KR100554753B1 - High strength cold rolled steel sheet with superior formability and weldability and method for manufacturing thereof - Google Patents

Abstract

The present invention relates to a tensile strength 70 ~ 90kgf / mm grade ² high strength cold rolled steel sheet and a method of manufacturing the same which can be easily molded when used as a structural part for automobiles to improve the stability of the vehicle due to the excellent energy absorption in the collision of the vehicle will be.

The present invention is in weight%, C: 0.15 to 0.25%, Si: 0.5 to 1.2%, Mn: 1.0 to 2.0%, P: 0.25% or less, S: 0.020% or less, Al: 0.015 to 0.050%, N: 0.008 ~ 0.026%, the high strength cold rolled steel sheet having excellent formability and weldability, wherein the Si and P satisfy the following relationship, 1.5 ≦ Si [%] + 50/8 P [%] ≦ 2.0 and are composed of the remaining Fe and unavoidable impurities; ,

 Continuously annealing the cold rolled steel sheet at a temperature in the range of relation 2 below 50 sec,

[Relationship 2]

563 + 651 C [%] + 42 Si [%] + 18 Mn [%] <Annealing Temperature [℃] ≤ 850 ℃

Excellent continuous formability and weldability comprising the step of continuous annealing and quenching the ostempering start temperature 400 ~ 450 ℃ at a cooling rate of 20 ~ 100 ℃ / sec and then cooling to 200 ~ 500 sec to 350 ~ 400 ℃ The technical subject matter of the manufacturing method of a high strength cold-rolled steel sheet is made.

Machining organic transformation steel, automotive parts, residual austenite, weldability, formability

Description

High strength cold rolled steel sheet with superior formability and weldability and method for manufacturing manufacture

1 is a graph showing that the state diagrams of C-1.5Mn-1.5Si steel and C-1.5Mn-1.0Si-0.08P steel are the same.

Figure 2 is a microstructure photograph showing that the precipitate of AlN inhibits austenite growth

3 is a graph comparing austenite fractions according to annealing temperatures of steels containing C, Si, and Mn contents, respectively;

The present invention relates to a tensile strength 70 ~ 90kgf / mm grade ² high strength cold rolled steel sheet and a method of manufacturing the same which can be easily molded when used as a structural part for automobiles to improve the stability of the vehicle due to the excellent energy absorption in the collision of the vehicle will be.

Recently, as the environment has emerged as a socially important issue, regulations on automobile emissions and fuel economy have been tightened worldwide. In addition, as regulations on collision stability continue to be tightened, automobile manufacturers around the world are developing vehicles that are light and have excellent collision safety. In addition, as the number of automobiles increases with the increase of automobiles, the safety of passengers is emphasized. In order to make the vehicle lighter and improve crash safety, automobiles must be manufactured using materials of high strength.

As regulations on automobile collision stability are tightened, the evaluation of existing frontal and side collisions is added, and an offset collision evaluation test, which is a stricter standard compared to the existing frontal collisions, has been added. The energy absorption of the bumper is important in automobile stability, and the strength of the automotive part material is increased to increase the energy absorption of the bumper.

Conventional manufacturing techniques of high strength cold rolled steel sheet can be divided into [1] processing hardened steel, [2] composite steel, and [3] common steel transformation steel.

[1] hardened steels

As a method using work hardening by cold rolling, the recovery annealing is performed after cold rolling to increase the strength of the recrystallized structure, so the amount of the additive alloy is small and the weldability is excellent. However, since elongation is low, moldability is bad.

[2] composite tissue steels

After cold rolling, the annealing temperature is heated above the A ₁ transformation point to form austenite, followed by quenching to transform austenite into martensite or bainite, thereby increasing the strength of the material. These steels are difficult to manufacture and have a low elongation rate because the cooling rate must be high in the heat treatment process.

[3] sharing slots

There is a processed organic transformation steel which increases the elongation by remaining residual austenite in the steel. As the retained austenite is transformed into high strength martensite during molding, the elongation is increased due to the faster work hardening rate. It is a steel containing residual austenite in processed organic transformation steel, and its basic additive elements are known as C, Si, and Mn. C reduces the transformation temperature of martensite to stabilize austenite and Si inhibits the formation of carbides to increase the solid solution C content in the retained austenite. Mn, together with C, serves to lower the martensite transformation temperature and increase strength.

