KR100957946B1 - High strength bake hardening cold rolled steel sheet having excellent surface quality and manufacturing method thereof - Google Patents

Abstract

The present invention relates to a high-strength quenched hardened steel sheet used as a material for automobiles, and to a high-strength cold-rolled steel sheet and a method of manufacturing the same by improving the quench hardening characteristics by adjusting the carbon content to an appropriate amount and finely distribute the precipitates. This cold rolled steel sheet is, in weight%, C: 0.0005 to 0.004%, Si: 0.02 to 0.6%, Mn: 0.2 to 0.8%, P: 0.005 to 0.2%, S: 0.003 to 0.02%, Al: 0.01 to 0.08% , N: 0.004% or less (not including 0%), Cu: 0.005 ~ 0.2%, and the content of Mn, Cu, S satisfies 5≤0.27 * (Mn + Cu) / S≤25 It is composed of the remaining Fe and other unavoidable impurities, including one or two or more precipitates selected from the group consisting of MnS, CuS, (Mn, Cu) S, and the average size of the precipitates is 0.2㎛ or less. In addition, the present invention also provides a method for producing this cold rolled steel sheet.

Cold Rolled Steel, Hardening Hardening, High Strength, Plastic Anisotropy Index, (Mn, Cu) S, CuS

Description

High hardness hardened cold rolled steel sheet with excellent surface quality and manufacturing method {HIGH STRENGTH BAKE HARDENING COLD ROLLED STEEL SHEET HAVING EXCELLENT SURFACE QUALITY AND MANUFACTURING METHOD THEREOF}

The present invention relates to a high-strength cold-rolled steel sheet used as a material for automobiles, and more particularly, to control the amount of carbon in the grains by controlling the distribution of fine precipitates while controlling the carbon content to an appropriate amount, the surface hardening type high strength cold rolled steel having excellent surface quality It relates to a steel sheet and a method of manufacturing the same.

In order to improve the dent resistance, exterior hardening type cold rolled steel sheets are frequently used for exterior materials such as automobiles. A small hardened type cold rolled steel sheet is a steel having a high yield point by allowing an appropriate amount of solid solution carbon to remain in the steel sheet and using solidified heat of the coated sheet to fix the potential generated during press molding.

There are Al-Killed steel and IF steel (Interstitial Free Steel).

In the case of Al-Killed steel, which is an ordinary annealing material, a small amount of solid carbon remains, and it has a hardening hardening capacity of about 10 to 20 Mpa after the quenching treatment while securing aging characteristics. The upper annealing material has the disadvantages of low yield strength and low productivity after baking.

In the case of IF steel, Ti and Nb are added to completely precipitate the carbon or nitrogen dissolved in the steel to improve moldability. The hardening hardening characteristic is given to the IF steel by hardening. The baking hardening type IF steel controls the adding amount of Ti or Nb and the adding amount of carbon so that an appropriate amount of carbon remains in the steel to give the baking hardening characteristic. In the case of small hardening IF steel, in order to employ an appropriate amount of carbon, not only the amount of carbon added, but also the amount of Ti or Nb added, as well as the amount of sulfur and nitrogen that react with Ti and Nb to form precipitates are controlled within a very narrow range. Since it is difficult to secure stable quality, and when Ti or Nb is added, the recrystallization temperature is high, so high temperature annealing is required.

Conventional steel that has improved the hardening hardening properties using fine precipitates has advantages in terms of hardening hardening properties and manufacturing costs, but when manufactured by the method, surface defects occur in automotive steel sheets.

It is an object of the present invention to provide a high strength cold rolled steel sheet and a method of manufacturing the same, which have a hardening characteristic and do not cause surface defects by controlling solid solution carbon in grains by adding precipitates without Ti and Nb.

