticity of the steel. Manganese also acts as a deoxidizer in steel together with aluminum and silicon. The amount of manganese added depends mainly on the strength level of the steel sheet. In the present invention, the content of manganese should be controlled at 0.5 to 1.5%.
  • Sulfur In the absence of titanium steel, the inclusion of sulfur in the steel and the formation of manganese and other plastic inclusions of manganese sulfide will damage the transverse plasticity and toughness of the steel. Therefore the sulfur content should be as low as possible. However, in the addition of titanium steel, the formation of long strips of manganese sulfide inclusions can be avoided by the addition of titanium. Therefore, the present invention requires that the content of S be: 0 ⁇ 008 ⁇ 0 ⁇ 035%. Phosphorus: Phosphorus is an element that seriously impairs the plasticity and toughness of steel sheets. It is also an inevitable impurity element in steel, so phosphorus is controlled at 0.02%.
  • Aluminum is a strong deoxidizing element. Aluminum and oxygen form alumina inclusions that are poorly ductile. In order to avoid excessive formation of alumina inclusions in the steel, the aluminum content is controlled to be 0.001 to 0.05%. The preferred aluminum content is from 0.001 to 0.03%.
  • Titanium is an element that forms strong carbonitrides. Adding an appropriate amount of titanium to steel helps to fix the nitrogen in the steel. The titanium nitride formed can make the austenite grains not grow excessively when the billet is heated. The original austenite grain size is obtained. Titanium can also form compounds such as TiC, TiS, Ti 4 C 2 S 2 with carbon and sulfur in steel, which are present in the form of inclusions and second phase particles. The precipitate of carbonitride bonded to titanium can also prevent grain growth in the heat-affected zone during soldering and improve its solderability.
  • the titanium content is controlled to be 0.001 to 0.05%
  • the nitrogen content is controlled to be 0.003 to 0.015%
  • Oxygen is an inevitable element in steel and an essential element in the formation of oxides. Excessive oxygen levels can cause excessive oxide inclusions in the steel, which can impair the plasticity and toughness of the steel. Therefore, the present invention controls oxygen at 0.001 to 0.035%.
  • Copper, Chromium, Nickel and Molybdenum Traces of copper, chromium, nickel and molybdenum help to improve the adhesion between the steel and porcelain layers and improve the anti-scale performance of steel. Nickel also improves the low temperature impact resistance of steel sheets. However, excessive levels of copper, chromium, nickel and molybdenum will not only increase production costs, but also hinder the reaction between the steel sheet and the porcelain layer, which will reduce the adhesion performance. Therefore, it is considered to comprehensively control copper, chromium, nickel and molybdenum to 0.10%.
  • Calcium and magnesium can control the inclusion of manganese sulfide in a spherical shape, avoiding the formation of simple strips of manganese sulfide, which is beneficial to improve the lateral plasticity and toughness of the steel sheet.
  • the amount of calcium + magnesium added should be controlled
  • the present invention also provides a method of manufacturing the above-described high-strength steel sheet for glass-lined glass, comprising the following steps:
  • casting can be carried out by continuous casting or die casting to ensure uniform composition of the slab The surface quality is good. If the die casting method is adopted, the die-cast steel ingot needs to be rolled into a steel slab by the preliminary rolling mill;
  • water cooling and air cooling are performed during the cooling process.
  • titanium precipitates in the form of a compound and is uniformly distributed in the matrix in a finely dispersed state.
  • the ferrite structure in the steel is refined. If the cooling rate is too high, it is not conducive to the analysis of titanium compounds, and it is easy to form martensite transformation. Therefore, the average cooling rate of the water cooling is controlled to 10 to 50 ° C / s, and the final cooling temperature is 550 to 700 ° C.
  • the present invention has the following beneficial effects by adopting the above technical solutions:
  • the manufacturing method of the present invention obtains a uniform austenitizing structure by heating at a temperature of 1100 to 1250 ° C, controlling the total rolling reduction ratio of the rolling, the finishing rolling temperature, and the water cooling parameters after the rolling. Partially dissolving the titanium compound to achieve fine grain strengthening, phase transformation strengthening and precipitation strengthening of the steel sheet, improving the strength of the steel sheet, and having good low temperature toughness;
  • the high-strength steel sheet for bismuth glass according to the present invention has good anti-scale, adhesion and weldability, and is suitable for manufacturing enamel products by double-sided enamel process, and remains high after being simmered.