In order to reduce the weight by applying the processed organic transformation steel to structural parts of automobiles, the formability should be increased than the processing organic transformation steel of the simple C-Si-Mn system. Moreover, as the shape of automobiles becomes more complex, conventional formability steels are not applied to a large number of automobile parts. In order to solve this problem, processed organic transformation steel with improved formability should be manufactured. The property to be improved along with formability is weldability. In the conventional processing organic transformation steel, Si is contained in an amount of 1.5% or more to suppress the formation of carbides and increase the fraction of retained austenite to form formability. If the Si content is high, the weldability is deteriorated, and not only the incidence of defects in the process of welding the steel sheet and the steel sheet during the production of the steel sheet is high, but also the welding defects are produced when the automobile parts are manufactured from such steel sheets and the parts are manufactured by spot welding.

The present invention was devised to improve the characteristics of conventional processed organic transformation steel, and because of its excellent formability and high strength, it is possible to reduce the thickness of parts materials when used as structural parts for automobiles, thereby reducing the weight of automobiles and energy during collision of automobiles. It is an object of the present invention to provide a tensile strength of 70 ~ 90kgf / mm grade ² cold rolled steel sheet excellent in moldability and weldability at the same time to improve the stability of the vehicle with excellent absorption.

Cold rolled steel sheet of the present invention for achieving the above object, in weight%, C: 0.15-0.25%, Si: 0.5-1.2%, Mn: 1.0-2.0%, P: 0.25% or less, S: 0.020% or less, Al: 0.015 to 0.050%, N: 0.008 to 0.026%, wherein Si and P satisfy the following relationship, 1.5 ≦ Si [%] + 50/8 P [%] ≦ 2.0 and are composed of the remaining Fe and unavoidable impurities .

In addition, the cold rolled steel sheet manufacturing method of the present invention,

Continuously annealing the cold rolled steel sheet formed as described above at a temperature in the range of relation 2 below 50 sec,

[Relationship 2]

563 + 651 C [%] + 42 Si [%] + 18 Mn [%] <Annealing Temperature [℃] ≤ 850 ℃

The continuous annealing and quenching at 20 ~ 100 ℃ / s cooling rate to the ostempering start temperature 400 ~ 450 ℃ and then comprises a step of osstem cooling to 200 ~ 500 s to 350 ~ 400 ℃.

Hereinafter, the present invention will be described in detail.

The present invention forms an appropriate amount of residual austenite by adding an appropriate amount of C, Si, P, and Mn to the steel, while maintaining a high elongation, by depositing AlN with the addition of an appropriate amount of Al and N to refine the grain size It is characterized by the production of a high strength cold rolled steel sheet suitable for automotive structural parts having excellent formability and weldability by the continuous annealing method. The present invention will be described by dividing it into emphasis range and manufacturing conditions thereof.

[Range composition range]

· C: 0.15 ~ 0.25%

C is a component that stabilizes austenite by lowering the martensite transformation temperature to form residual austenite at room temperature, thereby increasing elongation, and it is necessary to add 0.1% or more to obtain stable residual austenite. It is deteriorated, which is disadvantageous for welding of steel sheets and welding of automobile parts in the production of cold rolled steel sheets.

· Si: 0.5 ~ 1.2%

Si plays a role in suppressing carbide formation in the ostempering process. When the formation of carbides by Si is suppressed, the amount of solid solution C is increased, so that a large amount of solid solution C diffuses into the residual austenite, so that the residual austenite is stabilized. On the other hand, since Si drastically reduces the weldability, it is preferable that the Si content is small in order to facilitate the welding during the cold rolling process and the welding after molding into automotive parts. That is, in order to make an appropriate fraction of retained austenite for good moldability, the Si content should be high and the Si content should be low for weldability. Therefore, in the present invention, in order to effectively suppress the formation of carbides, it is preferable to reduce the content to 1.2% or less in consideration of weldability while adding 0.5% or more of Si. In this way, while suppressing the content of Si to 1.2% or less while improving the weldability, simultaneously adding P, which suppresses carbide formation when added with Si, maintains the fraction of retained austenite. If P is not added, Si should be contained 1.5 to 2.0% in order to suppress carbide formation and to form a proper amount of retained austenite.However, when P is added at the same time, 1.5 to 2.0% is added even if Si is added at 0.5 to 1.2%. Can be obtained.

· Mn: 1.0 ~ 2.0%

Mn increases the strength of the material and stabilizes austenite by decreasing the transformation temperature of martensite, such as C. If Mn is added less than 1.0%, the strength is lowered and the residual austenite becomes unstable. In addition, when Mn is added more than 2.0%, the transformation rate of the ferrite becomes too slow, so that the ferrite formed during the cooling decreases. When a large amount of ferrite is formed, it is important to form an appropriate amount of ferrite because a large amount of solid solution C diffuses into the residual austenite and the residual austenite is stabilized. The addition of excessive amounts of Mn leads to the formation of a high fraction of bainite at austempering temperatures at the austenite, which does not transform into ferrite during cooling, increasing the strength and decreasing the elongation. In the present invention, in consideration of this point, the content of Mn is limited to 1.0 to 2.0%.

