WO2018001019A1 - 一种磷化性能优异的冷轧低密度钢板及其制造方法 - Google Patents
一种磷化性能优异的冷轧低密度钢板及其制造方法 Download PDFInfo
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- 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
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- 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
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
- 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
- C21D8/0273—Final recrystallisation annealing
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
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- 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
Definitions
- the present invention relates to a cold rolled steel sheet and a method for producing the same, and more particularly to a cold rolled steel sheet excellent in phosphating performance and a method for producing the same.
- the path to achieve lightweight vehicles from the material point of view is: use light alloys such as aluminum and magnesium instead of steel; use higher-strength steel instead of traditional low-strength steel to achieve material thinning; increase the specific strength of steel by reducing the density of steel, ie Develop low density steel.
- the publication number is CN104220609A, and the publication date is December 17, 2014.
- the Chinese patent document entitled "High-strength non-clearral low-density steel and the preparation method of the steel” discloses a high-strength non-clear gap. Density steel and its preparation method, in order to reduce the density, the steel has an Al content of 6-9%.
- the Chinese Patent Publication No. CN101755057A published on June 23, 2010, entitled “Low Density Steel with Good Compressibility", discloses a hot rolled ferritic steel sheet in which Al is The content is 6% ⁇ Al ⁇ 10%.
- the materials used in auto parts are usually phosphatized to form a phosphate film on the metal surface.
- the normal phosphating film is porous, uniform and fine, and the coating penetrates into the pores. It increases the adhesion of the coating, and at the same time has the corrosion resistance during the electrophoresis of the electrophoretic paint and enhances the electrophoresis effect. Therefore, the phosphating film becomes a good bottom layer which is indispensable for the coating, and the quality of the coating cannot be ensured without the phosphating or phosphating effect.
- the alloying elements will enrich the surface of the annealed steel sheet to form an oxide film, which is not conducive to the uniform reaction of the phosphating process, and is easy to cause low phosphating coverage and coarse phosphating crystals. Defects such as looseness do not meet the requirements of automobile manufacturing. Poor phosphating performance is also high strength steel plate Common problems in car manufacturing.
- the controlled annealing process is another way to improve the phosphating performance of high-strength steels.
- drawbacks in the prior art for example, the control of the annealing process cannot be applied to most continuous annealing lines, or the process parameters for annealing production are difficult, for example, the atmosphere dew point is controlled below -45 ° C, or the annealing process step is increased. Increased production costs.
- the prior art mainly solves the adverse effect on the phosphating performance of the surface enrichment of the Si and Mn elements in the improvement of the phosphating performance of the high-strength steel, and the mass percentage of the Al element in the steel sheet is usually ⁇ 1%.
- One of the objects of the present invention is to provide a cold-rolled low-density steel sheet excellent in phosphating performance, which has a low density by controlling the mass percentage of Al element, and forms an iron particle layer by controlling oxidation of the surface of the steel sheet. It has high strength and excellent phosphating performance, thereby solving the technical problem that the prior art has high Al element content and excellent phosphating performance.
- the present invention provides a cold rolled low density steel sheet excellent in phosphating performance, the surface of the cold rolled low density steel sheet having an iron particle layer having dispersed iron particles therein;
- the cold rolled low density steel sheet contains an Al element having a mass percentage of 3.0 to 7.0%.
- the design principle of the Al element is that the Al element is a ferrite forming element.
- the addition of the Al element can significantly lower the density of the steel sheet, and therefore, in the present invention, the mass percentage of the Al element is not less than 3.0%.
- the mass percentage of the Al element exceeds 7.0%, which inhibits the formation of austenite.
- the Al element can significantly increase the stacking fault energy of austenite in the steel, and thus the mass percentage of the Al element exceeds 7.0%. It is suppressed that the retained austenite in the steel is induced to undergo martensite transformation during deformation, so that it is difficult to obtain good strength and plasticity matching of the steel sheet.
