JP3536412B2 - High strength hot rolled steel sheet excellent in workability and method for producing the same - Google Patents

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION This invention is excellent in workability, tensile strength, especially having excellent stretch flangeability a manufacturing method thereof and 500 MPa class or higher high strength hot rolled steel sheet.

[0002]

2. Description of the Related Art In recent years, hot rolled steel sheets having higher strength have come to be used in the field of automobiles against the backdrop of an increasing tendency to reduce the weight of members. For applications in which such high-strength hot-rolled steel sheets for automobiles are used, workability represented by press forming, particularly stretch flangeability, is required.

Conventionally, such hot-rolled steel sheet having excellent workability and a method for producing the hot-rolled steel sheet are disclosed in, for example, Japanese Patent Publication No. 61-11291 (a method for producing a high-strength hot-rolled steel sheet having a low yield ratio due to a mixed structure). and it is like, dual Fe size (dual
Pase) steel called a two-phase mixed structure steel of ferrite and martensite, for example, Japanese Patent Publication No. 6-4161
Publication No. 7 (Method for manufacturing hot rolled high strength steel sheet with excellent workability)
As disclosed in US Pat. No. 5,968,839, there is known a means for forming a three-phase mixed structure steel of ferrite, austenite and bainite called retained austenite steel.

However, although these steel sheets are excellent in ductility, microcracks are likely to occur at the interface between the second phase such as martensite and austenite and the ferrite phase during processing such as punching and shearing, and thus the stretch flangeability is inferior. There was a problem.

Further, for the purpose of improving the stretch flangeability, a means of forming a ferrite bainite structure is disclosed in, for example, Japanese Patent Laid-Open No. 6-49591 (High-strength hot-rolled steel sheet excellent in workability and its manufacturing method). Proposed and disclosed.
However, this steel sheet has a defect of poor ductility, and there is a problem that it cannot meet the recent demand for high stretch flangeability.

Further, each of the above-mentioned means requires low temperature winding in order to obtain a predetermined structure.
Since such low-temperature coiling is performed in a region where the heat transfer coefficient of cooling changes greatly, it is difficult to obtain a predetermined structure over the entire length of the coil, a shape defect is likely to occur, and the yield of steel sheet is likely to decrease. There are also problems such as.

[0007]

SUMMARY OF THE INVENTION In view of the above-mentioned circumstances, the present invention has a completely different concept from the conventional high-strength hot-rolled steel, and is a high-strength hot-rolled steel sheet having stretch flangeability which is far superior to the conventional one. It is an object of the present invention to propose a manufacturing method that enables stable manufacturing.

[0008]

[Means for Solving the Problems] As a result of many experiments and studies, the inventors of the present invention have found that ferrite and hard are the main causes of deterioration of stretch flangeability in ultra-low C steel (C: 0.02 wt% or less). It was found that there is a microcrack that occurs during shearing or punching due to the hardness difference with the second phase, and there is a new finding that reducing this hard second phase is most effective for improving stretch flangeability. The present invention has been achieved.

Based on the above findings, in the present invention,
In order to reduce the hard second phase, C and N, which are the factors for forming the hard second phase, are precipitated and fixed as carbonitrides of Nb and Ti in the cooling process after hot rolling to reduce the hard second phase. The decrease in strength of the steel sheet due to this is compensated by the precipitation strengthening of carbonitrides of Ti and Nb. Furthermore, by using ultra-low C steel which is one of the features of this invention, the reduction of hard second phase and Ti, It is intended to obtain a high-strength hot-rolled sheet having excellent stretch-flange formability by eliminating the harmful effects of excessive precipitation of carbonitrides of Nb.

That is, the gist of the present invention is as follows. (1) C: 0.010 wt% or more, 0.020 wt% or less ( 0.020 wt %
Excluding), Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Nb: 0.07 wt% or more, less 0.30wt%, Al: 0.01wt% or more, 0.05 wt% Below, S: 0.005 wt% or less and N: 0.005 wt% or less are contained, and Mn / Si = 0.9 to 1.6 Nb / 8 (C + 12N / 14) = 0.8 to 1.5 is contained, and the balance is Fe and unavoidable. High-strength hot-rolled steel sheet (first invention) having a metallic structure having a ferrite volume ratio of 95% or more and having excellent workability, which is composed of a composition of mechanical impurities.