Cold rolled steel sheet of the present invention for achieving the above object, in weight%, C: 0.0005 ~ 0.004%, Si: 0.02 ~ 0.6%, Mn: 0.2 ~ 0.8%, P: 0.005 ~ 0.2%, S: 0.003 ~ 0.02 %, Al: 0.01 ~ 0.08%, N: 0.004% or less (not including 0%), Cu: 0.005 ~ 0.2%, the content of Mn, Cu, S is 5≤0.27 * (Mn + Cu Satisfies) / S ≦ 25, is composed of the remaining Fe and other unavoidable impurities, and includes one or two or more precipitates selected from the group consisting of MnS, CuS, (Mn, Cu) S, and the average size of the precipitates. It is characterized by consisting of 0.2 μm or less.

Further, the method for producing a cold rolled steel sheet of the present invention, in weight%, in weight%, C: 0.0005 to 0.004%, Si: 0.02 to 0.6%, Mn: 0.2 to 0.8%, P: 0.005 to 0.2%, S: 0.003 ~ 0.02%, Al: 0.01 ~ 0.08%, N: 0.004% or less (not including 0%), Cu: 0.005 ~ 0.2%, and the content of Mn, Cu, S is 5≤0.27 * (Mn + Cu) / S≤25, reheating the steel composed of the remaining Fe and other unavoidable impurities to a temperature of 1100 ~ 1300 ℃, hot rolling with the finish rolling temperature above Ar3 transformation point, and 300 ~ 1000 ℃ / After cooling at a rate of min, wound at a temperature of 500 ~ 750 ℃, cold rolling at a reduction ratio of 30 ~ 90%, and continuous annealing for 10 seconds to 30 minutes in the temperature range of 500 ~ 900 ℃ It is characterized by.

The cold rolled steel sheet provided according to the present invention has a higher yield strength and a higher bake hardening value than the same tensile strength class, and thus yields high bake yield strength, and has excellent workability and secondary machinability, and does not cause surface defects. Is also excellent.

Hereinafter, the present invention will be described in detail.

The present inventors have discovered the following new facts in the course of research to improve the baking hardening properties without adding Ti and Nb. By controlling the carbon content to an appropriate amount and finely distributing the precipitates, the yield strength of the post-loading is greatly increased in high yield strength steels. This is based on the study that the fine precipitates of MnS, CuS and (Mn, Cu) S affect the amount of solid carbon in the grains.

As shown in FIG. 1, the finer the precipitates, the smaller the amount of the dissolved carbon in the grains. In view of this fact, the present inventors confirmed that the carbon content of the cold rolled steel sheet in the range of 0.0005 to 0.004% has a hardening hardening characteristic in consideration of the content of solid solution carbon in the grains controlled by the size of the precipitate. Carbon is precipitated around the finely distributed precipitates, which do not cause aging at room temperature, and are believed to significantly increase yield strength by dissolving carbon in coating heat treatment. To this end, the carbon content should be adjusted to 0.0005 to 0.004%, and can be stably secured when the average size of precipitates of MnS, CuS, and (Mn, Cu) S is 0.2 μm or less.

Paying attention to these new facts, we have studied how to finely distribute MnS, CuS, and (Mn, Cu) S. As a result, (1) the content of Mn, Cu, S was adjusted under the following conditions 0.5 * (Mn + Cu, while the content of Mn was 0.2-0.8%, the content of S 0.003-0.02%, and the content of Cu was 0.005-0.2%. ) / S: 5-20, it is necessary to adjust it. (2) If the cooling rate is over 300 ℃ / min after rolling, the average of precipitates of MnS, CuS, (Mn, Cu) S The size is less than 0.2㎛ fine.

As such, by adjusting the content of carbon and the size of precipitates according to the present invention, the secondary processing brittleness is also excellent while securing the hardening hardening property. When the precipitate becomes fine, an appropriate amount of carbon remains in the grain boundary and the grain boundary is strengthened, thereby preventing brittle fracture caused by the weak grain boundary after processing. Furthermore, the present inventors confirmed that in the distribution of MnS, CuS, and (Mn, Cu) S precipitates, fine precipitates are uniformly distributed as MnS and CuS are more uniform than Mn and Cu composite precipitates, resulting in better processability. It was. That is, when the ratio of 0.27 * (Mn + Cu) / S is in the range of 2.7 to 3.9, the more the precipitates of MnS and CuS are added than the composite precipitates of (Mn, Cu) S, the larger the number of precipitates is, the better the workability is. .