- the present invention defines the mass percentage of the Al element to be 3.0 to 7.0%. Further, the surface of the cold-rolled low-density steel sheet according to the present invention has an iron particle layer which can solve the problem of phosphating of low-density steel when the Al content is high.
- the inner side of the iron particle layer has an inner oxide layer adjacent to the iron particle layer, and the inner oxide layer contains an oxide of Al.
- the formation of external oxidation of Al 2 O 3 is suppressed by controlling the dew point of the annealing atmosphere, and is converted into internal oxidation of the inner oxide layer while being on the surface of the steel sheet. Iron particles are formed, thereby solving the problem of phosphating of cold-rolled high-strength low-density steel.
- the inner oxide layer further contains an oxide of Mn.
- the inner oxide layer has a thickness of 0.2 to 10 ⁇ m.
- the thickness of the inner oxide layer is less than 0.2 ⁇ m, the external oxidation of the Al element cannot be more effectively suppressed, and when the thickness of the inner oxide layer is >10 ⁇ m, The forming property of the secondary surface layer of the steel sheet is affected, and therefore, preferably, the thickness of the inner oxide layer is controlled to be 0.2 to 10 ⁇ m.
- the oxide in the inner oxide layer exists in the grain boundary and the crystal.
- the oxide in the inner oxide layer is mainly an oxide of Al and an oxide of Mn, and the oxide is simultaneously distributed inside the grain and at the grain boundary position in the inner oxide layer.
- the thickness of the iron particle layer is smaller than the thickness of the inner oxide layer.
- the iron particle layer has a thickness of 0.1 to 5 ⁇ m.
- the present invention defines the iron particle layer to have a thickness of 0.1 to 5 ⁇ m.
- the iron particle layer of the cold-rolled low-density steel sheet according to the present invention has a thickness of 0.3 to 3 ⁇ m.
- the iron particles have a particle diameter of 0.1 to 5 ⁇ m.
- the present invention defines that the iron particles have a particle diameter of 0.1 to 5 ⁇ m.
- the iron particles cover the surface of the steel sheet More than 30% of the area.
- the present invention defines that the iron particles cover an area of 30% or more of the surface of the steel sheet.
- the spacing between adjacent iron particles is not more than 10 times the average particle diameter of the iron particles.
- the phosphating may cause non-phosphating at intervals between the iron particles. Accordingly, preferably, the present invention defines that the spacing between adjacent iron particles does not exceed a maximum of 10 times the average particle size of the iron particles.
- the microstructure of the steel sheet is ferrite and retained austenite.
- the ratio of the retained austenite is 6 to 30%.
- the mass percentage of the C element in the retained austenite is not less than 0.8%.
- C is an important solid solution strengthening element to promote austenite formation, and in low-density steel rich in Al element, if retained in austenite
- mass percentage of C is less than 0.8%, the content and mechanical stability of retained austenite are relatively low, and thus the strength and ductility of the steel sheet are low. Therefore, the C content in the retained austenite of the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention is not less than 0.8%.
- the density is less than 7,500 kg/m3, so that the cold-rolled low-density steel has a low density and a light weight, and is suitable for use in the manufacture of automobile structural members.
- the chemical element mass percentage is: C: 0.25 to 0.50%, Mn: 0.25 to 4.0%, Al: 3.0 to 7.0%, and the balance is Fe. And other inevitable impurities.
- the inevitable impurities are mainly S, P and N elements, and can control P ⁇ 0.02%, S ⁇ 0.01%, N ⁇ 0.01%.
- C is an important solid solution strengthening element that promotes austenite formation.
- the C mass percentage is less than 0.25%, the retained austenite content and mechanical stability are relatively low, so the strength and ductility of the steel sheet are low; when the C mass percentage is higher than 0.5%, the lamellar layer Carbides and carbide particles distributed at the grain boundaries of the ferrite are coarse, thereby reducing the rolling deformation ability of the steel sheet. Therefore, the present invention controls the C mass percentage to be 0.25 to 0.50%.
