JP2007169679A - Steel sheet for hot forming having excellent joining strength in spot weld zone and hot formability, and hot formed article - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a steel sheet for hot forming which is improved in strength in a joint at spot welding and allows excellent forming without causing breaks, cracks, etc., at hot forming, and to provide a hot formed article or the like to be formed using such a steel sheet. <P>SOLUTION: The steel sheet for hot forming contains 0.1 to 0.35% C, 0.7 to 2.5% Si, 0.5 to 5% Mn, 0.005 to 0.5% Al, 0.005 to 0.05% Ti, 0.003 to 0.005% B, 0.001 to 0.01% N and the balance Fe with inevitable impurities, and satisfies the relationship in inequality ([Ti]/47.9)×14.0-[N]≥0(mass%) (wherein [Ti] and [N] represent the respective contents (mass%) of Ti and N, respectively). <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

In the field of manufacturing a thin steel sheet molded product mainly applied to an automobile body, the present invention heats a steel plate (blank) as a raw material to austenite + ferrite temperature (Ac ₁ transformation point) or higher and then presses hot. The present invention relates to a base steel plate (hot forming steel plate) used when manufacturing a molded product by molding, and a hot molded product formed by such a steel plate. The present invention relates to a steel sheet, a hot-formed product, and the like that can realize good forming without being generated and have excellent joint strength at a welded portion when spot welding is performed.

  In automotive parts, in order to achieve both collision safety and weight reduction, the strength of parts materials is being increased. Such parts are generally manufactured by press-molding a steel plate. However, when cold working is performed on a high strength steel sheet, it is particularly difficult to form a material having a tensile strength exceeding 980 MPa.

  For these reasons, studies on hot forming technology for forming a raw steel sheet in a heated state are being conducted. As such a technique, for example, Patent Document 1 proposes a technique of forming a metal material using a relatively low-temperature press mold in a state where the metal material is heated to 850 to 1050 ° C. According to this technique, it is said that the moldability of the metal material becomes better and the occurrence of delayed fracture due to residual stress can be prevented. In particular, it is possible to obtain a part having a strength equivalent to that obtained when a high-strength steel plate having a tensile strength of 1470 MPa, which has been difficult to form by a normal cold pressing method, is used as a material, and also has a good dimensional accuracy. Become.

  FIG. 1 is a schematic explanatory view showing a mold configuration for carrying out hot forming as described above (hereinafter sometimes referred to as “hot stamp”), in which 1 is a punch, 2 is a die, 3 is a blank holder (wrinkle presser), 4 is a steel plate (blank), BHF is a wrinkle presser force, rp is a punch shoulder radius, rd is a die shoulder radius, and CL is a punch / die clearance. Of these mold parts, the punch 1 and the die 2 are formed with passages 1a and 2a through which a cooling medium (for example, water) can pass, and the cooling medium passes through the passages. These members are configured to be cooled.

When hot stamping (for example, hot deep drawing) using the above-described mold, molding is started in a state where the blank (steel plate 4) is heated to the Ac ₃ transformation point or more and softened. That is, a shape corresponding to the outer shape of the punch 1 while pressing the steel plate 4 into the hole of the die 2 by the punch 1 while the blank 4 in a high temperature state is sandwiched between the die 2 and the blank holder 3 and reducing the outer diameter of the blank. To form. Although the temperature of the blank 4 is lowered by the punch 1 and the die 2 during molding, the material is finally quenched by holding and cooling at the bottom dead center of the molding (state shown in FIG. 1). By carrying out such a molding method, it is possible to obtain, for example, a 1470 MPa class part with good dimensional accuracy, and the molding load can be reduced compared to the case where parts of the same strength class are molded cold. The capacity of the can be small.

  As steel plates applicable to hot stamping, for example, steel plates as in Patent Documents 2 to 5 have been proposed. In these steel sheets, in order to achieve high strength by quenching in the mold after hot forming, the C content is set to about 0.2%, and at the same time, a hardenability improving element is added as necessary. It is proposed to contain. With these techniques, a steel sheet with improved hardenability after forming can be obtained. When the C content reaches the above level, the joint strength of the joint part (welded part) when spot welding is performed, particularly welding. There is a problem that the joint strength (tensile strength of the cruciform joint portion) when the force is applied to the portion in the vertical direction is lowered.

In the hot stamping technique as described above, the steel sheet is heated to a temperature higher than the austenite temperature (Ac ₃ transformation point) since it is strengthened by utilizing martensitic transformation in the rapid cooling process after forming. In general, the steel sheet is processed so that the strength of the steel sheet during the forming process becomes very small, and the dimensional accuracy after forming becomes good. However, on the other hand, because the steel sheet is too soft, breakage occurs depending on the shape of the molded product, and the shape that can be formed is limited.
JP, 2002-102980, A Claims etc. JP, 2004-197213, A Claims etc. JP, 2004-315927, A Claims etc. JP, 2004-2111197, A Claims etc. Japanese Patent No. 3389562 Patent Claim

  The present invention has been made under such circumstances, and the purpose thereof is excellent in the strength of the joint part when spot welding is performed, and without causing breakage or cracking during hot molding. An object of the present invention is to provide a hot-forming steel plate that can be formed, a hot-formed product formed by such a steel plate, and the like.

