JPH10219387A - Hot rolled high tensile strength steel plate excellent in workability and its production - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a means of stably providing a hot rolled high tensile strength steel plate having high ductility, easy of press working, excellent in spreadability, and having satisfactory weldability. SOLUTION: The hot rolled high tensile strength steel plate, having <=690N/mm<2> tensile strength and excellent in workability, is constituted so that it has a composition consisting of, by weight, 0.05-0.25% C, <=2.0% Si, <=1.6% Al, 0.8-2.0% Mn, 0-0.04% Ti, <=0.0100% N, <0.003% Nb, and the balance Fe with inevitable impurities and further containing, if necessary, one or more kinds among proper amounts of Ca, Zr, and rare earth elements and satisfying Si(%)+Al(%)>=1.0 and also has a structure consisting of, by volume ratio, >=5% retained austenite, 3-20% pearlite, and the balance polygonal ferrite and bainite. This steel plate can be produced by subjecting, after the completion of hot rolling, the resultant steel plate to air cooling for 1-5sec, to cooling down to 550-650 deg.C at >=30 deg.C/s cooling rate, further to air cooling for 2-10sec, to cooling again down to 350-520 deg.C at >=30 deg.C/s cooling rate, and then to coiling.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention is excellent in workability (ductility, hole expandability, punching hole expandability, etc.) and is formed into various shapes by press working, stretch flange working, etc., and is used for the structure of automobiles or industrial equipment. The present invention relates to a hot-rolled high-tensile steel sheet for processing suitable for use as a member and a method for producing the same.

[0002]

2. Description of the Related Art Hot-rolled steel sheets produced by continuous hot rolling are widely used as a relatively inexpensive structural material in various industrial equipment such as automobiles. Many members are formed by processing,
Therefore, there is a strong demand for achieving both high strength and high ductility.

As a means for improving the ductility of a high-strength steel sheet, a "method utilizing TRIP (transformation-induced plasticity) of retained austenite" is known. For example, Japanese Patent Application Laid-Open No. 63-4017 discloses a method. Related to this is disclosed a "method of greatly reducing the high Si content steel in the low temperature austenite region". This method aims to stabilize austenite by enriching C in untransformed austenite by causing bainite transformation, thereby obtaining residual austenite, The hot rolled steel sheet obtained by this method has a structure substantially composed of ferrite, bainite, and retained austenite.

However, in the above method, not only "carbinite-free bainite", which is important for the generation of retained austenite, but also "hard bainite containing carbide" is easily formed in a coarse and band-like form. Has a problem that although it has high ductility, the hole expandability is extremely poor.

In order to improve the hole expandability of a high-ductility, high-strength hot-rolled steel sheet using such retained austenite TRIP, Japanese Patent Application Laid-Open No. 5-195150 discloses "Nb
There has been proposed a technique relating to "a hot-rolled high-tensile steel sheet in which the amount of pearlite is appropriately controlled by addition to secure a retained austenite structure containing pearlite appropriately". However, in this method,
The strength of the product becomes too high due to the large precipitation strengthening ability of Nb,
Therefore, when press working is performed, problems such as deterioration of dimensional accuracy occur.

[0006] In order to realize low strength so that dimensional accuracy at the time of processing does not pose a problem, as disclosed in Japanese Patent Application Laid-Open No. 5-59485, "Al instead of Si has a low solid solution strengthening ability. However, when the Al content increases, a problem arises in the weldability, and there is still room for further improvement in performance.

In view of the above, an object of the present invention is to solve the above-mentioned problems of the prior art, to have sufficient ductility and easy press working, and to improve hole expandability. The aim was to establish a means for stably providing a hot-rolled high-tensile steel sheet that is excellent and that is satisfactory in terms of weldability.