- Mn can increase the stability of austenite, reduce the critical cooling rate of steel during quenching and improve the hardenability of steel. Mn also improves the work hardening properties of steel, thereby increasing the strength of the steel sheet. However, too high Mn content will cause Mn segregation in the slab and obvious band-like structure distribution in the hot-rolled sheet, thereby reducing the ductility and bending properties of the steel sheet; and too high Mn content tends to cause the hot-rolled sheet to be cold. Cracks occur during rolling deformation. Therefore, the present invention controls the mass percentage of Mn to be 0.25 to 4.0%.
- the Al element is a ferrite forming element.
- the addition of the Al element can significantly lower the density of the steel sheet, and therefore, in the present invention, the mass percentage of the Al element is not less than 3.0%. However, the mass percentage of the Al element exceeds 7.0%, which inhibits the formation of austenite.
- the Al element can significantly increase the stacking fault energy of austenite in the steel, and thus the mass percentage of the Al element exceeds 7.0%. It is suppressed that the retained austenite in the steel is induced to undergo martensite transformation during deformation, so that it is difficult to obtain good strength and plasticity matching of the steel sheet. Therefore, the present invention defines the mass percentage of the Al element to be 3.0 to 7.0%.
- P is a solid solution strengthening element; however, P increases the cold brittleness of the steel, reduces the plasticity of the steel, and deteriorates the cold bending property and the welding property. Therefore, the present invention defines a P mass percentage ⁇ 0.02%.
- S:S causes the steel to be hot brittle, reduces the ductility and toughness of the steel, deteriorates the weldability, and reduces the corrosion resistance of the steel. Accordingly, the present invention defines an S mass percentage of ⁇ 0.01%.
- N:N forms AlN with Al, and can refine columnar dendrites during solidification.
- the N content is too high, the formed coarse AlN particles affect the ductility of the steel sheet.
- excess AlN reduces the thermoplasticity of the steel. Accordingly, the invention defines N mass percent ⁇ 0.01%.
- At least one of Si, Ti, Nb, V, Cr, Mo, Ni, Cu, B, Zr, and Ca may be selectively added.
- the elongation is >25% and the tensile strength is >800 MPa.
- Another object of the present invention is to provide a method for producing a cold-rolled low-density steel sheet according to the above aspect, which is capable of producing a cold-rolled low-density steel sheet having any of the above-described phosphating properties.
- the present invention provides a method of manufacturing a cold rolled low density steel sheet according to any of the above, comprising the steps of:
- the soaking temperature and the holding time of the continuous annealing in the step (5) are mainly selected to form an iron particle layer on the surface of the steel sheet after continuous annealing.
- the soaking temperature is controlled at 750°C-950°C, and the holding time is limited to 30-600s, because: if the soaking temperature is lower than 750°C and the holding time is lower than 30s, Markov in the cold-rolled low-density steel plate matrix
- the austenite reverse phase transformation has not fully formed austenite grains, and the carbides in the cold rolled low density steel plate steel matrix have not been completely dissolved to form austenite grains, and the strip of high temperature iron cannot fully perform dynamic recrystallization.
- the iron particle layer on the surface of the annealed steel sheet is not sufficiently formed, and the phosphating performance is inferior.
- the soaking temperature is higher than 950 ° C and the holding time is higher than 600 s
- the austenite grains in the matrix structure of the steel sheet are coarsened after the soaking treatment, and the austenite stability in the steel is reduced, thereby causing the residual in the steel sheet matrix after annealing.
- the solid content is reduced and the retained austenite stability is also reduced.
- the mechanical properties of the steel sheet after annealing deteriorate.
- the iron particle size on the surface of the steel sheet after annealing is too large, and the thickness of the inner oxide layer is too thick. It is not conducive to the surface forming properties of the steel sheet.