  • the strength is better to meet the pressure requirements of enamel products.
  • Fig. 1 is a photograph showing a metallographic structure of a steel sheet after water cooling at a cooling rate of WV/s according to an embodiment of the present invention.
  • the high-strength steel sheet for bismuth glass of the present invention is produced according to the following procedure (the chemical distribution ratio of each steel strip in the embodiment AH is shown in Table 1, and the detailed process parameters of the high-strength steel sheet for the bismuth glass in the embodiment AH are shown in Table 2) :
  • the slab or slab is heated at 1100 ⁇ 1250 °C and then multi-pass rolling in the austenite recrystallization zone, the total reduction rate is 50%, and the controlled finishing temperature is 800 ⁇ 920 °C.
  • the steel plate of 2 ⁇ 18 ⁇ is rolled by a hot strip mill, and for a steel plate with a thickness of 8mm, it is rolled by a single-stand thick plate mill;
  • Example 1 is a photograph of the metallographic structure of a steel sheet after cooling at a cooling rate of 10 ° C / s in Example H of the present invention. It can be seen from Fig. 1 that after the steel having a carbon content of 0.08% is cooled by an average cooling rate of 10 ° C / s after hot rolling, the microstructure in the steel is ferrite plus a small amount of pearlite.
  • 2 is a photograph showing the metallographic structure of the steel sheet after cooling at a cooling rate of 30 ° C / s in Example C of the present invention. It can be seen from FIG. 2 that the steel having a carbon content of 0.08% is subjected to an average of 30 ° C / s after hot rolling. After the cooling rate is cooled, the structure in the steel is ferrite plus a small amount of pearlite plus a small amount of bainite. Table 1. Chemical composition (mass percentage, wt%) of high strength steel sheet for bismuth glass in Example AH

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Abstract