Hereinafter, the composition range of the cold rolled steel sheet of the present invention will be described in detail.

The content of carbon (C) is preferably 0.0005 to 0.004%.

If the content of carbon (C) is less than 0.0005%, the amount of hardening in steel is small, and if it is more than 0.004%, the moldability is drastically reduced.

The content of silicon (Si) is preferably 0.02 to 0.6%.

Silicon is a solid solution strengthening element of steel, which has lower elongation reduction rate compared with other elements, and has excellent powdering characteristics when plating, but when it is added more than 0.6%, the amount of red scale is large, and the pickling characteristics deteriorate rapidly. As the surface defects increased, the upper limit was set to 0.6%, and the lower limit was set to 0.02% because the strengthening effect and the powdering property were not improved when added below 0.02%.

The content of manganese (Mn) is preferably 0.2 to 0.8%.

Manganese is known as an element that precipitates solid sulfur in steel as MnS to prevent hot shortness caused by solid sulfur. In the present invention, when the content of manganese and sulfur is appropriate, very fine MnS is precipitated, and carbon precipitates around the precipitate, and the precipitated carbon is dissolved in the coating hardening process to enhance yield strength. It is preferable to make the content of 0.2 to 0.8%. If the manganese content is less than 0.2%, the amount of S remaining in the solid solution state is high, so the amount of FeS generated during reheating increases the probability of surface defects. When the content of manganese is 0.2% or more, the above-mentioned effect is not only exhibited, and there are no surface defects, and when the content of manganese is more than 0.8%, manganese has a high content of coarse MnS precipitates, resulting in poor hardening characteristics. Become

The content of phosphorus (P) is preferably 0.005 to 0.2%.

Phosphorus is an element having a high solid solution strengthening effect and a small decrease in the r value (plastic anisotropy index), which guarantees high strength in steels for controlling precipitates according to the present invention. When the content of phosphorus is more than 0.005% to ensure the strength, in the case of more than 0.2% ductility is lowered to limit the upper limit to 0.2%.

The content of sulfur (S) is preferably 0.003 ~ 0.02%.

When the content of sulfur (S) is less than 0.003%, the amount of precipitates of MnS, CuS, and (Mn, Cu) S is small, and the precipitates are very coarse in size, so that the hardening hardening characteristic is not good. If the sulfur content is more than 0.02%, the content of solute sulfur is large, so the ductility and formability are greatly lowered, and there is a fear of red brittleness.

The content of aluminum (Al) is preferably 0.01 to 0.08%.

Aluminum is an element added as a deoxidizer, but in the present invention, nitrogen is added in the steel to prevent formability deterioration due to solid nitrogen. If the aluminum content is less than 0.01%, the amount of solid solution is high, so the moldability is not good. If the aluminum content is more than 0.08%, the amount of aluminum present in the solid solution is high, so the ductility is lowered.

The content of nitrogen (N) is preferably 0.004% or less (not including 0%).

Nitrogen is an element inevitably added during steelmaking, and if it is more than 0.004%, the aging index is increased and moldability is deteriorated, so 0.004% or less is preferable.

The content of copper (Cu) is preferably 0.005 to 0.2%.

Copper forms precipitates of less than 0.2 µm when the ratio of Cu and S content and the cooling rate before winding in the hot rolling process are appropriate, and carbon precipitates around the precipitates, and the precipitated carbon is dissolved and yielded during the coating part treatment. Add 0.005-0.2% based on the study of increasing strength. If the copper content is 0.005% or more, fine precipitation can occur, and if it exceeds 0.2%, the coarsening precipitates poorly.

It is preferable that the weight ratio of said Mn, Cu, and S satisfy | fills 5 <= 0.27 * (Mn + Cu) / S <= 25.