- the formation of the iron particle layer in the present technical solution is also closely related to the dew point of the annealing atmosphere defined in the technical solution, and the formation of the external oxidation of Al 2 O 3 is suppressed by controlling the dew point of the annealing atmosphere of the continuous annealing, and is converted into Internal oxidation of the inner oxide layer causes iron particles to form on the surface of the steel sheet.
- the annealing atmosphere is all reductive to Fe, and thus the iron oxide is reduced.
- the dew point of the annealing atmosphere is lower than -15 ° C, the above annealing atmosphere is still oxidized to the Al element in the steel matrix, and Al in the steel matrix forms a continuous dense Al 2 O 3 film on the surface of the steel sheet, thereby affecting the phosphating performance. . If the dew point of the annealing atmosphere is higher than +20 ° C, the oxygen potential in the annealing atmosphere is too high, and the ability of O atoms to diffuse into the steel matrix is increased, and the inner oxide layer is too thick on the surface of the steel sheet and alloy elements such as Al and Mn, affecting the steel sheet. Formability of the surface.
- the holding time in the step (5) is 30-200 s.
- the soaking time is limited to 30-200 s.
- the heating temperature is 1000-1250 ° C
- the holding time is 0.5-3 h
- the finishing temperature is 800-900 ° C.
- the hot rolled sheet is taken up at a temperature of 500 to 750 °C.
- the heating temperature in the step (2) is limited to 1000 to 1250 ° C because the heating temperature exceeds 1250 ° C, which may result in
- the slab of the steel sheet is over-fired, and the coarse grain structure in the slab leads to a decrease in hot workability, and the ultra-high temperature causes severe decarburization on the surface of the slab;
- the heating temperature is lower than 1000 ° C, the slab is descaled by high-pressure water and initially After rolling, if the finishing temperature is too low, the deformation resistance of the slab is too large, and it is difficult to manufacture a steel sheet having neither surface defects nor a predetermined thickness.
- the holding time is limited to 0.5-3 h in the step (2) because the holding time exceeds 3 h, which causes the sheet of the steel sheet.
- the grain structure in the billet is large and the surface of the slab is decarburized seriously.
- the holding time is less than 0.5 h, and the inside of the slab is not even.
- the finishing rolling temperature is defined in the step (2) at 800-900 ° C in order to complete hot rolling of the slab, and final rolling If the temperature is too low, the deformation resistance of the slab is too high, so that it is difficult to manufacture hot-rolled steel sheets and cold-rolled steel sheets having the required thickness specifications and no surface and edge defects; in addition, for the present invention, when the finish rolling temperature is lower than At 800 ° C, the hot-rolled strip-shaped high-temperature ferrite inside the slab cannot be sufficiently recovered and recrystallized to be refined. Since the plate temperature will naturally drop during the hot rolling process after the slab is released, it is difficult to control the finish rolling temperature to be higher than 900 °C.
- the hot-rolled sheet is wound at a temperature of 500 to 750 ° C, and if the coiling temperature is higher than 750 ° C, It is easy to cause flat rolls, and the microstructure non-uniformity of the head, middle, and tail materials of the hot rolled coil is increased; if the coiling temperature is lower than 500 ° C, the high tensile strength of the hot rolled coil may cause difficulty in cold rolling.
- the cold rolling reduction is 30 to 90%.
- the cold rolling reduction is defined in the step (4) in order to perform cold rolling deformation on the hot-rolled steel sheet after pickling.
- the cold rolling reduction of >30% can increase the austenite formation rate during the subsequent annealing process, help to form the deformed high-temperature ferrite and improve the uniformity of the annealed steel sheet, thereby improving the ductility of the annealed steel sheet.
- the cold rolling reduction is >90%, and the deformation resistance of the material is very high due to work hardening. It is extremely difficult to prepare a cold-rolled steel sheet having a predetermined thickness and a good plate shape. Therefore, the cold rolling reduction of the cold rolled low density steel sheet according to the present invention is controlled to be 30 to 90%.
- the cold rolling reduction is 50-80%.
- the atmosphere of the heating section and the holding section is a mixed gas of N 2 and H 2 , wherein the volume content of H 2 is 0.5-20%.
