KR101105055B1 - Bake-hardenable cold rolled steel sheet having excellent resistance to second work embrittleness and high strength, and method of manufacturing the same - Google Patents

Abstract

Provided is a hardening type high strength cold rolled steel sheet used as a material for automobiles and a method of manufacturing the same. This cold rolled steel sheet is C: 0.003-0.005%, Si: 0.1-0.8%, Mn: 0.03-0.2%, P: 0.015% or less, S: 0.003-0.025%, Al: 0.01-0.08%, N by weight% : 0.004% or less, Cu: 0.005 to 0.2%, the Mn, Cu, S satisfy the conditions Mn + Cu ≤ 0.3, 0.5 * (Mn + Cu) / S: 2-20, the remaining Fe and other It is composed of unavoidable impurities, and the average size of the precipitate is less than 0.2 µm. According to the present invention, in the cold rolled steel sheet having high strength by Si addition, fine precipitates reduce the solid solution carbon in the crystal grains, thereby improving the quench hardening characteristics and the secondary processing brittleness.

Cold rolled steel, hardened hardening, high strength, secondary work brittleness, in-plane anisotropy index, (Mn, Cu) S

Description

BAKE-HARDENABLE COLD ROLLED STEEL SHEET HAVING EXCELLENT RESISTANCE TO SECOND WORK EMBRITTLENESS AND HIGH STRENGTH, AND METHOD OF MANUFACTURING THE SAME}

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 size of the precipitate according to the cooling rate,

       Figure 2a is the case of 0.5 * (Mn + Cu) / S: 2-20,

       2B shows the case of 0.5 * (Mn + Cu) / S ≦ 20.

The present invention relates to a high strength cold rolled steel sheet used as a material for automobiles and a method of manufacturing the same. More specifically, the present invention relates to a cold rolled steel sheet having excellent baking hardening properties and secondary workability by reducing solid carbon content in grains by fine precipitates 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 dissolved carbon remains, and it has a hardening hardening capacity of about 10 ~ 20MPa after the baking treatment while securing the non-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. Because of this, it is difficult to secure stable quality and costs a lot of production.

SUMMARY OF THE INVENTION The present invention provides a cold rolled steel sheet having a second hardening resistance and having a secondary hardening resistance by controlling the amount of solid solution carbon in grains by non-precipitation without adding Ti and Nb, and a method of manufacturing the same. .

Cold rolled steel sheet of the present invention for achieving the above object, by weight% C: 0.003-0.005%, Si: 0.1 ~ 0.8%, Mn: 0.03 ~ 0.2%, P: 0.015% or less, S: 0.003-0.025%, Al: 0.01-0.08%, N: 0.004% or less, Cu: 0.005-0.2%, wherein Mn, Cu, and S are conditions Mn + Cu ≦ 0.3, 0.5 * (Mn + Cu) / S: 2-20 Satisfactory, and is composed of the remaining Fe and other unavoidable impurities, the average size of the precipitate is less than 0.2㎛.

In addition, the method for producing a cold rolled steel sheet according to the present invention is C: 0.003-0.005%, Si: 0.1-0.8%, Mn: 0.03-0.2%, P: 0.015% or less, S: 0.003-0.025%, Al: 0.01-0.08%, N: 0.004% or less, Cu: 0.005 to 0.2%, and Mn, Cu, and S satisfy the conditions Mn + Cu ≦ 0.3, 0.5 * (Mn + Cu) / S: 2-20 After reheating the steel composed of the remaining Fe and other unavoidable impurities to a temperature of 1100 ° C. or higher, hot rolling with the finish rolling temperature above Ar ₃ transformation point, cooling at a speed of 300 ° C./min or higher, and winding at a temperature of 700 ° C. or lower. And then cold rolled, and continuous annealing.

In the present invention, precipitates have the form of MnS, CuS, (Mn, Cu) S, and the number of distribution of these precipitates is 4 × 10 ⁶ / mm ² or more. Under the conditions of 0.5 * (Mn + Cu) / S: 2-7, the number of distribution of precipitates increases. In the present invention, when Mo is included in an amount of 0.01 to 0.2%, workability is further improved.

Hereinafter, the present invention will be described in detail.

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

As shown in FIG. 1, the finer the precipitates, the smaller the amount of the dissolved carbon in the grains. Since the dissolved carbon remaining in the grain is relatively free to move, it affects the room temperature aging characteristics in combination with the operating potential. On the contrary, the carbons segregated at more stable positions, such as grain boundaries or surroundings of precipitates, are activated at high temperatures such as coating baking treatment, thereby affecting the baking hardening characteristics. As such, the decrease in the amount of solid solution carbon in the grains means that the segregation of carbon in a more stable position, that is, around grain boundaries or fine precipitates, affects the hardening hardening characteristics.