· P: 0.25% or less

P is added to ferrite strengthening elements such as Si to effectively suppress the formation of carbides. If the content is more than 0.25%, P is segregated too much in the center of crystal grains during the slab manufacturing process, so that fracture occurs in the continuous casting process. The chances are high. Also, a large amount of P may be segregated in the grain boundary of the product, thereby reducing the stiffness due to grain boundary fracture.

· S: 0.020% or less

S combines with Mn to form a precipitate of MnS. Since MnS is formed as inclusions and can act as a starting point of cracking, it is preferable to limit the amount of S to 0.020% or less since it is more advantageous.

· Al: 0.015 ~ 0.050%

Al is a deoxidation element that is added in the steelmaking process and reacts with O in the steel to make slag, and removes the slag formed in the upper part of the molten steel to remove O in the steel. The Al in the steel is removed and Al remains. In the present invention, AlN precipitates are formed by using Al remaining in the steel and used to improve elongation by reducing grains of retained austenite. It is known that when the same amount of retained austenite is present, when the grain size is small and a large number of austenite is distributed, the elongation is improved because the effect of transforming to martensite during deformation is great. In order to reduce the size of residual austenite, the size of austenite should be reduced during annealing. Formation of precipitates can suppress grain growth and reduce grain size. When there are too many precipitates, the strength tends to increase due to precipitation hardening and the elongation tends to decrease. Therefore, it is important to effectively reduce the grain size of austenite while reducing the amount of precipitates. Nb, Ti, and V precipitates, which are mainly used to obtain precipitation hardening effect in steel, are not only large in size but also combine with austenite stabilizing elements C to form NbC, TiC, and VC, thus reducing the content of solid solution C. Not suitable for processed organic transformation steel. Taken together, it can be seen that in order to increase the elongation in the processed organic transformation steel, small precipitates should be formed without combining with C. In the present invention, AlN is formed as a precipitate having such a role. AlN has no solid solubility of C and the precipitate is known to have a very small size compared with precipitates such as TiC, NbC, and VC. If the amount of Al is less than 0.015%, the number of precipitates formed is small, so that the size of residual austenite cannot be effectively reduced. On the other hand, if the amount of Al is more than 0.050%, the precipitate of AlN is coarsened, which is disadvantageous in forming elongation. For this reason, in the present invention, it is preferable to limit the content of Al to 0.015 ~ 0.050%.

· N: 0.008 ~ 0.026%

N is a component added to form AlN. In general steelworks steelmaking process, N added as an impurity is within 0.004%. In this invention, N is actively added to form AlN precipitates to achieve grain refinement. Since N is precipitated in the form of AlN, it is appropriate to add Al (14/27) as follows in consideration of the atomic weight. That is, when Al in the range of 0.015 to 0.050% is added, it is appropriate that the range of N is 0.008 to 0.026%. When N is added in this range, an appropriate amount of AlN is formed to reduce the grain size of the retained austenite, thereby increasing the elongation. Figure 2 shows that the AlN precipitate inhibits the movement of the austenite grains, and the AlN precipitate inhibits austenite growth during annealing.

· Control of the components Si and P

Figure 1 shows the state diagrams of the 1.5Mn-1.5Si added steel and 1.5Mn-1.0Si-0.08P added, respectively, 1.5Mn-1.5Si added and 1.5Mn-1.0Si-0.08P It can be seen that the state diagram of the added steel is the same. This shows that in phase transformation behavior, 0.08% P has the same effect as 0.5% Si. Si is an element that lowers the weldability, but P does not lower the weldability. Therefore, by adding P of 8/50 Si content instead of reducing the Si content, the change of phase transformation of the same effect can be obtained and the weldability can be improved. Based on this, in the present invention, the content of Si and P is determined in the range of the following formula.

1.5 ≤ Si [%] + 50/8 P [%] ≤2.0

Steel manufacturing conditions

The steel formed as described above is hot rolled and wound. Then, the hot rolled plate is cold rolled and then continuously annealed and heat treated to provide a cold rolled plate. In the present invention, there is a feature in controlling the continuous annealing process and the tempering conditions of the cold rolled sheet under such manufacturing conditions. Therefore, the hot rolling conditions and the cold rolling conditions can be manufactured through a variety of techniques, the representative technology described in the hot rolling process and cold rolling process as a specific example, but the present invention is limited thereto. It is not.