(2) C: 0.010 wt% or more and 0.020 wt% or less
( Excluding 0.020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Ti: 0.15 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less , Al: 0.01 wt% or more, 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and Mn / Si = 0.9 to 1.6 (Nb + 2Ti) / 8 (C + 12N / 14) = 0.8 A high-strength hot-rolled steel sheet (2nd invention), which is contained in the range of up to 1.5, the balance is composed of Fe and inevitable impurities, and has a metal structure with a ferrite volume ratio of 95% or more and is excellent in workability.

(3) C: 0.010 wt% or more and 0.020 wt% or less
( Excluding 0.020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less, Al: 0.01 wt% or more , 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and contained in a range satisfying Mn / Si = 0.9 to 1.6 Nb / 8 (C + 12N / 14) = 0.8 to 1.5, and the balance Heats a steel material composed of Fe and inevitable impurities to a temperature range of 1000 to 1300 ° C, finishes rolling at a temperature range of Ar ₃ points to Ar ₃ points + 100 ° C, and then cools within 2 seconds. Startability, cooling the temperature range from 800 to 650 ℃ at an average cooling rate of 10 ℃ / s or more and 50 ℃ / s or less, and winding the coil in the temperature range of 500 to 650 ℃. A method for producing a high-strength hot-rolled steel sheet excellent in heat resistance (third invention).

(4) C: 0.010 wt% or more and 0.020 wt% or less
( Excluding 0.020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Ti: 0.15 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less , Al: 0.01 wt% or more, 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and Mn / Si = 0.9 to 1.6 (Nb + 2Ti) / 8 (C + 12N / 14) = 0.8 contained in a range satisfying 1.5, remainder heats the steel material consisting of Fe and unavoidable impurities to a temperature range of 1000 to 1300 ° C., the rolling at a temperature range of Ar ₃ point to Ar ₃ point +100 ° C. After completion, cooling is started within 2 seconds, and the temperature range from 800 to 650 ℃ is cooled at an average cooling rate of 10 ℃ / sec or more and 50 ℃ / sec or less, and the coil is cooled in the temperature range of 500 to 650 ℃. A method for producing a high-strength hot-rolled steel sheet having excellent workability, which is characterized by being rolled up (4th invention).

The heating temperature (T) of the steel material depends on the contents of C, Nb and N of the steel material (% C) and (% N, respectively).
The following formula (1) or (2) expressed as b) and (% N)
A method for producing a high-strength hot-rolled steel sheet having excellent workability according to the third or fourth invention (5th invention). (Note) -6770 / (log [(% Nb)] [(% C) +12 (% N) / 14] -2.26) -273 ≤ T ... (1) -6770 / (log [(% Nb) ] ((% C) +12 (% N) / 14) -2.26) -173 ≧ T ‥‥ (2)

[0015]

The function of the present invention will be described in detail below. First,
The reasons for limiting the component composition of the present invention will be described below.

C: 0.010 to 0.020 wt % ( excluding 0.020 wt %
C ) C is an important component to combine with Ti and Nb to form a carbide and obtain a predetermined strength. For that purpose, 0.010 wt%
It is necessary to contain the above, but in relation to Ti, Nb and the amount of N, (Nb + 2Ti) / 8 (C + 12N / 14)
= 0.8 to 1.5 is satisfied, ferrite volume ratio 95
% Or more, and excellent stretch flangeability cannot be obtained. At this time, if the C content is large, a large amount of
It is necessary to add Nb and Ti, and when the C content exceeds 0.020 wt%, not only the increase in strength saturates, but also the presence of a large amount of carbonitrides of Ti and Nb deteriorates ductility and stretch flangeability.
Therefore, its content is 0.010 wt% or more, 0.020 wt%
Below.

In the present invention, the volume fraction of ferrite in the hot rolled sheet is 95% or more. This is because when the volume fraction of ferrite is less than 95%, the hard second phase is present, so microcracks are likely to occur during processing such as punching and shearing, and stretch flangeability is poor.