According to the present invention, the calcined hardening characteristic can be stably secured when the average content of precipitates of MnS, CuS, and (Mn, Cu) S is 0.2 μm or less while the carbon content is 0.003 to 0.005%. 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 is conditional Mn + Cu ≦ 0.3, 0.5 * while the content of Mn is 0.03-0.2%, the content of S is 0.003-0.025%, and the content of Cu is 0.005-0.2%. It is necessary to adjust to satisfy (Mn + Cu) / S: 2 ~ 20, and (2) MnS, CuS, (Mn, Cu) S when cooling rate is over 300 ℃ / min after rolling The average size of precipitates is less than 0.2㎛.

That is, Fig. 2 (a) is 0.5 * (Mn + Cu) / with steel having 0.0042% C-0.14% Mn-0.009% P-0.015% S-0.04% Al-0.0024% N-0.03% Cu-0.42% Si. It is a graph that investigates the size of precipitates according to the cooling rate after hot rolling steel of S: 5.67. Referring to the graph of FIG. 2 (a), when the cooling rate is adjusted for the case of satisfying 0.5 * (Mn + Cu) / S ≦ 20, the precipitates of MnS, CuS, and (Mn, Cu) S have an average size of 0.2 μm. It can be confirmed that the following can be satisfied.

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 and more favorable to processability as MnS and CuS single precipitates are larger than Mn and Cu composite precipitates. It was. It was confirmed that this greatly improved. That is, when the ratio of .5 * (Mn + Cu) / S is in the range of 2-7, the number of single precipitates of MnS and CuS is larger than that of (Mn, Cu) S composite precipitates, so that the number of precipitates is increased, resulting in greater workability. Improves.

The cold rolled steel sheet of the present invention and a manufacturing method thereof will be described in detail below.

[Cold rolled steel sheet of the present invention]

The content of carbon (C) is preferably 0.003-0.005%.

In the present invention, while the amount of solid solution in the grains is reduced by the fine precipitates, the amount of hardening of the calcined grain is increased by that much. In other words, as the total carbon content in the steel sheet increases, the content of carbon segregating around the grain boundaries or precipitates, which is more effective in the hardening characteristics than in the grains, increases. In consideration of this, the content of carbon (C) should be 0.003% or more to secure the baking hardening characteristics. In order to make the baking hardening amount larger, it is preferable to make content of carbon into 0.0031% or more. In the case where the carbon content is more than 0.005%, moldability is drastically reduced.

The content of silicon (Si) is preferably 0.1 to 0.8%.

Silicon is an element having a high solid solution strengthening effect and a low drop in elongation, which ensures high strength in steels for controlling precipitates according to the present invention. If the content of silicon is more than 0.1% to secure the strength, in the case of more than 0.8% ductility is reduced.

The content of manganese (Mn) is preferably 0.03-0.2%.

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 is precipitated around the precipitate so that the precipitated carbon is dissolved in the coating baking process to increase yield strength. It is preferable to make content into 0.03 to 0.2%. The above effects can be obtained when the content of manganese is 0.03% or more, and when the content of manganese is more than 0.2%, coarse MnS precipitates are generated due to high content of manganese, resulting in poor baking hardening characteristics.

The content of phosphorus (P) is preferably 0.015% or less.

When the content of phosphorus is more than 0.015%, ductility and moldability are lowered, so it is preferable to be 0.015% or less.

The content of sulfur (S) is preferably 0.003-0.025%.

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 content of sulfur is more than 0.025%, the content of the solid solution of sulfur is so high that the ductility and moldability is greatly lowered, there is a fear of red brittle brittleness.

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

Aluminum is an element added as a deoxidizer, but in the present invention, nitrogen is added in steel to prevent formability deterioration by solid solution nitrogen. If the amount of aluminum is less than 0.01%, the amount of solid solution is not good because of the large amount of solid solution, and if the amount of aluminum is more than 0.08%, the amount of aluminum in the solid state is high, the ductility is lowered.

The content of nitrogen (N) is preferably 0.004% or less.

Nitrogen is an element inevitably added during steelmaking, and in the case of more than 0.004%, the moldability is lowered, 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 the precipitated carbon is dissolved and yielded in the coating process Add 0.005-0.2% based on the study of increasing strength. If the content of copper is 0.005% or more, it can be finely precipitated. If it exceeds 0.2%, the copper is precipitated coarsely, so that the hardening hardening characteristic is poor.