S is combined with Mn and Cu to be precipitated as MnS, CuS, (Mn, Cu) S, and the precipitates vary depending on the amount of Mn, Cu, and S added, resulting in hardening hardening properties, secondary processing brittleness, and plastic anisotropy index. This affects the in-plane anisotropy index. According to the present invention, an effective precipitate is obtained when the addition ratio of Mn, Cu and S (0.27 * (Mn + Cu) / S (wherein the content of Mn, Cu, S is in weight%)) is 5 or more, 25 In the case of excess, the precipitates are coarse, so that the hardening hardening characteristic is not good, and the characteristics of plastic anisotropy index and in-plane anisotropy index are not good.

In the component system of the present invention, the average size of the precipitate is preferably 0.2 µm or less.

According to the results of the present invention, the size of MnS, CuS, (Mn, Cu) S precipitates directly affects the hardening characteristics, secondary processing brittleness, plastic anisotropy index, and in-plane anisotropy index, and the average size of these precipitates. In the case of more than 0.2 µm, the baking hardening characteristic is not good, and the secondary work brittleness, the plastic anisotropy index, and the in-plane anisotropy index are not good. The smaller the size of the precipitate, the greater the number of precipitates in the same amount of precipitation, so that the reinforcing effect is large and advantageous, preferably 0.1 μm or less.

Cold rolled steel sheet of the present invention may further include Mo. The content of such molybdenum (Mo) is preferably 0.01 ~ 0.2%. Molybdenum is added as an element to increase the plastic anisotropy index, the plastic anisotropy index is increased only when the content is more than 0.01%, the plastic anisotropy index does not increase any more it may cause hot brittleness.

Hereinafter, the manufacturing method of the cold rolled steel sheet of this invention is demonstrated concretely.

According to the present invention, MnS, CuS, and (Mn, Cu) having an average size of precipitates of 0.2 μm or less on a cold rolled plate by adjusting control conditions such as hot rolling, cold rolling, and annealing based on a steel material satisfying the above-mentioned emphasis. It is characterized by forming one or two or more precipitates selected from the group consisting of S. The average size of these precipitates in the cold rolled plate is affected by the conditions of addition, reheating temperature, winding temperature, etc., but is directly affected by the cooling rate after hot rolling.

[Hot Rolling Condition]

In the present invention, the steel that satisfies the above-mentioned emphasis is reheated and hot rolled. As for reheating temperature, 1100-1300 degreeC is preferable. If the reheating temperature is less than 1100 ℃, the reheating temperature is low, the coarse CuS produced during the continuous casting is not completely dissolved, the coarse precipitates remain even after hot rolling. If the reheating temperature exceeds 1300 ℃, there is almost no undissolved precipitate, so there is little effect of refining the precipitate due to the temperature rise and the manufacturing cost increases with the temperature rise.

Hot rolling is preferably carried out under the conditions of the finish rolling temperature higher than the Ar3 transformation temperature. If the finish rolling temperature is less than the Ar3 transformation temperature, not only the workability is degraded by the formation of the rolled grain, but also the ductility is greatly reduced.

After hot rolling, the cooling rate before winding is preferably 300 to 1000 ° C / min. According to the present invention, even when the temperature is 5≤0.27 * (Mn + Cu) / S≤25, if the cooling rate is less than 300 ° C / min, the average size of precipitates exceeds 0.2 µm. In other words, as the cooling rate increases, a large number of nuclei are generated and the precipitate becomes fine. In the case of 0.27 * (Mn + Cu) / S exceeding 25, the coarse precipitates undissolved in the reheating process, and even if the cooling rate is fast, the number of new nuclei is generated and the precipitates do not become fine (Fig. 2, 0.0041% C). -0.16% Mn-0.062% P-0.005% S-0.03% Al-0.0025% N-0.11% Cu). Referring to the graph of FIG. 2, the faster the cooling rate, the finer the size of the precipitate is. Therefore, there is no need to limit the upper limit of the cooling rate. However, even if the cooling rate exceeds 1000 ° C./min, the fineness of the precipitate is no longer increased. 300-1000 degreeC / min is more preferable. The upper limit of the cooling rate was set at 1000 ° C./min, and the upper limit was set at 1000 ° C./min since it is almost impossible to have a cooling rate exceeding that of the current equipment. The cooling end temperature is the temperature just before winding up, that is, the temperature immediately before the coil is wound around the winder.