[0008]

Means for Solving the Problems The present inventors have conducted intensive studies to achieve the above object, and as a result, have obtained the following findings. a) It is indispensable to utilize the TRIP effect of retained austenite in order to secure sufficiently satisfactory high ductility in a hot-rolled high-tensile steel sheet. It is absolutely necessary to keep b) In order to ensure good weldability, it is necessary to reduce the C content and suppress the Al content. However, when the C content is reduced, the strength of the steel sheet may be reduced. .
However, even if the steel sheet has a low C content, if the structure is made of polygonal ferrite containing residual austenite and pearlite and bainite, the strength required for high-strength steel sheets for automobiles and the like is stabilized. Can be secured. c) In addition, as described above, an appropriate amount (3% by volume)
-20%), the amount of hard bainite is reduced and the hole expandability of the steel sheet is significantly improved.

D) However, the frequency of mixing of Nb into steel sheets has increased due to recent steelmaking raw material circumstances and the like, and Nb also has an action of facilitating the remaining austenite, so that the TRIP effect is reduced. It is advantageous to positively utilize the effect of Nb in high-strength steel sheets for automobiles and the like to be used.However, as described above, Nb has a large precipitation strengthening ability, and therefore high-strength steel sheets containing Nb are pressed by pressing. There is a great disadvantage in manufacturing products with high dimensional accuracy (it is necessary to suppress the tensile strength to 690 N / mm ² or less to secure dimensional accuracy at the time of pressing, but if Nb is contained, the strength will be in this range Difficult to control). Therefore, when the press workability is considered, the Nb content must be sufficiently regulated.

E) However, an appropriate amount of retained austenite leading to excellent elongation is obtained by using a steel not containing Nb and having an Al content of 1.6% or less that does not adversely affect weldability. There is no known means for realizing a high-tensile hot-rolled steel sheet having a stable amount of pearlite and a controlled amount of pearlite having appeared and improved hole expandability. However, when nucleation of ferrite is performed by air cooling for a predetermined time prior to accelerated cooling after hot rolling, and when gradual cooling (air cooling) is performed for a predetermined time even in a specific temperature range during accelerated cooling, the above-described problem occurs. 5 from material
690 having a structure composed of polygonal ferrite and bainite containing at least 3% to 20% of austenite and 3 to 20% of pearlite, and capable of ensuring dimensional accuracy during pressing.
It has been found that a hot-rolled high-tensile steel sheet having a tensile strength not exceeding N / mm ² and excellent in elongation and hole expandability can be obtained.

