JP2005105399A - Method for manufacturing low-yield-ratio high-strength galvannealed steel - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a low-yield-ratio high-strength galvannealed steel with the use of a steel containing comparatively few alloying elements, which does not include a precipitate-forming element. <P>SOLUTION: A steel slab has a composition including 0.03-0.18 mass% C, 0.2-2.0 mass% Si, 0.5-3.0 mass% Mn, 0.10 mass% or less P and 0.03% mass% or less S; and has a segregation degree of Mn of 1.05 to 1.10, which is defined by the following expression (1): segregation degree of Mn = (Mn concentration in slab center-average Mn concentration)/average Mn concentration --- (1). The method for manufacturing the galvannealed steel comprises hot-rolling the steel slab, further cold-rolling it, forming a Fe-based plated film with a coating weight of 3 to 15 g/m<SP>2</SP>, annealing it in a reductive gas atmosphere in a continuous plating and annealing line, immersing it in a hot-dip galvanizing bath to form a galvanized layer, and then skipping a heating step or heating it to a temperature lower than 530°C, to form a galvannealed layer on the surface of a steel sheet. <P>COPYRIGHT: (C)2005,JPO&NCIPI

Description

  The present invention relates to a method for producing a low yield ratio high strength alloyed hot dip galvanized steel sheet for automobile steel sheets, building structural members, and home appliances.

2. Description of the Related Art In recent years, thinning of steel plates for automobiles has been attempted for the purpose of improving fuel consumption associated with weight reduction of automobiles. On the other hand, laws and regulations on automobile crash safety have been strengthened, and it has come to be required that steel sheets for automobiles have excellent impact toughness as well as high strength and thinness. This trend is spreading not only in the automobile industry but also in the fields of housing, building materials and home appliances.
By the way, in general, the strength and ductility of a steel sheet are contradictory properties, and when attempting to increase the strength, the ductility is deteriorated and the impact toughness is extremely reduced. Further, a high strength steel sheet employing precipitation hardening means that is considered to be the most effective as means for increasing strength has a problem that the amount of elastic recovery after deformation processing is large and the shape freezing property is not good.

From these technical problems, a technique using retained austenite has been proposed as a conventional technique focusing on a high-tensile steel sheet exhibiting high ductility.
In Patent Document 1, after heating a steel sheet containing C: 0.30 to 0.55%, Si: 0.7 to 2.0%, Mn: 0.5 to 2.5% to an austenite single phase region, By holding at 650 to 750 ° C. for 4 to 15 seconds, and subsequently holding at 450 to 650 ° C. in the subsequent cooling process for a total of 10 to 50 seconds, “10% or more by volume in martensite or bainite” It has been proposed to obtain a “high-strength steel sheet exhibiting high ductility” by causing the appearance of a “mixed structure containing ferrite and retained austenite”.

In Patent Document 2, in addition to C: 0.12 to 0.55%, Si: 0.4 to 1.8%, Mn: 0.2 to 2.5%, if necessary, an appropriate amount of P, Ni, A steel sheet containing one or more of Cu, Cr, Ti, Nb, V and Mo is heated to a “ferrite + austenite single phase region” and then held at a temperature range of 500 to 350 ° C. during the cooling for 30 seconds to 30 minutes. By doing so, it has been proposed to obtain a “high-tensile steel sheet exhibiting high ductility” by causing a “ferrite + bainite + residual austenite mixed structure” to appear.
Further, Patent Document 3 proposes a Si-added type retained austenite-containing steel sheet that uses Si as an element for suppressing carbide formation and stabilizing retained austenite. Patent Document 3 also shows that the impact resistance is further improved by adding Ti and Nb to form carbonitrides thereof.

JP 60-43464 A JP-A 61-157625 JP-A-6-145808

However, the technologies proposed in Patent Documents 1 and 2 ensured high ductility by utilizing “a phenomenon in which retained austenite undergoes strain-induced transformation during deformation during processing and exhibits large elongation (transformation-induced plasticity)”. Is. Therefore, in order to increase the strength with a low yield ratio type, it is necessary to increase Si, Mn, etc. within a specified range. When the amount of Si and Mn is relatively large and the strength is low yield ratio type, the properties such as weldability and impact toughness are deteriorated, making industrial practicality difficult. In addition, in the use of precipitates by addition of Ti and Nb as in the technique proposed in Patent Document 3, the yield strength increases and the amount of elastic recovery after deformation processing increases.
The present invention has been devised to solve such a problem, and a low yield ratio type high strength alloyed hot dip galvanized steel sheet is obtained by using a relatively low component steel that does not contain precipitate forming elements. The purpose is to obtain.