[Coiling condition]

Winding is performed after hot rolling as mentioned above, but winding temperature is preferable 500-750 degreeC. If the coiling temperature exceeds 750 ° C., precipitates grow too coarsely, resulting in poor baking hardening. If the coiling temperature is less than 500 ℃, the solid nitrogen is not completely precipitated by Al, which adversely affects aging. Therefore, the lower limit of the coiling temperature is preferably 500 ℃.

[Cold rolling condition]

Cold rolling is preferably performed at a reduction ratio of 30 to 90%. If the cold reduction rate is less than 30%, since the annealing recrystallization nucleation amount is small, the crystal grains grow too large during annealing, and the strength and formability decrease due to the coarsening of the annealing recrystallization grains. If the cold reduction rate exceeds 90%, the ductility is lowered, it is preferable to limit the upper limit to 90%.

[Continuous Annealing]

Continuous annealing temperature plays an important role in determining the material of the product. In this invention, it is preferable to carry out in the temperature range of 500-900 degreeC. If the continuous annealing temperature is less than 500 ° C., recrystallization is not completed and the target ductility value cannot be secured. If the annealing temperature is higher than 900 ° C., the strength decreases due to coarsening of the recrystallized grains. The continuous annealing time keeps the recrystallization complete. If it is about 10 seconds or more, the recrystallization is completed. Preferably, the continuous annealing time is in the range of 10 seconds to 30 minutes. If the continuous annealing time is less than 10 seconds, the elongation is low, the workability is deteriorated, and if it exceeds 30 minutes, the strength is reduced by coarsening of the crystal grains, so it is limited to the above range.

Hereinafter, the present invention will be described in more detail with reference to Examples.

EXAMPLE

In Table 1, the steel slab was reheated at 1200 ° C, hot rolled to finish, cooled at a rate of 600 ° C / min, and wound up at 650 ° C. The finishing rolling temperature at this time was 910 degreeC above Ar3 transformation point, and continuous annealing was performed by heating at 700 degreeC for 40 second at the speed of 10 degreeC / sec.

The obtained annealing plate was processed into a standard specimen according to ASTM E-8 standard to investigate the mechanical properties. The specimen was measured for yield strength, tensile strength, elongation and plastic anisotropy index (rm value) using a tensile tester (INSTRON, Model 6025). Where rm = (r0 + 2r45 + r90) / 4. The quench hardening properties were measured by applying a 2% strain to the specimens, followed by heat treatment at 170 ° C for 20 minutes, measuring the yield yield of the yield strength, and subtracting the measured yield strength from the original yield strength value as Table BH. Shown in

division Chemical composition (% by weight) 0.27 * (Mn + Cu) / S C Si Mn P S Al N Cu Etc Inventive Steel 1 0.0032 0.05 0.25 0.01 0.01 0.028 0.0012 0.05 - 8.10 Inventive Steel 2 0.0008 0.05 0.29 0.061 0.009 0.061 0.0019 0.11 - 12.00 Invention Steel 3 0.0018 0.32 0.33 0.072 0.012 0.052 0.0021 0.12 - 10.13 Inventive Steel 4 0.0022 0.45 0.72 0.093 0.012 0.041 0.0013 0.08 - 18.00 Inventive Steel 5 0.0018 0.48 0.66 0.072 0.009 0.048 0.0021 0.12 Mo: 0.06 23.40 Comparative Steel 1 0.0015 0 0.14 0.057 0.021 0.029 0.0028 0.08 - 2.83 Comparative Steel 2 0.0062 0.23 0.15 0.058 0.012 0.03 0.0022 0.12 - 6.08 Comparative Steel 3 0.0028 0 0.4 0.07 0.01 0.04 0.0016 0 Ti: 0.022 10.80 Comparative Steel 4 0.0028 0 0.4 0.07 0.01 0.04 0.0016 0 Ti: 0.022 10.80