The present invention has been made based on the above findings and the like, and provides a hot-rolled high-tensile steel sheet having excellent workability as described below and a method for producing the same. C: 0.05 to 0.25% (% representing the component ratio is hereinafter referred to as% by weight), Si: 2.0% or less, Al: 1.6% or less,
Mn: 0.8 to 2.0%, Ti: 0 to 0.04%, and N: 0.
0100% or less, Nb: less than 0.003%, Si (%) + Al (%) ≧
1.0, the balance being Fe and unavoidable impurities, and containing at least 5% by volume of residual austenite and 3 to 20% of pearlite, with the balance being polygonal ferrite and bainite. A hot-rolled high-strength steel sheet excellent in workability having a tensile strength of 690 N / mm ² or less, characterized by having a microstructure of: C: 0.05 to 0.25%, Si: 2.0% or less, Al:
1.6% or less, Mn: 0.8 to 2.0%, Ti: 0 to 0.04%, Ca: 0.0002 to 0.01%, Zr: 0.01 to 0.10%,
Rare earth elements: At least one of 0.002 to 0.10%, N: 0.0100% or less, Nb: less than 0.003%, Si (%) + Al
(%) ≧ 1.0, the balance being Fe and unavoidable impurities, containing at least 5% by volume of residual austenite and 3 to 20% of pearlite, and the remainder being polygonal A hot-rolled high-strength steel sheet having a structure composed of ferrite and bainite and having excellent workability with a tensile strength of 690 N / mm ² or less. C: 0.05 to 0.25%, Si: 2.0% or less, Al:
1.6% or less, Mn: 0.8 to 2.0%, Ti: 0 to 0.04%, N: 0.0100% or less, Nb: less than 0.003%,
Si (%) + Al (%) ≥ 1.0 and the balance is Fe
The steel slab comprising unavoidable impurities is heated to 1100 ° C. or higher to perform hot rolling. After finishing hot rolling at a finishing temperature of ₃ points or more, air cooling is performed for 1 to 5 seconds, and then 30 ° C. / s
After cooling to 550 to 650 ° C at the above cooling rate and further performing air cooling for 2 to 10 seconds, it is cooled to 350 to 520 ° C again at a cooling rate of 30 ° C / s or more, and then rolled up. A tensile strength of 6 having a structure consisting of polygonal ferrite and bainite containing 5% or more of retained austenite and 3 to 20% of pearlite by volume fraction,
A method for producing a hot-rolled high-tensile steel sheet excellent in workability of 90 N / mm ² or less. C: 0.05 to 0.25%, Si: 2.0% or less, Al:
1.6% or less, Mn: 0.8 to 2.0%, Ti: 0 to 0.04%, Ca: 0.0002 to 0.01%, Zr: 0.01 to 0.10%,
Rare earth elements: At least one of 0.002 to 0.10%, N: 0.0100% or less, Nb: less than 0.003%, Si (%) + Al
(%) The steel slab that satisfies each condition of ≧ 1.0 and the balance is made of Fe and unavoidable impurities is heated to 1100 ° C. or more, hot-rolled, and hot-rolled at a finishing temperature of ₃ points or more. After performing air cooling for 1 to 5 seconds, then cool to 550 to 650 ° C. at a cooling rate of 30 ° C./s or more, further perform air cooling for 2 to 10 seconds, and then cool again to 30 ° C./s or more Characterized in that it is cooled to a temperature of 350 to 520 ° C. at a speed and is wound up, characterized in that 5% or more by volume of retained austenite and 3 to 20%
% Pearlite and the balance is composed of polygonal ferrite and bainite, and has a tensile strength of 690 N / m.
A method for producing a hot-rolled high-tensile steel sheet excellent in workability of m ² or less.

As described above, according to the present invention, a low austenitic carbon content and a low Al content in a range capable of satisfying the weldability and a sufficient amount of austenite to exhibit high ductility by the TRIP effect are ensured. However, it is intended to provide a hot-rolled high-strength steel sheet that is easy to press and has good hole expandability, and is capable of stably providing the following chemical composition and structure of the steel sheet and its manufacturing conditions. Explain the specified reason.

[A] Chemical composition of steel sheet a) CC is an important component in the steel sheet of the present invention, and stabilizes austenite by concentrating in untransformed austenite during the cooling process after hot rolling. By doing so, it is possible to obtain sufficient austenite in the hot-rolled steel sheet to obtain the TRIP effect. However, if the C content is less than 0.05%, sufficient retained austenite cannot be obtained. On the other hand, if the C content exceeds 0.25%, weldability becomes a problem and the second phase becomes too large. Hole spreadability also deteriorates. Therefore, the C content is 0.
Although it was determined to be from 05 to 0.25%, it is preferable to adjust it to from 0.08 to 0.20%.

B) Si Since Si promotes the formation of polygonal ferrite, assists the concentration of C into untransformed austenite, and has the effect of delaying the precipitation of cementite, the residual austenite is obtained. It has the effect of making it easier. However, excessive addition remarkably strengthens the steel sheet by solid solution strengthening, so that not only the press formability becomes a problem, but also the surface quality and weldability deteriorate. Therefore, the upper limit of the Si content is set to 2.0%, but is preferably adjusted to 1.1% or less, more preferably 0.5% or less.