The sum of the Mn and Cu is preferably 0.3% or less. This is because if the sum of Mn and Cu is more than 0.3%, the size of the precipitate becomes large and it is difficult to secure the baking hardening characteristics.

It is preferable that the weight ratio of said Mn, Cu, and S satisfy | fills 0.5 * (Mn + Cu) / S: 2-20. 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 (0.5 * (Mn + Cu) / S (wherein the content of Mn, Cu, S is in weight%)) is 2 or more, 20 In the case of more than one, the precipitates are coarse, so that the characteristics of hardening hardening, plastic anisotropy, and in-plane anisotropy index are not good. The ratio of 0.5 * (Mn + Cu) / S is significantly different from 7 and the distribution number of precipitates is significantly different, that is, when the ratio of 0.5 * (Mn + Cu) / S is 7 or less, (Mn, Cu Evenly distributed MnS and CuS single precipitates are much finer than composite precipitates of S. When the ratio of 0.5 * (Mn + Cu) / S is greater than 7, the number of distribution decreases despite the small difference in size of precipitates ( This is because the amount of composite precipitates of Mn and Cu) S increases.

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, and (Mn, Cu) S precipitates directly affects the hardening characteristics, secondary processing brittleness, plastic anisotropy index, and in-plane anisotropy index. In the case where the average size of these precipitates is larger than 0.2 µm, the baking hardening characteristic, the secondary processing brittleness, the plastic anisotropy index, and the in-plane anisotropy index are not good.

Furthermore, in the component system of the present invention, when the distribution number of precipitates of 0.2 μm or less is 4 × 10 ⁶ / mm ^{2 or} more, the plastic anisotropy index is increased and the in-plane anisotropy index is lowered, thereby greatly improving workability. In general, when the plastic anisotropy index increases, the in-plane anisotropy index rises and there is a limit to increasing the plastic anisotropy index in terms of processability. . In addition, in the present invention, when the ratio of 0.5 * (Mn + Cu) / S is 2-7, the distribution number of precipitates of 0.2 µm or less is increased, which is advantageous for securing workability.

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.

[Manufacturing method of cold rolled steel sheet]

The present invention is characterized by satisfying the average size of MnS, CuS, (Mn, Cu) S precipitates in a cold rolled plate through hot rolling and cold rolling to satisfy the above-described stress. 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. The reheating temperature is preferably 1100 占 폚 or higher. 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.

Hot rolling is preferably performed at a finish rolling temperature above Ar ₃ transformation temperature. This is because when the finish rolling temperature is lower than the Ar ₃ transformation temperature, not only the workability is degraded due to the formation of the rolled grain but also the ductility is greatly reduced.

After hot rolling, the cooling rate before winding is preferably 300 ° C / min or more. According to the present invention, even when the temperature is 2 ≦ 0.5 * (Mn + Cu) / S ≦ 20, if the cooling rate is less than 300 ° C./min, the average size of the precipitate exceeds 0.2 μm. In other words, as the cooling rate increases, a large number of nuclei are generated and the precipitate becomes fine. If the amount of 0.5 * (Mn + Cu) / S exceeds 20, the coarse precipitates undissolved during the reheating process, and even if the cooling rate is increased, the number of new nuclei is generated and the precipitates do not become fine (Fig. 2b, 0.0045% C). -0.15% Mn-0.012% P-0.006% S-0.05% Al-0.0019% N-0.13% Cu-0.43% Si). Referring to the graph of Figure 2, the faster the cooling rate is the size of the precipitate becomes fine, so there is no need to limit the upper limit of the cooling rate, even if the cooling rate is more than 1000 ℃ / min cooling rate is no longer increased 300-1000 degreeC / min is more preferable.

[Coiling condition]

Winding is performed after hot rolling as above, but the winding temperature is preferably 700 ° C or lower. If the coiling temperature is higher than 700 ° C, the precipitate grows too coarsely, resulting in poor baking hardening.

[Cold rolling condition]

Cold rolling is preferably performed at a reduction ratio of 50 to 90%. If the cold reduction rate is less than 50%, the amount of nucleation of the annealing recrystallization is small, so that grains grow too large during annealing, resulting in a decrease in strength and formability due to coarsening of the annealing recrystallization grains. If the cold reduction ratio is more than 90%, the moldability is improved, but the nucleation amount is too high, so the annealing recrystallized grain is too fine to decrease the ductility.