一种搪玻璃用高强度钢板，其化学元素质量百分含量配比为：C：0.06～0.15%，Si：0.15～0.50%，Mn：0.5～1.5%，P≤0.02%，S： 0.008∼0.035%，Al：0.001～0.05%，N：0.003～0.015%，O：0.001～0.035%，Ti：0.001～0.05%，Cu≤0.10%，Cr≤0.10%，Ni≤0.10%，Mo≤0.10%，余量为Fe和其他不可避免的杂质，其中Ti×N≤0.0003%。相应地，还提供了该搪玻璃用高强度钢板的制造方法。该搪玻璃用高强度钢板具有较高的强度、良好的塑性，还具有良好的抗鳞爆性、密着性和焊接性等综合力学性能。

Description

一种搪玻璃用高强度钢板及其制造方法 技术领域
本发明涉及钢种及其制造方法， 尤其涉及一种搪玻璃用钢板及其制造方 法。 背景技术
目前， 搪玻璃用高强度钢板主要应用于化工、 石油、 医药、 农药、 食品 及水环境等领域， 其主要用途是作为这些领域中的搪玻璃设备的基板。
搪玻璃工艺是将含有高二氧化硅组份的玻璃质瓷釉先涂覆在钢质基体表 面， 然后经过高温烧结后瓷釉牢固地密着于钢质基体表面而成为复合材料制 品， 该复合材料制品即为搪玻璃制品。 搪玻璃设备具有玻璃的稳定性和金属 的强韧度的双重优点， 其具备良好的耐磨性， 并且对各种酸性溶液和有机溶 剂均有较好的耐腐蚀性， 对碱性溶液也具有一定的耐腐蚀性。
普通钢板在搪玻璃工艺过程中经常会产生鳞爆、密着不良和针孔等缺陷， 严重损害了搪玻璃设备的产品质量和使用性能。
鳞爆是搪玻璃过程中经常出现的缺陷。 鳞爆主要是由于搪玻璃制胚在高 温烧结时， 瓷浆内的结晶水与钢板表面的铁、 碳反应生成原子氢， 氢原子向 钢中扩散。 当钢制品冷却时， 氢在钢中的溶解度急剧下降， 如果钢中没有足 够的吸氢场所， 氢气则会大量逸出， 在钢板表面积聚至一定程度以很大压力 冲破瓷釉表面， 产生鳞爆剥落。 鳞爆的产生就是因为在涂搪冷却时氢气在钢 板表面释放所引起的。 能够导致搪瓷制品产生鳞爆的因素很多， 但是钢板本 身的质量会对鳞爆的产生有着很大的影响。
密着不良主要表现为钢板和瓷层之间的结合力小， 瓷层容易剥落。 由于 钢板和瓷层的晶体结构不同， 特别是对于搪玻璃来说， 瓷釉中的二氧化硅组 份较高使得钢板和瓷层之间的密着更难。 密着不良在很大程度上会影响搪玻 璃设备的使用寿命。 能够影响密着性能的因素很多， 包括钢板本身， 瓷釉的 组成及烧成工艺等都会对密着性能有着明显的影响。 针孔缺陷是在搪烧过程中钢板和瓷层界面产生的气泡造成的， 其同样损 害搪玻璃设备的耐蚀性和绝缘性。
公开号为 JP2006037215A, 公开日为 2006年 2月 9日， 名称为"一种具 有良好附着力搪瓷的搪瓷钢板， 制造方法及其搪瓷产品" 的日本专利文献公 开了是一种密着性良好的冷轧搪瓷钢， 其主要化学成分质量百分配比为： C 0.07%，， Si 0.50， Mn: 0.010-0.95%, P^O.020%, 0.080%, Al<0.20%, N^O.070%, 该搪瓷钢采用了低碳成分设计， 并在加入贵重金属铜、 钴、 钼 和 /或镍中的一种以上， 并且贵金属的加入量较高。
公告号为 CN1966753A, 公开日为 2007年 5月 23日， 名称为 "一种热 轧双面搪瓷用钢板及其制造方法" 的中国专利文献公开了一种热轧搪瓷用钢 板， 通过添加钛， 并将其控制为： 0.08~0.20%， 且 Ti/C: 2.2~5,并且可选择添 加 0.015~0.060 %的 V和 /或： 0.05~0.20%的 Cr， 其特点主要是加入较高含量 的钛并控制钛与碳的比例。
公告号为 CN 101586210A, 公开日为 2009年 11月 25日， 名称为 "高 强度搪瓷用钢及其生产和烧搪工艺" 的中国专利文献涉及了一种高强度搪瓷 用钢， 其采用添加 0.020~0.050%的铌和 0.05~0.30%的钼等合金元素的方法， 并控制铌和钼的加入比例， §Ρ lONb^Mo且 0.30 10Nb+Mo 0.50， 该种搪 瓷用钢适用于制造食具、 卫生洁具和家电行业领域。
另外， 现有技术领域的加钛搪瓷用钢板主要依赖加入较高含量的钛， 一 般钛的加入量在 0.05%以上， 通过钛在钢中形成氮化钛、 碳化钛等来提高抗 鳞爆性能。 发明内容
本发明的目的在于提供一种搪玻璃用高强度钢板及其制造方法， 该搪玻 璃用钢板应当具有良好的抗鳞爆性、 密着性和焊接性， 还应当具有较高的强 度和良好的塑性。