division Yield strength (MPa) Tensile Strength (MPa) Elongation (%) Plastic anisotropy index (rm) Secondary process brittleness (DBTT- ℃) Sore Hardening Index (MPa) Surface Defects Average size of precipitate (μm) Inventive Steel 1 186 309 49 1.83 -40 58 No occurrence 0.08 Inventive Steel 2 218 358 42 1.79 -40 37 " 0.09 Invention Steel 3 253 403 38 1.73 -50 45 " 0.1 Inventive Steel 4 302 459 33 1.63 -40 42 " 0.13 Inventive Steel 5 298 462 32 1.59 -40 39 " 0.15 Comparative Steel 1 208 352 40 1.77 -40 33 Occur 0.1 Comparative Steel 2 239 361 35 1.39 -50 82 Occur 0.08 Comparative Steel 3 279 402 31 1.39 -10 39 No occurrence 0.38 Comparative Steel 4 202 345 40 1.83 0 32 “ 0.38

Inventive steels 1 to 5 in Tables 1 and 2 have an average size of precipitates of 0.2 μm or less, high strength, a hardening characteristic of 30 MPa or more, excellent workability, and excellent surface quality due to no surface defects.

On the other hand, in the case of Comparative Steel 1, the average size of precipitates was 0.2 µm or less, which was high strength and had a bake hardening characteristic of 30 MPa or more. . Comparative steel 2 has a high carbon content and a low elongation and plastic anisotropy index, which is highly likely to cause breakage during molding, and a surface defect occurs due to a low Mn content.

Comparative steel 3 has a higher yield strength than that of the inventive steel in the same tensile strength class, a very low elongation and a low plasticity preventive rate, and is likely to break during molding. In the case of Ti-added IF steel, it is difficult to secure formability at the same annealing temperature due to the high recrystallization temperature and it is very disadvantageous in terms of cost because it must be annealed at a higher temperature.

Comparative steel 4 is annealing treatment of the same component steels as the sample 7 at a higher temperature of 830 ℃, lower yield strength and lower cure resistance than the same tensile strength class. In addition, the secondary processing brittleness evaluation scale is also known to have a high transition temperature (DBTT) has a high disadvantage that the probability of fracture after molding processing in extreme fat.

1 is a graph showing the change in the amount of solid solution carbon in the grain according to the size of the precipitate.

2 is a graph showing the change in precipitate size according to the cooling rate.

Claims (3)

In weight%, C: 0.0005-0.004%, Si: 0.02-0.6%, Mn: 0.25-0.8%, P: 0.005-0.2%, S: 0.003-0.02%, Al: 0.01-0.08%, N: 0.004% (Not including 0%), Cu: 0.005 to 0.2%, the content of Mn, Cu, S satisfies 5≤0.27 * (Mn + Cu) / S≤25, and the remaining Fe and other Composed of inevitable impurities, A small hardening type high strength cold rolled steel sheet comprising one or two or more precipitates selected from the group consisting of MnS, CuS, and (Mn, Cu) S, wherein the average size of the precipitates is 0.2 μm or less. According to claim 1, wherein the steel sheet is hard to harden the high strength cold-rolled steel sheet, characterized in that the Mo is added 0.01-0.2%. In weight%, C: 0.0005-0.004%, Si: 0.02-0.6%, Mn: 0.25-0.8%, P: 0.005-0.2%, S: 0.003-0.02%, Al: 0.01-0.08%, N: 0.004% (Not including 0%), Cu: 0.005 to 0.2%, the content of Mn, Cu, S satisfies 5≤0.27 * (Mn + Cu) / S≤25, and the remaining Fe and other After reheating the steel composed of unavoidable impurities to a temperature of 1100 ~ 1300 ℃, hot rolling with the finish rolling temperature above Ar3 transformation point, cooling at a speed of 300 ~ 1000 ℃ / min, and winding at a temperature of 500 ~ 750 ℃ After that, cold rolling at a reduction ratio of 30 to 90%, and a method for producing a hardened hardened type cold rolled steel sheet comprising a continuous annealing for 10 seconds to 30 minutes in a temperature range of 500 to 900 ° C.

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