[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,

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

In the embodiment, the mechanical properties of the cold rolled steel sheet were measured by processing the standard specimens according to the ASTM standard (ASTM E-8 standard). Mechanical properties were used for a tensile tester (INSTRON, Model 6025). The yield strength after baking is the yield strength measured after heat treatment at 170 ° C for 20 minutes after 2% strain is applied to the specimen. Plastic anisotropy index (r _m value) and in-plane anisotropy index (Δr value) were calculated by the following equation.

r _m = (r ₀ + 2r ₄₅ + r ₉₀ ) / 4, △ r = (r ₀ -2r ₄₅ + r ₉₀ ) / 2

The average size of the precipitates and the number of distributions of the precipitates are the size and distribution of all the precipitates present in the matrix.

Example 1

In Table 1, the steel slabs of specimens A1-A7 were reheated at 1200 ° C, hot rolled to finish, cooled at a rate of 600 ° C / min, and wound up at 650 ° C. The finish rolling temperature of not less than Ar ₃ transformation point is 910 ℃, continuous annealing was performed by heating for 40 seconds to 750 ℃ to 10 ℃ / second.

Specimen Number Chemical composition (% by weight) Mn + Cu 0.5 *
(Mn + Cu) / S C Mn Si P S Al N Cu
0.003-0.005 0.03-0.2 0.1-0.8 ≤0.015 0.003-0.025 0.01-0.08 ≤0.004 0.005-0.2
≤0.3 2-20 A1 0.0041 0.06 0.18 0.01 0.018 0.04 0.0019 0.04
0.1 5 A2 0.0036 0.1 0.17 0.009 0.015 0.05 0.0026 0.03
0.13 7.22 A3 0.0038 0.13 0.35 0.012 0.015 0.04 0.0032 0.03
0.16 6.67 A4 0.0045 0.22 0.55 0.012 0.01 0.04 0.0032 0.05
0.27 13.5 A5 0.0021 0.12 0.2 0.009 0.011 0.05 0.0024 0.12
0.24 10.9 A6 0.0064 0.12 0.34 0.01 0.012 0.04 0.0028 0.07
0.19 7.9 A7 0.0044 0.25 0.53 0.012 0.009 0.05 0.0022 0.18
0.43 23.9

Specimen Number Mechanical properties Average size of precipitate
(Μm) Precipitation Water (pieces / mm ² ) Remarks Yield strength
(MPa) The tensile strength
(MPa) Elongation
(%) Plastic Anisotropy Index (r _m ) In-plane anisotropy index
(△ r) Yield strength after baking
(MPa) 2nd processing brittleness
(DBTT- ℃) A1 245 350 50 1.85 0.28 338 -80 0.06 4.5 X ^{10 8} Invention steel A2 253 355 49 1.83 0.29 342 -80 0.07 2.5 X ^{10 8} Invention steel A3 293 405 45 1.65 0.21 390 -60 0.06 4.0X10 ⁸ Invention steel A4 355 453 38 1.51 0.22 435 -60 0.09 9.1X10 ⁶ Invention steel A5 234 342 52 1.85 0.33 275 -80 0.09 4.2 X 10 ⁶ Comparative steel A6 308 412 36 1.48 0.21 398 -70 0.09 3.2 X 10 ⁶ Comparative steel A7 335 448 34 1.38 0.57 380 -60 0.51 9.3X10 ⁴ Comparative steel

In Tables 1 and 2, A1 to A4 (inventive steel) have an average size of precipitates of 0.2 µm or less, which is high in strength, hardenable to harden, and has excellent secondary work brittleness and workability. Especially in the case of A1 to A3 having a ratio of 0.5 * (Mn + Cu) / S of 7 or less, the moldability is very excellent. This confirmed that the very fine precipitates precipitated with MnS or CuS alone were uniformly distributed. Due to the distribution characteristics of these precipitates, the plastic anisotropy index is high, and the in-plane anisotropy index is low, which shows very excellent processing characteristics. In the case where the ratio of 0.5 * (Mn + Cu) / S was 7 or more, the smaller number of the precipitates was found to have a large amount of (Mn, Cu) S complex precipitates.

On the other hand, A5 (comparative steel) has a low carbon content, low yield strength after quenching, and Sample 6 (comparative steel) has a high carbon content, which has a low elongation and plastic anisotropy index, which is likely to cause breakage during molding. A7 (comparative steel) has a large sediment size and low yield strength after baking.

[Example 2]

The steel slabs of Table 3 were reheated at 1200 ° C., hot rolled to finish, cooled at a rate of 600 ° C./min, and wound up at 650 ° C. The wound hot rolled sheet was subjected to cold rolling and continuous annealing at a reduction ratio of 75%. The finish rolling temperature of not less than Ar ₃ transformation point is 910 ℃, continuous annealing was performed by heating for 40 seconds to 750 ℃ to 10 ℃ / second.