· Hot rolling

The steel formed as described above is reheated at high temperature and hot rolled. The reheating temperature is preferably 1050 to 1300 ° C. Reheating and hot rolling as described above, the finish rolling temperature at this time is preferably 890 ~ 940 ℃. Although rolling by winding as above, it is preferable that the coiling temperature at this time shall be 600-700 degreeC.

- cold rolling

The hot rolled plate obtained above is pickled and cold rolled, and the cold reduction rate at this time is preferably 40 to 70%.

· Continuous Annealing Process

In order to increase the elongation using the steel containing C, Si, Mn as in the present invention, the content of residual austenite must be increased. According to the study of the present invention, in order to increase the residual austenite, the heat treatment cycle should be set appropriately for the components.

In order to make residual austenite when annealed using a continuous annealing furnace, an austenite must be annealed to form austenite, cooled to an ostempering temperature, and austened to form bainite, while dissolving solid solution C into residual austenite to stabilize austenite. do. At this time, it is important to set the annealing temperature well. If the annealing temperature is too low, the pearlite present in the hot-rolled steel sheet cannot be dissolved, thereby reducing the stability of austenite. In addition, if the annealing temperature is too high, too much austenite is formed and the ferrite becomes less, so only bainite is finally formed, thereby increasing strength and decreasing elongation. In view of this, it is important to set the optimum annealing temperature for the steel of each component.

The elements that greatly influence the determination of annealing temperature are C, Si, and Mn, so in the present invention, the continuous annealing temperature is measured by measuring the amount of austenite when the steel produced by changing these components is maintained at each annealing temperature for 51 sec. Is set. 3 shows the results of the experiment. In order to increase the amount of retained austenite using the steel having the component system of FIG. 3, it is necessary to form the maximum ferrite to diffuse the maximum solid solution C in the austenite. Perlite must be dissolved while maximizing the fraction of ferrite. Since there is a large amount of carbides in Perlite, the presence of Perlite reduces the amount of solid solution C spread to austenite. In order to completely dissolve the pearlite, the amount of austenite in each steel with a C content of 0.1, 0.15 and 0.20% must be 19, 28 and 38%. If the austenite is formed more than this, the amount of ferrite is reduced, so it is difficult to form a large amount of retained austenite. Under these conditions, the annealing temperature to completely dissolve the pearlite is 563 + 651 C [%] + 42 Si [%] + 18 Mn [%], and the annealing temperature is higher than 850 ° C, so much austenite is formed. It is suitable to anneal. Therefore, the most suitable annealing temperature range is as follows.

563 + 651 C [%] + 42 Si [%] + 18 Mn [%] <Annealing Temperature [℃] ≤ 850 ℃

In the present invention, by annealing for 50 seconds or more in the continuous annealing temperature range described above to ensure the proper austenite.

Agarose, tempering heat treatment

In the annealing section, the austenite-formed material is quenched to austelling start temperature of 400 ~ 450 ℃ to prevent the formation of a pearlite, and then osstem cooling to 200 ~ 500 sec to 350 ~ 450 ℃. Rapid cooling from the continuous annealing section to the starting temperature of ossempering, the cooling rate is preferably about 20 ~ 100 ℃ / sec. When austempering, a portion of the austenite formed in the annealing section is formed as bainite, and the solid solution C diffuses into the residual austenite to stabilize the residual austenite.

In the present invention, it is preferable to quench to 400 ~ 450 ℃ the start tempering temperature in the annealing section. Then, it is cooled for 200 to 500 sec from the tempering start temperature to 350 to 450 ° C.

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

Example 1

Each steel of Table 1 component was melted and hot-rolled. During the annual rolling, the reheating temperature was 1250 ℃, the finishing temperature was 910 ℃, and the winding temperature was 600 ℃. After removing the surface oxide layer of the hot rolled plate by pickling, 50% cold rolling was performed to prepare a 1.4 mm thick internal rolled steel sheet. The cold rolled steel sheet was heat-treated in a continuous annealing furnace, and the annealing time was 51 to 102 sec and the tempering time was 300 sec. Table 2 shows the measurement results of the material of the cold rolled steel sheets according to the heat treatment conditions.