The production method of the low yield ratio type high-strength galvannealed steel sheet according to the present invention achieves the object, C: 0.03-0.18 mass%, Si: 0.2-2.0 mass% , Mn: 0.5 to 3.0% by mass, P: 0.10% by mass or less, S: 0.03% by mass or less, and Mn segregation degree defined by the following formula (1) A slab having a thickness of 1.05 to 1.10 was hot-rolled and further cold-rolled, and then an Fe-based plating layer having an adhesion amount of 3 to 15 g / m ² was formed and subjected to gas reduction annealing in a continuous annealing plating line. After that, it is immersed in a hot dip galvanizing bath to perform plating, and after that, without heating or by heating to less than 530 ° C., alloying treatment is performed to form an alloyed galvanized layer on the steel sheet surface. To do.
Mn segregation degree = (slab center part Mn concentration−base Mn concentration) / base Mn concentration (1)

  Further, in the above method, after forming the Fe-based plating layer, it is heated in a two-phase region or a single-phase region at 750 to 870 ° C. in a continuous annealing plating line for 60 seconds or more, and then an average cooling rate of 20 ° C./s. The steel sheet after cooling to 350 to 490 ° C. and holding at that temperature range for less than 20 minutes is hot-dip galvanized and then alloyed, and cooled to room temperature. You may make it become the 4 structure | tissue of nulferrite + ashular ferrite + bainite + martensite.

The inventors of the present invention have intensively studied paying attention to the impact absorption characteristics of the steel sheet. In the process, in low-component steels with relatively low C, Mn, P, and S contents, the content of each component is regulated within an appropriate range, and the segregation of slabs that has been avoided in the past is used. Thus, the inventors have found new knowledge that low yield ratio can be achieved while securing high strength even in low component steels.
That is, the band-like structure after hot rolling caused by Mn segregation of the slab creates segregation of C concentration in the austenite by the subsequent continuous annealing condition, and the transformation in the continuous annealing is delayed and the amount of martensite increases. Thus, high strength was obtained even with a low component system.

In addition, when performing hot dipping, since the diffusion of Zn plating layer and Fe is inhibited if Si and Mn are contained in the steel, the heating temperature when alloying the plating layer and the steel sheet is increased. Need arises. When the heating temperature is increased, pearlite is generated in the steel, and the strength and ductility in the steel are deteriorated.
The inventors of the present invention studied various methods for reducing the alloying temperature when manufacturing an alloyed hot-dip galvanized steel sheet using a steel sheet containing Si and Mn as a raw material. As a result, the alloying heating temperature could be greatly reduced by applying Fe-based plating that does not contain an element that hinders alloying with the Zn plating layer on the steel sheet.

In producing the low yield ratio high strength alloyed hot dip galvanized steel sheet of the present invention, the component composition of the steel is first determined as follows.
C: 0.03-0.18 mass%
C is an element effective for increasing the strength of steel, and the effect cannot be obtained unless the content is less than 0.03% by mass. On the other hand, when the content exceeds 0.18% by mass, not only the spot weldability is deteriorated, but also the strength is excessively increased and the workability is extremely deteriorated.

Si: 0.2-2.0 mass%
In addition to being effective for increasing the strength, Si is an element that has the effect of suppressing the precipitation of cementite and the effect of suppressing the formation of pearlite and the like in steel. The effect is not exhibited unless it is less than 0.2% by mass. On the other hand, when the concentration exceeds 2.0 mass%, not only the effect is saturated, but also the Si diffusion phenomenon during annealing is remarkable, and even if Fe-based plating is applied, a Si oxide film layer is formed on the surface layer. As a result, the temperature required for alloying increases.

Mn: 0.5 to 3.0% by mass
Mn is an element that ensures hardenability and is effective in increasing strength. The effect is not exhibited unless it is less than 0.5 mass%. On the other hand, if the content exceeds 3.0% by mass, the hardenability of the steel sheet is excessively increased to cause an excessive increase in strength and a decrease in ductility, and spot weldability is also deteriorated. Further, even if Fe plating is performed in the same manner as Si, an oxide film is formed on the surface layer, and the alloying temperature is increased.