为实现上述目的， 本发明提供了一种搪玻璃用高强度钢板， 其化学元素 质量百分含量设计为： C: 0.06〜0.15%， Si: 0.15〜0.50%， Mn: 0.5〜1.5%， P^O.02%, S: 0·008〜0·035%， A1: 0·001〜0·05%， Ν: 0·003〜0·015%， 0： 0·001〜0·035%， Ti: 0·001〜0·05%， Cu^O.10%, Cr^O.10%, Ni^O.10%, Mo 0.10%,余量为 Fe和其他不可避免的杂质， 其中 Ti (%) XN ( %) 3 X 10
进一歩地，所述搪玻璃用高强度钢板还包括 Ca和 Mg元素中的至少一种， 且满足 Ca+Mg 0.005wt%。
优选地， 所述搪玻璃用高强度钢板中 A1元素含量为 0.001〜0.03%。 更进一歩地， 本发明所述的搪玻璃用高强度钢板的微观组织为铁素体 + 珠光体， 或铁素体 +珠光体 +氏体， 或铁素体 +贝氏体， 钢中具有细小弥散的 含钛化合物。
本发明所述的搪玻璃用高强度钢板中各化学元素的成分设计原理如下： 碳： 碳是确保钢板强度的关键元素。 含碳量增加， 可以提升钢板强度， 但是会降低钢板的塑性和韧性。 对于本技术方案来说， 如果要获得铁素体 + 珠光体、 铁素体 +珠光体 +贝氏体或铁素体 +贝氏体的微观组织， 碳含量不能 过低也不能过高， 要保证适当含量。当碳含量过低时， 钢中的珠光体含量低， 强度也低； 当碳含量过高时， 钢中的珠光体含量过高， 珠光体片层粗大且分 布也不均匀。 如果冷却速度过快会在钢板内形成马氏体等组织， 虽然钢板强 度升高了， 但是其塑性和韧性就降低了。 同时， 具有过多的珠光体的钢板在 搪瓷过程中很容易产生针孔等缺陷。 因此， 为了获得良好的组织和强度、 韧 性等综合性能， 碳含量控制在 0.06〜0.15%。
硅： 硅在钢中起到固溶强化的作用， 硅还可以提高抗高温变形能力， 有 利于在高温搪瓷烧成过程中提高钢板的抗软化能力。 但硅含量过高时， 不仅 钢的塑性较差， 也不利于后续焊接工艺的进行。 故将本发明硅含量设定为 0· 15〜0·50%。
锰： 锰是廉价的强化基体元素。 加入锰的主要目的是： 提高钢的强度， 但锰含量过高会严重降低钢的塑性。 锰在钢中还和铝、 硅元素共同起到脱氧 的作用。 锰的加入量主要取决于钢板的强度级别。 在本发明中， 锰的含量应 控制在 0.5〜1.5%。
硫： 在不加钛钢中， 硫在钢中与锰等化合形成的塑性夹杂物硫化锰会损 害钢的横向塑性和韧性。 因此硫的含量应尽可能地低。 但在加钛钢中， 通过 添加钛元素可以避免形成长条状的硫化锰夹杂。 所以， 本发明要求 S的含量 为: 0·008〜0·035%。 磷： 磷是严重损害钢板的塑性和韧性的元素， 可也是钢中不可避免的杂 质元素， 因此磷控制在 0.02%。
铝： 铝是强脱氧元素。 铝和氧会形成延展性很差的氧化铝夹杂物。 为了 避免钢中形成过多的氧化铝夹杂物， 因此将铝含量控制在 0.001〜0.05%。 优 选的铝含量在 0.001〜0.03%。
钛和氮： 钛是形成强碳氮化物的元素， 在钢中加入适量的钛有利于固定 钢中的氮， 形成的氮化钛能使钢坯加热时奥氏体晶粒不过分长大， 细化原始 奥氏体晶粒度。钛在钢中还可分别与碳和硫生成 TiC、 TiS、 Ti4C2S2等化合物， 它们以夹杂物和第二相粒子的形式存在。 与钛结合的碳氮化物的析出物在焊 接时还可阻止热影响区晶粒长大， 改善其焊接性能。 但是当钛含量过高时， 钛会优先和氮形成粗大的氮化钛夹杂物， 这些夹杂物会严重损害钢的塑性和 韧性。因此，在本发明中将钛含量控制在 0.001〜0.05%，氮含量控制在 0.003〜 0.015%且 Ti (%) XN (%) 3 X 10-4。
氧： 氧是钢中不可避免的元素， 也是形成氧化物的必要元素。 氧含量过 高会造成钢中的氧化物夹杂物过多， 会损害钢的塑性和韧性。 因此本发明将 氧控制在 0.001〜0.035%。
铜、 铬、 镍和钼： 微量的铜、 铬、 镍和钼有利于提高钢板和瓷层之间的 密着性能， 改善钢的抗鳞爆性能。 镍还可以提高钢板的耐低温冲击性能。 但 铜、 铬、 镍和钼元素含量过高， 不但会增大生产成本， 还会阻碍钢板与瓷层 之间的反应， 会降低密着性能。 因此， 综合考虑将铜、 铬、 镍和钼均控制在 0.10%。
钙和镁： 钙和镁元素可控制硫化锰夹杂呈球形， 避免形成单纯的长条状 硫化锰， 有利于改善钢板横向的塑性和韧性。 钙 +镁的加入量应控制在
0.005%。
相应地， 本发明还提供了上述搪玻璃用高强度钢板的制造方法， 包括以 下歩骤：