- the volume content of H 2 is 1-5%.
- the annealing atmosphere has a dew point of -10 to 0 °C.
- the heating rate is 1-20 ° C / s
- the cooling rate after soaking is 1-150 ° C / s.
- the cooling rate after soaking is selected to be 1-150 ° C / s, preferably the cooling rate is 10-50. °C / s, the selection of the cooling rate needs to avoid the decomposition of austenite during the cooling process.
- the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention has excellent phosphating performance because it has an iron particle layer;
- the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention is excellent in mechanical properties, and has an elongation of >25% and a tensile strength of >800 MPa.
- Fig. 1 is a schematic view showing the structure of a cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention.
- Fig. 2 is a cross-sectional metallographic structure of a cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention.
- Fig. 3 is a surface scanning electron microscope secondary electron image of Example A2 of the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention.
- Figure 4 is a view showing the surface of Example A7 of the cold rolled low density steel sheet excellent in phosphating performance according to the present invention; Scanning electron microscope secondary electron image.
- Fig. 5 is a surface scanning electron microscope secondary electron image of Comparative Example B1 of the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention.
- Fig. 6 is a surface SEM low-power backscattered electron image of Example A2 of the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention after phosphating.
- Fig. 7 is a high-order secondary electron image of a surface scanning electron microscope after phosphating of Example A2 of the cold-rolled low-density steel sheet having excellent phosphating performance according to the present invention.
- Fig. 8 is a surface-scanning electron microscope low-power backscattered electron image of a comparatively-prepared B1 of a cold-rolled low-density steel sheet having excellent phosphating performance according to the present invention after phosphating.
- Fig. 9 is a high-order secondary electron image of a surface scanning electron microscope after phosphating of Comparative Example B1 of a cold-rolled low-density steel sheet having excellent phosphating performance according to the present invention.
- Fig. 1 shows the structure of a cold rolled low-density steel sheet excellent in phosphating performance according to the present invention.
- the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention comprises a steel substrate 1, an iron particle layer 3 on the surface of the steel sheet, and an inner layer of the iron particle layer having an inner oxide layer 2 in close proximity to the iron particle layer.
- Fig. 2 is a view showing a cross-section metallographic structure of a cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention.
- the formation of external oxidation of the iron particle layer 3 on the surface of Al 2 O 3 is suppressed by controlling the dew point of the annealing atmosphere, and It is converted into internal oxidation of the inner oxide layer 2, and at the same time, iron particles are formed on the surface of the steel sheet, and after phosphating, a surface having uniform appearance and complete coverage of the phosphate film can be obtained.
- the thickness of the inner oxide layer 2 is 0.2-10 ⁇ m, and the oxide of the inner oxide layer 2 exists in the grain boundary and the crystal, the thickness of the iron particle layer 3 is smaller than the thickness of the inner oxide layer, and the thickness of the iron particle layer 3 is 0.1. -5 ⁇ m.
- Table 1 lists the mass percentages of the chemical elements of the cold-rolled low-density steel sheets excellent in the phosphating performance of Examples A1 to A16 and the conventional steel sheets of B1-B6.
- Table 2 lists the cold-rolled low-density steel sheets excellent in phosphating performance in Examples A1 to A16 and
- Figure 3 shows a surface scanning electron microscope secondary electron image of Example A2.
- Figure 4 shows a surface scanning electron microscope secondary electron image of Example A7.
- Figure 5 shows a surface SEM secondary electron image of Comparative Example B1.
- FIG. 3 and Fig. 4 iron particles were present on the surfaces of Examples A2 and A7, except that the iron particles of Example A2 were sufficiently grown, and the gap between the iron particles was small, while the iron particles of Example A7 were not. When fully grown, the gap between the iron particles is large.
- the soaking time of the embodiment A2 is longer than the soaking time of the embodiment A7. Therefore, the soaking time of the present invention is preferably 30-200 s. .