P: 0.10% by mass or less P is an element that affects the formation of ferrite in the same way as Si. However, when P exceeding 0.10% by mass is contained, ductility deterioration becomes remarkable. Accordingly, the upper limit of the P content is 0.10% by mass.
S: 0.03% by mass or less S causes a deterioration in workability because a large number of A-based compounds are produced with an increase. And this tendency becomes remarkable when S content exceeds 0.03 mass%. For this reason, the upper limit of S content was 0.03 mass%. Preferably it is 0.002 mass% or less.

Except for Al added as a deoxidizer, the components other than those described above are impurities. Cr, Mo, V, Ti, Nb and the like are not added because they may affect the strength. The present invention is characterized in that a refinement effect and an increase in strength are obtained by segregation without adding an expensive alloy element.
Mn segregation degree: 1.05-1.10
The Mn segregation degree represented by the following formula (1) is the greatest characteristic point of the present invention. In a state where there is little segregation such that this value is less than 1.05, the strength of the cold rolled steel sheet is insufficient, and conversely, in a severe segregated state so as to exceed 1.10, the strength of the cold rolled steel sheet increases rapidly, Yield ratio increases and material stability is lacking. In the present invention, the optimum range of the degree of segregation of Mn is confirmed by repeating such an experiment as described later.
Mn segregation degree = (slab center part Mn concentration−base Mn concentration) / base Mn concentration (1)
The Mn segregation degree is determined by continuous casting by adjusting / changing electromagnetic stirring conditions, casting speed conditions, etc., when molten steel having the above composition is melted in a converter as usual and slabs are produced by continuous casting. It is adjusted by controlling the conditions.

After continuous casting, a slab in which Mn is segregated to a segregation degree of 1.05-1.10 is formed, and then hot rolling is performed while it is hot, or after being cooled to room temperature, hot rolling is performed. To obtain a hot-rolled steel sheet. The hot rolling may be performed under normal conditions without any limitation on the soaking temperature, the rolling temperature, etc. From the viewpoint of the load during cold rolling and the pickling property, the rolling after hot rolling is 500 A temperature of ˜650 ° C. is preferable.
The wound hot rolled coil is then pickled as usual and then subjected to cold rolling. Although it is not necessary to specifically limit the cold rolling conditions, the cold rolling rate is preferably set to 30% or more in consideration of the sheet passability during the cold rolling.

Fe-based plating is formed in the range of ^{3 to} 15 g / m ² of adhesion amount. When the coating weight is less than 3 g / m ² , alloying does not proceed sufficiently only in the Fe-based plating layer, so diffusion from the steel in which Mn and Si are present is necessary, and alloying at less than 530 ° C. It becomes impossible to process. The alloying temperature can be lowered as the plating adhesion amount increases at 3 g / m ² or more, and the alloying can be performed without reheating after galvanizing by making the Fe-based plating 5 g / m ² or more. You can also. However, if it exceeds 15 g / m ² , even if the Fe-based plating layer is increased, an Fe plating layer that is not used for alloying is generated, which only increases the manufacturing cost.

When annealing a steel sheet with Fe-based plating in a continuous annealing line, it is necessary to concentrate C in austenite, so it is necessary to heat in a two-phase region or a single-phase region at 750 to 870 ° C. . It is preferable to heat at a two-phase temperature. Further, in order to re-dissolve carbides generated by hot rolling and to concentrate C in austenite, the heating and holding time in recrystallization annealing needs to be 60 seconds or more.
When a steel sheet having an austenite structure enriched with C is gradually cooled at an average cooling rate of 20 ° C./s or less, polygonal ferrite is first produced from austenite, and then ashular ferrite is produced. After cooling to 350 to 490 ° C., it is kept for 20 minutes or less in that temperature range, and then hot dip galvanized and subsequent alloying treatment is performed. When such cooling is applied, the structure of the steel sheet cooled to room temperature after the alloying treatment is four structures of polygonal ferrite + ashular ferrite + bainite + martensite, and the yield ratio is maintained while ensuring high strength. A small galvannealed steel sheet is obtained.
If the holding time is 20 minutes or more, the bainite transformation proceeds too much, and the amount of martensite finally produced decreases, and the desired strength cannot be obtained.
The alloying treatment after hot dip plating is performed at a temperature of less than 530 ° C. When the temperature is 530 ° C. or higher, pearlite is generated in the steel, leading to a decrease in ductility.