Specimen Number Chemical composition (% by weight) C Mn Si P S Al N Cu Mo Mn + Cu 0.5 *
(Mn + Cu) / S 0.003-
0.005 0.03-0.2 0.1-0.8 ≤0.015 0.003-
0.025 0.01-0.08 ≤0.004 0.005-0.2 0.01-0.2 ≤0.3 2-20 B1 0.0039 0.11 0.21 0.012 0.014 0.034 0.0029 0.044 0.017 0.15 5.5 B2 0.0045 0.12 0.32 0.009 0.011 0.042 0.0042 0.038 0.075 0.16 7.18 B3 0.0036 0.14 0.62 0.012 0.009 0.033 0.0022 0.063 0.16 0.20 11.3 B4 0.0042 0.09 0.2 0.013 0.01 0.038 0.0033 0.053 0.25 0.14 7.15

Psalter
number Mechanical property Average size of precipitate
(Μm) Number of precipitates (pcs / mm ² ) Remarks Yield strength
(MPa) The tensile strength
(MPa) Elongation
(%) Firing
Anisotropy Index (r _m ) Inside
Anisotropy
Exponent (△ r) Yield strength after baking
(MPa) 2nd processing brittleness
(DBTT- ℃) B1 240 352 50 2.28 2.9 335 -80 0.05 8.2X10 ⁸ Invention steel B2 303 410 44 1.88 2.1 387 -60 0.06 4.5 X ^{10 8} Invention steel B3 359 460 37 1.7 2.0 437 -60 0.08 4.1 X 10 ⁶ Invention steel B4 252 359 50 1.86 2.2 339 -80 0.07 4.5 X 10 ⁶ Comparative steel

As shown in Tables 3 and 4, it was found that in the case of B1 to B3, workability was improved by addition of Mo. In the case of B4, when Mo was excessively added, workability was rather poor.

As described above, the cold rolled steel sheet provided in accordance with the present invention has high strength, high post-rolling yield strength, and low secondary work brittleness temperature, thereby providing excellent workability.

Claims (8)

By weight%, C: 0.003-0.005%, Si: 0.1-0.8%, Mn: 0.03-0.2%, P: 0.015% or less, S: 0.003-0.025%, Al: 0.01-0.08%, N: 0.004% or less, Cu: 0.005 to 0.2%, the Mn, Cu, S satisfy the conditions Mn + Cu ≤ 0.3, 0.5 * (Mn + Cu) / S: 2-20, and is composed of the remaining Fe and other unavoidable impurities The hardened high strength cold rolled steel sheet having excellent secondary processing brittleness, characterized in that it comprises at least one precipitate of MnS, CuS and (Mn, Cu) S having an average size of 0.2 μm or less. According to claim 1, wherein the precipitate water is 4 × 10 ⁶ / mm ² or more, the secondary hardening resistance excellent hardening type high strength cold rolled steel sheet. According to claim 1, 0.5 * (Mn + Cu) / S: 2-7 hardening type high strength cold rolled steel sheet excellent in secondary processing brittleness characterized in that. The hardened hardened high strength cold rolled steel sheet according to any one of claims 1 to 3, wherein Mo is further included in an amount of 0.01-0.2%. By weight%, C: 0.003-0.005%, Si: 0.1-0.8%, Mn: 0.03-0.2%, P: 0.015% or less, S: 0.003-0.025%, Al: 0.01-0.08%, N: 0.004% or less, Cu: 0.005 to 0.2%, wherein the Mn, Cu, S satisfy the conditions Mn + Cu ≤ 0.3, 0.5 * (Mn + Cu) / S: 2-20, and is composed of the remaining Fe and other unavoidable impurities After reheating the steel to a temperature above 1100 ° C, hot rolling with a finish rolling temperature above Ar ₃ transformation point, cooling at a rate above 300 ° C / min, winding at a temperature below 700 ° C, and then cold rolling and continuous annealing It is made, including, the hardened high strength cold rolled steel sheet of secondary hard brittleness, characterized in that to produce a steel sheet in which one or more precipitates of MnS, CuS and (Mn, Cu) S is distributed in average size less than 0.2㎛ Manufacturing method. The method of claim 5, wherein the precipitate water is 4 X 10 ⁶ / mm ² or more. The method of manufacturing a hardened hardened type high strength cold rolled steel sheet having excellent secondary work brittleness, characterized in that 0.5 * (Mn + Cu) / S: 2-7. The method for producing a hardened hardened cold rolled sheet according to any one of claims 5 to 7, wherein Mo is further included in an amount of 0.01-0.2%.

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