Si: 0.5-2.0 wt%, Mn: 0.45-3.2 wt% Si is an effective component for increasing the strength without deteriorating the ductility and stretch-flangeability, and at the same time, the content of C in the ferrite. It has a function of expanding the solid solubility limit and delaying the formation of a hard second phase such as pearlite in the cooling process after hot rolling. In order to exert these characteristics, the content must be 0.5 wt% or more, but if the content exceeds 2.0 wt%, the surface properties of steel deteriorate. Therefore, its content is 0.5 wt%
As described above, the content is 2.0 wt% or less, but the upper limit is preferably 1.5 wt% from the viewpoint of surface texture.

Mn is required as a solid solution strengthening component to secure the required strength of the steel sheet, and at the same time, it has the effect of lowering the transformation temperature of the steel and refining the precipitation of carbonitrides of Ti and Nb. This point also contributes to the increase in strength. However, if added excessively, it becomes impossible to completely precipitate and fix C and N as carbonitrides of Ti and Nb in the cooling and winding process after hot rolling, which deteriorates stretch flangeability.

On the other hand, the above-mentioned Si has the effect of increasing the transformation temperature of the steel sheet as opposed to Mn and coarsening the precipitation of carbonitrides of Ti and Nb, and reduces the precipitation strengthening. Therefore, in this invention, in particular, in order to effectively utilize both the precipitation strengthening of Ti and Nb and the solid solution strengthening of Si, the relationship between the Si content and the Mn content is defined as Mn.
/Si=0.9 to 1.6, and correspondingly, the lower limit of Mn content is 0.45 wt% and the upper limit is 3.2 wt%. However, the more preferable range is Mn / Si = 1.0 to 1.2.
Correspondingly, the preferable Mn content is 0.5 wt% or more and 1.8 wt% or less.

Ti: 0.15 wt% or less, Nb: 0.07 to 0.30 wt% Ti, Nb is a component that plays an important role in the present invention. That is, these components precipitate and fix C that causes the hard second phase, contribute to the improvement of stretch flangeability, and contribute to the strength increase of the steel sheet by precipitation strengthening.
Therefore, as described in section C above, (Nb + 2Ti) / 8
(C + 12N / 14) = 0.8 to 1.5 is contained.

At this time, Ti and Nb have the same effect, but from the knowledge that Nb is more advantageous in ductility and stretch flangeability, it is essential to add Nb, and Ti is substituted for part of its role. From the relationship with the C content, the Nb content is 0.07 wt%
As described above, the content is 0.30 wt% or less, and the Ti content is 0.15 wt% or less. A more preferable relationship between C, N and Ti, Nb is
(Nb + 2Ti) / 8 (C + 12N / 4) = 1.0 to 1.2.

Al: 0.01 to 0.05 wt% Al is a component necessary for cleaning steel, and for that purpose, it is necessary to contain 0.01 wt% or more. However, if added excessively, it will cause surface defects due to alumina clusters, so the upper limit of its content is 0.05 wt%.
And

S: 0.005 wt% or less S bonds with Mn to form non-metallic inclusions, deteriorating stretch flangeability. Therefore, it is preferable that the content is small, and the allowable upper limit of the content is 0.005 wt%, but preferably 0.003 wt% or less.

N: 0.005 wt% or less N is preferentially combined with Ti and Nb added to combine with C, and reduces effective Ti and Nb. Therefore, it is preferable that the content is small, and the upper limit of the allowable content is set.
The amount is 0.005 wt%, but preferably 0.003 wt% or less.

Next, the reasons for limiting the manufacturing conditions of the hot-rolled steel sheet of the present invention will be described.

Heating temperature of steel material (SRT): for melting coarse carbonitrides of Ti and Nb generated during solidification in casting,
To secure a predetermined rolling finish temperature, heating at 1000 ° C or higher is required. However, excessive heating deteriorates the properties of the steel surface, so the upper limit is set to 1300 ° C. More preferably, the temperature T is represented by the following formula (1) or (2) in which Ti and Nb are completely dissolved and abnormal grain growth of crystals does not occur. -6770 / (log [(% Nb)] [(% C) +12 (% N) / 14] -2.26) -273 ≤ T ... (1) -6770 / (log [(% Nb)] [( % C) +12 (% N) / 14) -2.26) -173 ≧ T ‥‥ (2)

The hot rolling conditions of the present invention include the case where the continuous casting slab is once cooled and then reheated for rough rolling, and from the viewpoint of energy saving, the temperature is not lowered to 1000 ° C. or lower after continuous casting. The rough rolling may be carried out immediately or after heat insulation treatment.