Slabs having a Mn segregation degree of about 1.0 to about 1.2 were manufactured by continuous casting in which steels having various component compositions were melted by a converter and the casting conditions were appropriately adjusted.
Once cooled to room temperature, it was soaked again to 1250 ° C., hot-rolled at 1150-930 ° C., wound up at 600 ° C., and a 2.4 mm thick hot-rolled steel sheet was obtained.
Next, after the obtained hot-rolled steel sheet was pickled, it was cold-rolled to obtain a cold-rolled steel sheet having a thickness of 1.2 mm. Table 1 shows the components and composition of the obtained cold-rolled steel sheet and the degree of Mn segregation at the slab stage.
Next, an Fe-based plating layer was formed by electroplating under the plating conditions shown in Table 2.
Furthermore, annealing, hot dipping, and alloying treatment were performed under the conditions shown in Table 3.

Each plated steel sheet was examined for alloying state and tensile properties.
In the alloying state, the cross section of the plating layer was observed, and the case where there was no η-Zn phase in the plating layer was evaluated as ◯.
In the tensile test, the tensile properties at room temperature were investigated using a JIS No. 5 tensile test piece cut out in parallel with the rolling direction.
The results are shown in Table 4.

As can be seen from the survey results in Table 4, after having a predetermined component and composition, adjusting the Mn segregation degree within a predetermined range, and performing Fe-based plating of 3 to 15 g / m ² in advance, Test No. in which continuous annealing hot dip plating was performed under the same conditions. All of the alloyed hot-dip galvanized steel sheets 1 to 14 were in a good alloyed state and exhibited a low yield ratio.
On the other hand, test No. using a steel type h having a low degree of segregation of Mn. 15 is a test No. using a steel type a having an almost equivalent composition. Compared with 1, TS is extremely low. Test No. using steel type i with high Mn segregation degree. No. 16 has a higher yield ratio.
Test No. 1 using steel types j and k containing Si or Mn in a specified amount or more. In Nos. 17 and 18, alloying was not possible at a predetermined alloying temperature. Furthermore, test No. with less Fe-based plating adhesion amount. 19 was not alloyed at a predetermined alloying temperature.

As described above, according to the present invention, in the low-component steel in which the contents of C, Mn, P, and S are relatively low, the content of each component is regulated to an appropriate range, and then the cast slab When an appropriate Mn segregation is caused and continuous annealing and subsequent alloying hot dip plating are performed by making the best use of this Mn segregation, an alloyed hot dip galvanized steel sheet having a low yield ratio is obtained while ensuring high strength. Can do.
Therefore, it is possible to provide an alloyed hot-dip galvanized steel sheet that is optimal for automobile steel sheets, building structural members, and home appliances.

Claims (2)

C: 0.03-0.18 mass%, Si: 0.2-2.0 mass%, Mn: 0.5-3.0 mass%, P: 0.10 mass% or less, S: 0.03 A slab having a composition of not more than% by mass and having a Mn segregation degree defined by the following formula (1) of 1.05 to 1.10 is hot-rolled and further cold-rolled. After forming a 15 g / m ² Fe-based plating layer and subjecting it to gas reduction annealing in a continuous annealing plating line, it is immersed in a hot dip galvanizing bath for plating, and then heated without heating or below 530 ° C. And producing a low-yield ratio type high-strength galvannealed steel sheet characterized by forming an alloyed galvanized layer on the steel sheet surface.
Mn segregation degree = (slab center part Mn concentration−base Mn concentration) / base Mn concentration (1)   After forming the Fe-based plating layer, it is heated in a continuous annealing plating line in a two-phase region at 750 to 870 ° C. or a single phase region for 60 seconds or more, and then 350 to 490 at an average cooling rate of 20 ° C./s or less. After cooling to 0C and holding for 20 minutes in that temperature range or less, after hot dip galvanizing and subsequent alloying treatment, the steel sheet structure after cooling to room temperature is polygonal ferrite + ash The method for producing a low yield ratio type high strength alloyed hot-dip galvanized steel sheet according to claim 1, wherein the structure has four structures of ferrite + bainite + martensite.