C) Al Al, like Si, promotes the formation of polygonal ferrite and assists the concentration of C into untransformed austenite, and also delays the precipitation of cementite to facilitate the production of retained austenite. However, since the steel sheet is not strengthened much as compared with the case of Si, workability and dimensional accuracy at the time of pressing are not deteriorated. However, if the content of Al exceeds 1.6%, the weldability becomes a problem.
It is set at 1.6% or less, but it is better to regulate it to 1.3% or less. In addition, since it is necessary to regulate the Al content in this way, it is desired that the above-mentioned Si content does not fall below 0.05%. Further, it promotes the formation of polygonal ferrite and helps the concentration of C into untransformed austenite,
In addition, in order to make the effect of Si and Al sufficient to delay the precipitation of cementite and obtain residual austenite, the total content of Si and Al should be "Si (%) + Al (%) ≥ 1.0". Needs to be satisfied.

D) Mn Mn is also an important constituent element in the steel sheet of the present invention, and suppresses the untransformed austenite from being excessively transformed into pearlite. However, this effect is not sufficient if the Mn content is less than 0.8%, while if it exceeds 2.5%, sufficient polygonal ferrite cannot be obtained in the cooling process after hot rolling, and the untransformed C Concentration into austenite is also insufficient, and the desired high ductility or TRIP effect cannot be obtained. Therefore, the content of Mn was determined to be 0.8 to 2.5%.

E) Ti Ti is effective in preventing cracking of the slab, and is therefore a component that is added as necessary. However, even if added in excess of 0.04%, the effect is saturated. The upper limit of the content was set to 0.04%.

F) NN N is an undesired element that precipitates as nitride during the slab casting process and causes slab cracking. Therefore, the N content is determined to be 0.0100% or less.

G) Nb Nb is an undesired element that remarkably strengthens the steel sheet, deteriorating press formability and excessively suppresses pearlite transformation in the present invention. This is one of the major features of the invention steel plate. However, if the Nb content is 0.0
If the content is restricted to a range of less than 03%, the above-mentioned adverse effects are not remarkable. Therefore, in the steel sheet of the present invention, the Nb content is set to be less than 0.003%.

H) Ca, Zr and rare earth elements These components have the effect of improving the cold workability by adjusting the shape of the inclusions. Therefore, it is preferable that one or more of these components be contained as necessary. . However, its content is Ca
In the case of less than 0.0002%, in the case of Zr, less than 0.01%, and in the case of a rare earth element, less than 0.002%, the desired effect cannot be obtained by the above-described action.
If the content exceeds 0.10% and rare earth elements exceed 0.10%, on the contrary, the inclusions in the steel will be too large and the cold workability will be deteriorated.
0002-0.01%, Zr: 0.10-0.10%, rare earth element: 0.002
0.10.10.

I) Residual components Other components in the steel sheet of the present invention are Fe and inevitable impurities not described above. As the inevitable impurities, O,
Elements such as P, S, Cu, Ni, Cr, and Mo, which are inevitably mixed into steel, are included. Among these, P is an impurity element that adversely affects the weldability, so that the lower the content, the more preferable.In order to ensure the desired weldability, the content of P is set to 0.
It is desirable to keep it below 05%. Since S is an impurity element that forms MnS-based inclusions and lowers workability, the content of S is also preferably as low as possible, and if possible, the content is desirably 0.02% or less.

[B] Structure of Steel Sheet In the case of a hot-rolled steel sheet having a relatively low C content as in the present invention, it is important to ensure strength. However, the structure is changed to a polygonal ferrite containing residual austenite and pearlite. When the structure is made of bainite, it becomes possible to stably secure the strength required for high-tensile steel sheets for automobiles and the like. Further, in this case, in order to impart high ductility for working to the hot-rolled steel sheet by utilizing the TRIP effect of the retained austenite, it is indispensable to secure 5% or more of the retained austenite by volume. . In addition, the volume ratio of pearlite in the steel sheet structure is set to 3
By setting it to ２０20%, the amount of hard bainite is reduced, and the hole expandability of the steel sheet is significantly improved. Here, if the volume percentage of pearlite is less than 3%, the above effect is not sufficient. On the other hand, if the volume percentage of pearlite exceeds 20%, it becomes difficult to secure the retained austenite. The desired high ductility cannot be achieved. The above structure can be realized by adjusting the chemical composition of the steel sheet and adjusting the manufacturing conditions described below.