- Figure 5 shows the surface electron microscope secondary electron image of Comparative Example B1. A layer of Al 2 O 3 film was observed on the surface, but no iron particles were observed, and the surface topography was completely different from that shown in Figure 3 and Figure 4. In the examples, the cross-section metallographic pattern revealed that no iron particle layer and an inner oxide layer were formed.
- Table 3 lists the respective performance parameters of the cold rolled low density steel sheets excellent in the phosphating performance and the conventional steel sheets rolled in the B1-B6 in Examples A1 to A16.
- the phosphating performance is tested by randomly selecting 10 500-fold fields of view to observe the phosphating film on the surface of the phosphating steel sheet under scanning electron microscopy, and using the image software to measure the coverage of the phosphating film. If the average coverage of the phosphating film in the field of view is ⁇ 75%, it is judged that the phosphating performance is good (indicated by ⁇ ), and if the average coverage of the phosphating film in 10 fields of view is ⁇ 75%, it is judged that the phosphating performance is poor. (with X table Show).
- Fig. 6 is a surface SEM low-power backscattered electron image of Example A2 of the cold-rolled low-density steel sheet excellent in phosphating performance according to the present invention after phosphating.
- Fig. 7 is a high-order secondary electron image of a surface scanning electron microscope after phosphating of Example A2 of the cold-rolled low-density steel sheet having excellent phosphating performance according to the present invention.
- Fig. 8 is a surface-scanning electron microscope low-power backscattered electron image of a comparatively-prepared B1 of a cold-rolled low-density steel sheet having excellent phosphating performance according to the present invention after phosphating.
- Fig. 9 is a high-order secondary electron image of a surface scanning electron microscope after phosphating of Comparative Example B1 of a cold-rolled low-density steel sheet having excellent phosphating performance according to the present invention.
- the phosphating of Example A2 was observed to be uniform at a low magnification of the scanning electron microscope, and further, As can be seen from the high power microscope shown in Fig. 7, the phosphate film in Example A2 completely covered the surface of the steel sheet, and the phosphating crystal was uniform. As shown in Fig. 8, the phosphating unevenness of Comparative Example B1 can be seen under the low magnification observation of the scanning electron microscope, in which the black region is a position having phosphating crystals, the white region is a position where no phosphating crystal is formed, and surface phosphating is performed. The coverage is low, and the image after further enlargement is shown in Fig. 9. As can be seen from Fig. 9, the surface of Comparative Example B1 has only partial phosphating crystals.
- the dew point of the annealing atmosphere of the embodiment is -15 ° C to +20 ° C, which can promote the conversion of Al element from external oxidation to internal oxidation within the above dew point range, avoiding the formation of continuous dense Al 2 O on the surface of the steel sheet of the example.
- Effects of phosphate film 3, and a thickness of 0.2-10 ⁇ m is formed such that the Al oxide layer is an element in the steel. Since the iron particle layer was present in the surface layer of the steel sheet of the example, when the steel sheet of the example was phosphatized, it was equivalent to phosphating on the surface of ordinary mild steel.