Rolling end temperature (FDT): In order to refine the crystal grains, the rolling end temperature is preferably low enough not to cut Ar ₃ transformation, and is set to a temperature range of Ar _{3 to} Ar ₃ + 100 ° C.

Air cooling time after completion of rolling until forced cooling: The effect of grain refinement is greater if forced cooling is started immediately after completion of rolling. However, air cooling time occurs due to the structure of the hot rolling mill. Therefore, the air cooling time is suppressed within 2 seconds. Desirably within 0.5 seconds.

Cooling rate until winding: If the cooling rate is too slow, after ferrite transformation, the ferrite grains grow and coarsen, and at the same time, the carbonitrides of Ti and Nb also coarsen, and the crystal grains and carbonitrides become fine. The improvement effect of strength due to the increase in strength cannot be expected. Therefore, in order to prevent coarsening of ferrite grains and carbonitrides of Ti and Nb, the average cooling rate from 800 ° C to 650 ° C is set to 10 ° C / sec or more. Also, if the cooling rate is too fast, precipitation of Ti and Nb does not occur sufficiently and the hard second layer increases due to the increase of solid solution C, which deteriorates stretch flangeability. Therefore, the upper limit of the average cooling rate is 50 ° C / sec. And

Winding temperature (CT): The higher the winding temperature is Ti, Nb
However, if it is too high, it becomes a coarse precipitate and does not contribute to the strength improvement. Therefore, the upper limit of the coiling temperature is 650 ℃. On the other hand, if the coiling temperature is too low, Ti and Nb precipitates will not be generated sufficiently, and the hard second phase will increase, deteriorating the stretch flangeability. Therefore, the lower limit of the coiling temperature is 500 ° C.

[0033]

[Examples] Using steel materials having various compositional compositions shown in Table 1, under the hot rolling conditions shown in Table 2, each coil having a plate thickness of 3.0 mm was manufactured, and the mechanical properties of the obtained coils were measured. Were investigated respectively. The survey results are also shown in Table 2.

[0034]

[Table 1]

[0035]

[Table 2]

From the above results, Mn / Si and TS x λ (M
The graph of the relationship with (Pa ·%) is shown in Fig. 1, (Nb + 2Ti) / 8
A graph of the relationship between the value of (C + 12N / 14) and TS × λ (MPa ·%) is shown in FIG.

Among the mechanical properties, the tensile property is JI.
Tested using S5 test piece, stretch flangeability is 200m in length and width
A 20 mmφ hole (do) is made in the center of a square m test piece, this hole is expanded with a conical punch with a tip angle of 60 °, and the limit diameter (d) at which cracks occur at the edge of the hole is calculated using the following formula. It was evaluated by the hole expansion ratio (λ). λ = (d-do) / do × 100

As is clear from Table 2, sample No. 3,
4,6,7,8,10,16,21,23 and 24 are the conforming examples of this invention, which have high strength and ductility balance with TS × El exceeding 1800 MPa ·% and high TS × λ exceeding 6000 MPa ·%. The balance between strength and stretch-flangeability is shown. According to the metallographic examination, they all have a ferrite volume ratio of 95% or more.

On the other hand, samples No. 1, 2, 17, 18,
In the comparative examples of 19, 20, 22, 25 and 27, the composition was out of the limited range of the present invention, so that high strength, ductility, stretch flangeability, etc. were not obtained, and sample Nos. 9, 11, 12 , 13, 14
In Comparative Examples 15 and 15, the hot rolling, cooling, and winding conditions are out of the limits of the present invention, and thus high strength, ductility, stretch flangeability, etc. are not obtained as in the above. Also,
The comparative examples of Sample Nos. 5 and 26 could not be used for automobiles and the like which are the objects of the present invention because the surface properties of the steel sheet were extremely poor.

On the other hand, as is apparent from FIGS. 1 and 2, when Mn / Si is within the range of the present invention, (Nb + 2Ti) / 8 (C +
When 12N / 14) is within the range of the present invention, high strength and stretch flangeability balance are exhibited.