[C] Production conditions of hot-rolled steel sheet The steel to be subjected to hot rolling can be melted by, for example, a converter, an electric furnace or an open-hearth furnace, and the steel type is rimed steel, capped steel, semi-killed steel or killed steel. Any of steel may be used. In addition, any means such as "ingot-bulk rolling" or "continuous casting" may be adopted for the production of a billet as a rolled material.

However, in the present invention, the steel slab to be subjected to hot rolling is heated and held at 1100 ° C. or higher, and then hot rolling is started, and finish rolling is finished at a temperature of ₃ or more Ar points. 11
At a temperature lower than 00 ° C., the billet is cooled during hot rolling.
r The finishing temperature of ₃ points or more cannot be secured. When finishing the temperature is less than ₃ points Ar, ferrite transformation occurs during hot rolling workability of the resulting hot rolled steel sheet distortion due to hot rolling in the ferrite grains obtained is introduced deteriorates. The steel slab to be charged into the heating furnace may be a slab kept at a high temperature after casting or a slab left at room temperature.

In the present invention, the cooling conditions after rolling are important. That is, air cooling for 1 to 5 seconds after completion of hot rolling and air cooling for 2 to 10 seconds from 550 to 650 ° C. during accelerated cooling are particularly important.

First, in order to form a controlled amount of pearlite without adding Nb as in the case of the steel sheet of the present invention, 2 to 10 from a temperature of 550 to 650 ° C.
It was confirmed that air cooling for 2 seconds was necessary. And, since the pearlite transformation in this temperature range is relatively slow, it also contains an appropriate amount of untransformed austenite, and is subjected to bainite transformation in the subsequent winding by accelerated cooling, so that 5% or more effective for ductility is obtained. Of retained austenite can be left. In this case, if the air cooling start temperature is higher than 650 ° C., it is impossible to adjust the amount of pearlite to an appropriate amount. On the other hand, if the air cooling start temperature is lower than 550 ° C., bainite containing carbide is generated. In any case, the desired amount of pearlite cannot be secured, so that the air cooling start temperature during the accelerated cooling is set to 550 to 650 ° C, but it is preferable to adjust the temperature to the range of 550 to 600 ° C.

The formation of pearlite is started when the C concentration in austenite reaches the eutectoid point (about 0.8%) or more, and the concentration of C in austenite (remaining austenite is reduced). (Indispensable for securing) is generated by the expulsion of C into untransformed austenite due to the formation of ferrite. The present inventors have assiduously studied and found that air cooling for 1 to 5 seconds after hot rolling is important for promoting ferrite formation.

This finding means that the early ferrite nuclei play an important role. That is, if the air cooling after hot rolling is less than 1 second, the formation of ferrite nuclei is insufficient, and as a result, sufficient ferrite is not generated, and the concentration of C in austenite is insufficient, resulting in accelerated cooling. Even if air cooling is performed halfway, sufficient pearlite cannot be obtained, and bainite containing carbides will be generated. On the other hand, this air cooling is 5
If the time exceeds seconds, the generation of pearlite is started from a high temperature range because the amount of ferrite generation increases. Since the rate of transformation to pearlite in such a high temperature range is very high, almost all of the untransformed austenite undergoes pearlite transformation, and it becomes impossible to obtain residual austenite effective for improving ductility. .

By the way, except for the above-mentioned air cooling, accelerated cooling is performed at a cooling rate of 30 ° C./s or more to the winding temperature. This is because the steel of the present invention is a steel which does not actively contain Nb.
This is because the light generation speed is high, and therefore, excessive structural change is suppressed except at a temperature at which the structure can be controlled by air cooling. That is, the cooling rate in this accelerated cooling is 30 ° C./s
If it is less than 100%, pearlite is excessively generated, and a target structure cannot be obtained.