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Abstract
Description
C | Mn | Al | Si | N | S | P | |
成分I | 0.37 | 1.1 | 4.1 | 0.31 | 0.0025 | 0.002 | 0.004 |
成分II | 0.45 | 2 | 6.1 | - | 0.0040 | 0.003 | 0.007 |
成分III | 0.34 | 2.8 | 5.2 | - | 0.0027 | 0.003 | 0.007 |
Claims (21)
- 一种磷化性能优异的冷轧低密度钢板,其特征在于:所述冷轧低密度钢板的表面具有铁颗粒层,所述铁颗粒层中具有分散的铁颗粒;所述冷轧低密度钢板含有质量百分含量为3.0~7.0%的Al元素。
- 如权利要求1所述的冷轧低密度钢板,其特征在于,所述铁颗粒层内侧具有紧邻铁颗粒层的内氧化层,所述内氧化层中含有Al的氧化物。
- 如权利要求2所述的冷轧低密度钢板,其特征在于,所述内氧化层中还含有Mn的氧化物。
- 如权利要求2或3所述的冷轧低密度钢板,其特征在于,所述内氧化层的厚度为0.2-10μm。
- 如权利要求2或3所述的冷轧低密度钢板,其特征在于,所述内氧化层中的氧化物存在于晶界和晶内。
- 如权利要求2或3所述的冷轧低密度钢板,其特征在于,所述铁颗粒层的厚度小于内氧化层的厚度。
- 如权利要求1所述的冷轧低密度钢板,其特征在于,所述铁颗粒层的厚度为0.1-5μm。
- 如权利要求1所述的冷轧低密度钢板,其特征在于,所述铁颗粒的粒径为0.1-5μm
- 如权利要求1所述的冷轧低密度钢板,其特征在于,所述铁颗粒覆盖钢板表面30%以上的面积。
- 如权利要求1所述的冷轧低密度钢板,其特征在于,相邻铁颗粒之间的间距最大不超过铁颗粒平均粒径的10倍。
- 如权利要求1所述的冷轧低密度钢板,其特征在于,所述钢板的微观组织为铁素体和残余奥氏体。
- 如权利要求11所述的冷轧低密度钢板,其特征在于,所述残余奥氏体的相比例为6-30%。
- 如权利要求11或12所述的冷轧低密度钢板,其特征在于,所述残余奥氏体中C元素的质量百分含量不低于0.8%。
- 如权利要求1所述的冷轧低密度钢板,其特征在于,其密度<7500kg/m3。
- 如权利要求1或14所述的冷轧低密度钢板,其特征在于,其化学元素质量百分含量为:C:0.25~0.50%,Mn:0.25~4.0%,Al:3.0~7.0%,余量为Fe和其他不可避免的杂质。
- 如权利要求15所述的冷轧低密度钢板,其特征在于,其延伸率>25%,抗拉强度>800MPa。
- 如权利要求1-16中任意一项所述的冷轧低密度钢板的制造方法,其特征在于,包括步骤:(1)冶炼和铸造;(2)热轧;(3)酸洗;(4)冷轧;(5)连续退火:加热至均热温度750-950℃后保温30-600s,退火气氛的露点为-15℃~20℃,然后将经过均热的带钢冷却后卷取。
- 如权利要求17所述的冷轧低密度钢板的制造方法,其特征在于,在所述步骤(2)中,加热温度为1000-1250℃,保温时间为0.5-3h,终轧温度800-900℃,然后在500-750℃的温度下卷取热轧板。
- 如权利要求17所述的冷轧低密度钢板的制造方法,其特征在于,在所述步骤(4)中,冷轧压下量为30-90%。
- 如权利要求17所述的冷轧低密度钢板的制造方法,其特征在于,在所述步骤(5)中,加热段和保温段的气氛采用N2和H2混合气体,其中H2的体积含量为0.5-20%。
- 如权利要求17所述的冷轧低密度钢板的制造方法,其特征在于,在所述步骤(5)中,加热的速率为1-20℃/s,均热之后的冷却速度为1-150℃/s。
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US16/304,947 US11371112B2 (en) | 2016-06-28 | 2017-05-26 | Cold-rolled low-density steel sheet having excellent phosphorability, and manufacturing method therefor |
KR1020187031774A KR102163179B1 (ko) | 2016-06-28 | 2017-05-26 | 우수한 인수용성을 갖는 냉간 압연 저밀도 강철 판, 및 이의 제조 방법 |
EP17819016.1A EP3476967B1 (en) | 2016-06-28 | 2017-05-26 | Cold-rolled low-density steel plate having excellent phosphorization performance, and manufacturing method therefor |
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KR102319479B1 (ko) * | 2020-12-10 | 2021-10-29 | 경상국립대학교산학협력단 | 페라이트계 경량 철강의 제조방법 및 이를 이용한 페라이트계 경량 철강 |
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