( 1 )冶炼和真空脱气： 确保钢液的基本成分要求， 除去钢中的氢气等有 害气体， 并加入锰、 钛等必要的合金元素， 通过锰元素来提高钢板的强度， 通过钛元素来细化原始奥氏体晶粒度， 同时进行合金元素的调整；
(2)铸造：铸造可以采用连铸或模铸的方式以保证铸坯内部成分均匀和 表面质量良好，如果采用模铸的方式，模铸的钢锭还需经初轧机轧制成钢坯;
( 3 ) 将连铸坯或钢坯于 1100〜1250°C加热后在奥氏体再结晶区进行多 道次轧制， 总压下率 50%， 控制终轧温度为 800〜920°C ; 连铸坯或钢坯在 1100〜1250°C的温度下加热， 一方面可以获得均匀的奥氏体化组织， 另一方 面可以使钛的化合物部分溶解；
(4) 对轧后钢板进行水冷， 水冷的平均冷却速率为 10〜50°C/s ， 终冷 温度为 550〜700°C ;
( 5 ) 空冷。
在本技术方案中， 冷却过程中水冷和空冷。 在冷却过程中， 钛会以化合 物的形式析出， 呈细小弥散状态均匀地分布在基体中。 同时通过控制冷却， 钢中的铁素体组织得到细化。 冷速过高， 不利于钛的化合物充分析出， 也容 易形成马氏体转变。 因此， 将水冷的平均冷却速率控制为 10〜50°C/s ， 而终 冷温度为 550〜700°C。
与现有技术相比， 本发明通过采用上述技术方案， 使得其具有下列有益 效果：
( 1 )本技术方案中的搪玻璃用高强度钢板的屈服强度（Rp。.2或 ReL) ^
345MPa, 抗拉强度 （Rm) ^455MPa, 延伸率 A5。 20%;
(2 ) 本发明的制造方法通过在 1100〜1250°C的温度下加热、 控制轧制 的总压下率和终轧温度及轧后冷却的水冷参数， 既获得均匀的奥氏体化组织 又使钛的化合物部分溶解， 使钢板实现细晶强化、 相变强化和析出强化， 提 高了钢板的强度， 具有良好的低温韧性；
( 3 )本发明所述的搪玻璃用高强度钢板， 具有良好的抗鳞爆性、密着性 和焊接性， 适用于以双面搪瓷工艺制造搪瓷制品， 而且在经过搪烧以后仍然 保持较高的强度， 更好地满足搪瓷制品的耐压要求。 附图说明
图 1为本发明实施例 H经冷却速度为 WV/s水冷后钢板的金相组织照 片。
图 2为本发明实施例 C经冷却速度为 30V/S水冷后钢板的金相组织照 片。 具体实施方式
以下根据实施例 A-H， 来对本发明的技术方案作进一歩的具体说明。 按照下述歩骤制造本发明的搪玻璃用高强度钢板（实施例 A-H中各钢带 的化学成分配比见表 1， 实施例 A-H中搪玻璃用高强度钢板的详细工艺参数 见表 2 ) :
( 1) 将钢水进行转炉吹炼和真空脱气处理；
(2 ) 连铸或模铸， 模铸的钢锭需轧制成钢坯；
( 3 ) 将钢坯或铸坯于 1100〜1250°C加热后在奥氏体再结晶区进行多道 次轧制，总压下率 50%，控制终轧温度为 800〜920°C，对于厚度为 2〜18匪 的钢板， 采用热连轧机轧制， 对于厚度为 8mm 的钢板， 采用单机架的厚板 轧机轧制；
(4) 对轧后钢板进行水冷， 水冷的平均冷却速率为 10〜50°C/s ， 终冷 温度为 550〜700°C ;
( 5 ) 空冷。
由表 1和表 2可见， 采用上述的成分设计和工艺参数进行冶炼和加工， 其成品钢板的延伸率大于 30%， 具有较高的屈服强度和抗拉强度， 经采用上 述的搪玻璃瓷釉和烧成工艺进行双面搪瓷， 没有发生鳞爆现象， 钢板和瓷釉 的密着性均达到 II级以上， 表明具有优良的密着性能， 完全满足制造搪瓷制 品如化工反应罐、 水处理罐等的成形、 焊接、 搪瓷等加工要求， 制品具有较 高的耐压能力， 具有广泛的应用价值和市场前景。
另外，图 1为本发明实施例 H经冷却速度为 10°C/s水冷后钢板的金相组 织照片。 从图 1可以看出， 0.08%碳含量的钢在热轧后经 10°C/s的平均冷却 速率冷却后， 钢中的组织为铁素体加少量珠光体。 图 2为本发明实施例 C经 冷却速度为 30°C/s水冷后钢板的金相组织照片从图 2可以看出， 0.08%碳含 量的钢在热轧后经 30°C/s的平均冷却速率冷却后， 钢中的组织为铁素体加少 量珠光体加少量贝氏体。 表 1.实施例 A-H中搪玻璃用高强度钢板的化学成分（质量百分含量， wt% )
Figure imgf000008_0001
表 2.实施例 A-H 搪玻璃用高强度钢板的的工艺参数和力学性能
Figure imgf000008_0002

Claims

权利要求书