As described above, in the present invention, "production of ferrite nuclei by air cooling immediately after rolling" and "5.
The combination with "air cooling at 50 to 650 DEG C." is a very important treatment for producing an appropriate amount of ferrite and pearlite.

The above-mentioned accelerated cooling is carried out at a temperature of 350 to 520 ° C., and thereafter winding is performed. By winding in this temperature range, untransformed austenite is transformed into bainite containing no carbide, and C is further concentrated into untransformed austenite, thereby suppressing martensitic transformation, which is necessary for high ductility. 5% or more of austenite remains. That is, if the winding is performed at a temperature exceeding 520 ° C., carbides are formed and no austenite remains, while if the winding is performed at a temperature lower than 350 ° C., martensitic transformation occurs instead of bainite transformation. However, no residual austenite of 5% or more can be obtained.

Next, the present invention will be described with reference to examples.

EXAMPLE After smelting 50 kg of steel having the chemical composition shown in Table 1 in a vacuum melting furnace, a slab 60 mm thick was manufactured by hot forging.
Under the conditions shown in Table 2, a hot-rolled steel sheet having a thickness of 2 mm was obtained.

[0033]

[Table 1]

[0034]

[Table 2]

Next, JIS No. 5 tensile test pieces were collected from each of the hot rolled steel sheets thus obtained, and their mechanical properties were examined. In addition, another test piece was collected from each hot-rolled steel sheet,
The "critical hole expansion rate" of a punched hole punched with a 15% clearance was expanded and investigated using a 60φ conical punch. Furthermore,
Test specimens for X-ray tests were taken from the center of each hot-rolled steel sheet, and the amount of retained austenite was measured. The amount of pearlite was measured by observing the sample which had been subjected to the nital corrosion after the cross-section polishing by SEM and image processing. Table 3 shows the results.

[0036]

[Table 3]

From the results shown in Table 3, the following can be confirmed. That is, the high-tensile hot-rolled steel sheets according to Test Nos. 1 to 6 and Test Nos. 18 to 28 manufactured according to the method of the present invention have more than 5% of retained austenite and 3 to 20% of pearlite, Therefore, it exhibited excellent workability with a tensile strength of 690 N / mm ² or less, an elongation of 35% or more, and a hole expansion ratio of 80% or more.

On the other hand, the hot-rolled steel sheet of Test No. 7 having a low hot-rolling heating temperature has a finishing temperature lower than the Ar ₃ point due to a temperature drop during rolling, and together with the hot-rolled steel sheet of Test No. 8, During the hot rolling, strain was added to the ferrite, resulting in a decrease in ductility. The hot-rolled steel sheet according to Test No. 9 having a short air-cooling time after hot rolling had insufficient pearlite generation and was poor in hole expandability. Test numbers 10 and 15 with slow cooling rate during accelerated cooling
The hot-rolled steel sheet according to Test No. 14, the intermediate air cooling time of which is long, and the hot-rolled steel sheet according to Test No. 16 having a higher winding temperature all have excessively pearlite transformation. The amount of retained austenite is insufficient and elongation is low. Further, the hot-rolled steel sheet according to the test number 11 having a high air-cooling start temperature and the test number 12 having a low air-cooling start temperature during accelerated cooling, and the test number 13 having a short air-cooling time and the hot-rolling sheet according to the test number 17 having a low winding temperature. All of the steel sheets have insufficient pearlite generation and low hole expandability.

On the other hand, the hot-rolled steel sheet according to Test No. 29 having a high Si content had too high strength, and the hot-rolled steel sheet according to Test No. 30 having a high Al content had good properties. Sufficient welding strength was not obtained. Also, Nb
The hot-rolled steel sheets according to Test Nos. 31 and 32 having a high content have insufficient pearlite under the production conditions according to the present invention, and have low hole expandability. And test number 33 with low total content of Si + Al
The hot-rolled steel sheet according to (1) has a low elongation because the pearlite transformation proceeds excessively and the amount of retained austenite is insufficient.