[0041]

EFFECTS OF THE INVENTION The present invention is to contain Si and Mn in a well-balanced manner in C: 0.01 to 0.02% low carbon steel,
A high-strength hot-rolled steel sheet having excellent workability is obtained by fixing C as a precipitate of Nb and Ti. The steel sheet according to the present invention is excellent in strength, ductility, and stretch-flangeability, and is a foot of automobiles. It can be stably and advantageously provided as a high-strength hot-rolled steel sheet for processing, which is suitable for a rotating component and the like.

[Brief description of drawings]

FIG. 1 is a graph showing the relationship between Mn / Si and TS × λ.

[Figure 2] (Nb + 2Ti) / 8 (C + 12N / 14) value and TS ×
It is a graph which shows the relationship with (lambda).

─────────────────────────────────────────────────── --Continued from the front page (56) References JP-A-6-200351 (JP, A) JP-A-4-263022 (JP, A) JP-A-61-3844 (JP, A) (58) Field (Int.Cl. ⁷ , DB name) C22C 38/00-38/60 C21D 9/46

Claims (5)

(57) [Claims] 1. C: 0.010 wt% or more and 0.020 wt% or less ( 0.
020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less, Al: 0.01 wt% or more, 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and Mn / Si = 0.9 to 1.6 Nb / 8 (C + 12N / 14) = 0.8 to 1.5 A high-strength hot-rolled steel sheet having a composition of Fe and unavoidable impurities and having a metal structure with a ferrite volume ratio of 95% or more and excellent workability. 2. C: 0.010 wt% or more and 0.020 wt% or less
( Excluding 0.020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Ti: 0.15 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less , Al: 0.01 wt% or more, 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and Mn / Si = 0.9 to 1.6 (Nb + 2Ti) / 8 (C + 12N / 14) = 0.8 A high-strength hot-rolled steel sheet having a metal structure having a volume fraction of ferrite of 95% or more, which has a composition of Fe and unavoidable impurities, and which is contained in the range of up to 1.5. 3. C: 0.010 wt% or more and 0.020 wt% or less
( Excluding 0.020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less, Al: 0.01 wt% or more , 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and contained in a range satisfying Mn / Si = 0.9 to 1.6 Nb / 8 (C + 12N / 14) = 0.8 to 1.5, and the balance Heats a steel material composed of Fe and inevitable impurities to a temperature range of 1000 to 1300 ° C, finishes rolling at a temperature range of Ar ₃ points to Ar ₃ points + 100 ° C, and then cools within 2 seconds. Startability, cooling the temperature range from 800 to 650 ℃ at an average cooling rate of 10 ℃ / s or more and 50 ℃ / s or less, and winding the coil in the temperature range of 500 to 650 ℃. A method for producing a high-strength hot-rolled steel sheet excellent in heat resistance. 4. C: 0.010 wt% or more and 0.020 wt% or less
( Excluding 0.020 wt %) , Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.45 wt% or more, 3.2 wt% or less, Ti: 0.15 wt% or less, Nb: 0.07 wt% or more, 0.30 wt% or less , Al: 0.01 wt% or more, 0.05 wt% or less, S: 0.005 wt% or less and N: 0.005 wt% or less, and Mn / Si = 0.9 to 1.6 (Nb + 2Ti) / 8 (C + 12N / 14) = 0.8 contained in a range satisfying 1.5, remainder heats the steel material consisting of Fe and unavoidable impurities to a temperature range of 1000 to 1300 ° C., the rolling at a temperature range of Ar ₃ point to Ar ₃ point +100 ° C. After completion, cooling is started within 2 seconds, and the temperature range from 800 to 650 ℃ is cooled at an average cooling rate of 10 ℃ / sec or more and 50 ℃ / sec or less, and the coil is cooled in the temperature range of 500 to 650 ℃. A method for producing a high-strength hot-rolled steel sheet having excellent workability, which is characterized in that 5. The heating temperature (T) of the steel material depends on the contents of C, Nb and N of the steel material (% C) and (% Nb), respectively.
And a method of manufacturing a high-strength hot-rolled steel sheet having excellent workability according to claim 3 or 4, which satisfies the following formula (1) or (2) expressed as (% N).