River C Mn Si P S S-Al N Si + 50 / 8P Annealing temperature lower limit Remarks A1 0.20 1.51 1.05 0.072 0.010 0.035 0.0100 1.5 784 Invention steel A2 0.19 1.58 1.20 0.100 0.005 0.049 0.0140 1.8 766 A3 0.20 1.48 0.90 0.080 0.003 0.034 0.0120 1.4 758 A4 0.20 1.46 0.70 0.100 0.003 0.034 0.0110 1.3 749 B1 0.10 2.35 1.44 0.011 0.009 0.035 0.0020 1.5 731 Comparative steel B2 0.14 1.79 1.43 0.013 0.011 0.039 0.0036 1.5 746 B3 0.20 1.33 1.70 0.011 0.009 0.037 0.0020 1.76 789 The annealing temperature lower limit is calculated using the formula 563 + 651 C [%] + 42 Si [%] + 18 Mn [%].                                             

River Annealing Temperature (℃) Annealing Time (SEC) Osstem Furring Start Temperature (℃) Ostem Furring Time (SEC) Yield strength (kgf / mm ² ) Tensile Strength (kgf / mm ² ) Elongation (%) Flash Butt Weldability Remarks A1 800 51 400 300 44.37 74.23 34.02 ○ Invention steel A1 830 51 400 300 40.71 80.53 31.17 ○ A1 800 51 450 300 42.99 81.01 30.14 ○ A1 830 51 450 300 43.74 81.13 29.38 ○ A1 800 102 400 300 42.90 80.60 29.10 ○ A2 800 51 400 300 44.98 74.16 30.53 ○ A2 830 51 400 300 43.23 75.13 31.34 ○ A2 830 51 450 300 45.10 72.44 28.93 ○ A2 800 102 400 300 45.90 76.90 29.30 ○ A3 830 51 400 300 43.91 80.26 29.35 ○ A4 830 51 400 300 42.06 81.90 30.31 ○ B1 800 51 400 300 41.10 83.80 21.60 △ Comparative steel B1 800 51 450 300 40.30 92.10 17.40 △ B1 800 51 500 300 41.50 85.30 16.20 △ B1 800 102 450 300 40.30 92.10 17.40 △ B2 800 51 400 300 42.60 76.10 23.10 △ B2 800 51 450 300 36.50 82.50 23.80 △ B2 800 51 500 300 47.00 68.50 23.20 △ B2 800 102 450 300 36.50 82.50 23.80 △ B3 800 51 450 300 47.80 71.00 20.80 × B3 800 51 500 300 55.60 70.80 23.20 × B3 800 102 450 300 47.80 71.00 20.80 ×

As shown in Tables 1 and 2, it can be seen that the steel satisfying the present invention has a higher yield strength than the comparative material.

As described above, the present invention can provide a high-strength steel sheet having high elongation and excellent moldability, and this high-strength steel sheet has a useful effect of improving the stability of an automobile by using it for automotive structural parts.

Claims (3)

In weight%, C: 0.15-0.25%, Si: 0.5-1.2%, Mn: 1.0-2.0%, P: 0.25% or less, S: 0.020% or less, Al: 0.015-0.050%, N: 0.008-0.026%, Si and P satisfy the following relationship, and 1.5 ≦ Si [%] + 50/8 P [%] ≦ 2.0 High strength cold rolled steel sheet with excellent formability and weldability composed of remaining Fe and unavoidable impurities. By weight%, C: 0.15-0.25%, Si: 0.5-1.2%, Mn: 1.0-2.0%, P: 0.25% or less, S: 0.020% or less Al: 0.015 to 0.050%, N: 0.008 to 0.026%, wherein Si and P satisfy the following relationship, 1.5 ≦ Si [%] + 50/8 P [%] ≦ 2.0 and are composed of the remaining Fe and unavoidable impurities Continuously annealing the cold rolled sheet at a temperature in the range of the following relation 2 for at least 50 sec, [Relationship 2] 563 + 651 C [%] + 42 Si [%] + 18 Mn [%] <Annealing Temperature [℃] ≤ 850 ℃ Excellent continuous formability and weldability comprising the step of continuous annealing and quenching the ostempering start temperature 400 ~ 450 ℃ at a cooling rate of 20 ~ 100 ℃ / sec and then cooling to 200 ~ 500 sec to 350 ~ 400 ℃ Method for producing high strength cold rolled steel sheet. The method of claim 2, wherein the cold rolled steel is reheated to a temperature of 1050 ~ 1300 ℃ hot rolled to a finish rolling temperature conditions of 890 ~ 940 ℃ wound the hot rolled plate at a temperature of 600 ~ 700 ℃, A method for producing a high strength cold rolled steel sheet having excellent formability and weldability, which is obtained by pickling and cold rolling at a cold reduction ratio of 40 to 70%.

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