1. 一种搪玻璃用高强度钢板， 其特征在于， 其化学元素质量百分含量为： C: 0·06〜0·15%， Si: 0·15〜0·50%， Μη: 0·5〜1·5%， Ρ^Ο.02%, S: 0.008-0.035%, Α1: 0·001〜0·05%， Ν: 0·003〜0·015%， 0： 0·001〜0·035%， Ti: 0.00卜 0.05%， Cu^O.10%, Cr^O.10%, Ni^O.10%, Mo ^0.10%, 余量为 Fe和其他不可避免的杂质， 其中 Ti (%) XN (%) 3X104。
2. 如权利要求 1 所述的搪玻璃用高强度钢板， 其特征在于， 还包括 Ca和 Mg元素中的至少一种， 且满足 Ca+Mg 0.005wt%。
3. 如权利要求 1所述的搪玻璃用高强度钢板， 其特征在于， A1元素含量为 0.001〜0·03%。
4. 如权利要求 1或 2所述的搪玻璃用高强度钢板，其特征在于，其微观组织 为铁素体 +珠光体。
5. 如权利要求 1或 2所述的搪玻璃用高强度钢板，其特征在于，其微观组织 为铁素体 +珠光体 +贝氏体。
6. 如权利要求 1或 2所述的搪玻璃用高强度钢板，其特征在于，其微观组织 为铁素体 +贝氏体。
7. 如权利要求 1或 2所述的搪玻璃用高强度钢板的制造方法，包括下列歩骤：
1) 冶炼和真空脱气；
2) 铸造；
3) 将钢坯或铸坯于 1100〜1250°C加热后在奥氏体再结晶区进行多道次 轧制， 总压下率 50%， 控制终轧温度为 800〜920°C;
4) 对轧后钢板进行水冷， 水冷的平均冷却速率为 10〜50°C/s ， 终冷温度 为 550〜700°C;
5) 空冷。
8. 如权利要求 7所述的制造方法， 其特征在于， 所述歩骤 （1) 中的铸造方 法为连铸或模铸。
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* Cited by examiner, † Cited by third party
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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0499844A (ja) * 1990-08-13 1992-03-31 Nkk Corp グラスライニング機器用鋼板
CN101353758A (zh) * 2007-07-23 2009-01-28 宝山钢铁股份有限公司 一种双面搪瓷用热轧高强度钢板及其制造方法
CN101370952A (zh) * 2006-01-18 2009-02-18 新日本制铁株式会社 搪瓷加工产品以及瓷釉
CN102766822A (zh) * 2012-07-27 2012-11-07 宝山钢铁股份有限公司 一种搪玻璃用高强度钢板及其制造方法
CN102796955A (zh) * 2011-05-25 2012-11-28 宝山钢铁股份有限公司 搪瓷钢用热轧中厚板及其制造方法

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4332086B2 (ja) * 2004-07-30 2009-09-16 新日本製鐵株式会社 ホーロー密着性が良好なホーロー用鋼板およびその製造方法並びにホーロー製品
CN100473742C (zh) * 2006-04-29 2009-04-01 宝山钢铁股份有限公司 静电搪瓷用热轧细晶粒钢及其制造方法
WO2008035528A1 (fr) * 2006-09-19 2008-03-27 Nippon Steel Corporation Pièces à émailler et produits émaillés

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0499844A (ja) * 1990-08-13 1992-03-31 Nkk Corp グラスライニング機器用鋼板
CN101370952A (zh) * 2006-01-18 2009-02-18 新日本制铁株式会社 搪瓷加工产品以及瓷釉
CN101353758A (zh) * 2007-07-23 2009-01-28 宝山钢铁股份有限公司 一种双面搪瓷用热轧高强度钢板及其制造方法
CN102796955A (zh) * 2011-05-25 2012-11-28 宝山钢铁股份有限公司 搪瓷钢用热轧中厚板及其制造方法
CN102766822A (zh) * 2012-07-27 2012-11-07 宝山钢铁股份有限公司 一种搪玻璃用高强度钢板及其制造方法

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