[0040]

As described above, according to the present invention, a high-tensile hot-rolled steel sheet for processing, which exhibits high ductility, has good hole expandability and weldability, and is suitable as an automobile foot part, etc., is stably provided. And other industrially useful effects.

Claims (4)

[Claims] 1. C: 0.05 to 0.25% by weight, Si:
2.0% or less, Al: 1.6% or less, Mn: 0.8 to 2.0%,
Ti: 0 to 0.04%, N: 0.0100% or less,
Nb: less than 0.003%, satisfying each condition of Si (%) + Al (%) ≧ 1.0, the balance being Fe and unavoidable impurities, and 3 to 20% by volume of retained austenite of 5% or more.
A hot-rolled high-strength steel sheet excellent in workability having a tensile strength of 690 N / mm ² or less, characterized by having a structure comprising polygonal ferrite and bainite, the balance comprising pearlite. 2. C: 0.05 to 0.25% by weight, Si:
2.0% or less, Al: 1.6% or less, Mn: 0.8 to 2.0%,
Including Ti: 0-0.04%, Ca: 0.0002-0.01%,
Zr: 0.01 to 0.10%, Rare earth element: One or more of 0.002 to 0.10%, N: 0.0100% or less, Nb:
Less than 0.003%, Si (%) + Al (%) ≥ 1.0, the balance is Fe and unavoidable impurities, and the residual austenite is at least 5% by volume and 3-20% −
A hot-rolled high-strength steel sheet excellent in workability having a tensile strength of 690 N / mm ² or less, characterized by having a structure comprising polygonal ferrite and bainite, including light. 3. C: 0.05 to 0.25% by weight, Si:
2.0% or less, Al: 1.6% or less, Mn: 0.8 to 2.0%,
Ti: 0 to 0.04%, N: 0.0100% or less,
Nb: Less than 0.003%, Si (%) + Al (%) ≥ 1.0, and the remainder is made of steel and unavoidable impurities, heated to 1100 ° C or higher, hot rolled, and finished. After finishing the hot rolling at a temperature of ₃ points or more, air-cooling is performed for 1 to 5 seconds, and then 550 to 65 at a cooling rate of 30 ° C./s or more.
After cooling to 0 ° C. and further air cooling for 2 to 10 seconds,
It is cooled to a temperature of 350 to 520 ° C. again at a cooling rate of 30 ° C./s or more, and is wound, and contains 5% or more of retained austenite by volume and 3 to 20% of pearlite. A method for producing a hot-rolled high-strength steel sheet having a structure composed of polygonal ferrite and bainite and having excellent tensile workability of 690 N / mm ² or less. 4. C: 0.05 to 0.25% by weight, Si:
2.0% or less, Al: 1.6% or less, Mn: 0.8 to 2.0%,
Including Ti: 0-0.04%, Ca: 0.0002-0.01%,
Zr: 0.01 to 0.10%, Rare earth element: One or more of 0.002 to 0.10%, N: 0.0100% or less, Nb:
A steel slab that satisfies each condition of less than 0.003%, Si (%) + Al (%) ≥ 1.0 and the balance is made of Fe and inevitable impurities
Hot rolling is performed by heating to 100 ° C. or more, and finishing temperature Ar ₃
After performing hot rolling at 1 point or more and performing air cooling for 1 to 5 seconds, cooling to 550 to 650 ° C. at a cooling rate of 30 ° C./s or more, and further performing air cooling for 2 to 10 seconds, Again 3
It is cooled to 350 to 520 ° C. at a cooling rate of 0 ° C./s or more, and is wound up. The residual volume containing 5% or more of retained austenite and 3 to 20% of pearlite by volume ratio remains. A method for producing a hot-rolled high-tensile steel sheet having a structure comprising polygonal ferrite and bainite and having excellent tensile workability of 690 N / mm ² or less.