The hot-forming steel sheet of the present invention that has achieved the above object is a steel sheet used to obtain a molded product by hot forming, and C: 0.1 to 0.35% (mass% Meaning: the same applies hereinafter), Si: 0.7 to 2.5%, Mn: 0.5 to 5%, Al: 0.01 to 0.5%, Ti: 0.005 to 0.05%, B: 0.003 to 0.005% and N: 0.001 to 0.01%, respectively, satisfy the following formula (1), and the remainder is composed of Fe and inevitable impurities Is.
([Ti] /47.9) × 14.0− [N] ≧ 0 (mass%) (1)
However, [Ti] and [N] indicate the contents (mass%) of Ti and N, respectively.

  In the hot forming steel sheet of the present invention, if necessary, (a) Cr and / or Mo: 0.01 to 1% in total, (b) Nb: 0.01 to 0.1%, (c) Ni And / or Cu: It is also effective to contain 0.01 to 0.5% in total, etc., and the characteristics of the steel sheet are further improved according to the type of element contained.

Using the steel sheet of the present invention as described above, (A) the steel sheet is heated to a temperature not lower than the Ac ₃ transformation point and held at that temperature for 30 minutes or less, and then hot-formed or (B) the steel sheet After being heated to a temperature not lower than the Ac ₁ transformation point and not higher than the Ac ₃ transformation point, hot molding is obtained by hot molding.

  In the steel sheet of the present invention, by containing a relatively large amount of Si, the joint strength of the spot welded portion is improved, and deterioration of hot formability due to the inclusion of a large amount of Si is suppressed by the B content. It is possible to realize a hot-forming steel plate that does not cause breakage or cracking during forming between the two, and by using such a steel plate, a molded product with good quality can be obtained.

  The present inventor has been researching on a technique that can realize good press formability, and as part of the research, has proposed a technique of drawing with a mold shown in FIG. 14002). In this mold configuration, a pin 7 for supporting a steel plate is provided on a part of the blank holder 3, and a steel plate 4 is placed on the pin 7, whereby a steel plate is placed on the die 2 and the blank holder 3. Can be brought into close proximity without direct contact (in FIG. 2, the configuration of the other parts is basically the same as in FIG. 1). At the time of molding, the upper surface of the pin 7 is flush with the upper surface of the blank holder, and the steel plate 4 is placed on the blank holder 3.

  In the mold configuration as described above, by supporting the steel plate 4 with the pins 7 before forming, and avoiding direct contact between the steel plate 4 and the mold (particularly the die 2 and the blank holder 3), The upper surface portion of the punch 1 and most of the other portions are cooled almost simultaneously, and due to the temperature non-uniformity of the steel plate 4, the material strength on the punch surface is relatively low on the flange surface. Can be prevented. As a result, breakage particularly on the punch surface is prevented, and drawability is improved. With this technology, the hot drawability of steel sheets can be significantly improved, but it is assumed that hot drawability cannot be fully exhibited with some steel sheets and such techniques cannot be fully utilized. Is done. In addition, as described above, the steel plates that have been proposed so far also have a problem that the bonding strength when spot welding is not sufficient.

  Under such circumstances, the inventor further increased the joint strength at the spot welded portion and further examined the relationship with the chemical composition of the steel sheet with good hot drawing.

  As a result, it was found that the joint strength of the spot welded portion can be increased when the Si content is relatively large. However, if the Si content is increased, the hot formability tends to deteriorate. In view of eliminating such inconveniences, the inventors have found that if a predetermined amount of B is contained, deterioration of hot formability due to the inclusion of Si can be prevented, and the present invention has been completed. However, since the above effect is not exhibited unless B is in a solid solution state (free state), it is necessary to fix N forming B and the compound with Ti. From this viewpoint, the relationship between Ti and N is also appropriate. [Refer to the above formula (1)].

  The present inventor first uses a steel sheet in which the Si content is changed in the range of 0.2 to 2.0% based on the chemical component composition shown in Table 1 below, and performs hot rolling → pickling according to a conventional method. → Cold-rolled to a thickness of 1 mm, held at 900 ° C. for 3 minutes, then water-cooled, spot-welded, and measured for bonding strength (spot cross joint breaking load) (welding conditions and breaking load measurement method) Is the same as in Example 1 below). The result is shown in FIG. 3. By setting the Si content to 0.7% or more, the breaking load: 3.0 kN or more is achieved, and by setting the Si content to 1.0% or more, the breaking load: 3.5 kN. It can be seen that the above has been achieved.

  This inventor investigated the influence which addition of B has on hot formability about the steel plate of the chemical component composition shown in the said Table 1, and the steel plate which made only Si content 0.2%. Except for Si and B, a steel plate having the same chemical composition as in Table 1 above was used, and in accordance with an ordinary method, hot rolling → pickling → cold rolling to a thickness of 1.2 mm was maintained at 700 ° C. for 60 minutes. Then, it processed into the circular blank. At this time, the blank diameter was changed at a pitch of 2.5 mm within a range of 80 to 100 mm, and the hot formability was evaluated based on the moldable blank diameter (see Example 2 below). About each obtained circular blank, after hold | maintaining for 4 minutes in the furnace which maintained temperature at 930 degreeC, it took out from the furnace and press-molded as it was (from taking-out to shaping | molding start about 6 second). At this time, using an 80 ton crank press machine equipped with a 45 mm × 45 mm square tube mold, molding was performed under the conditions of BHF: 1 ton, molding height: 37 mm, molding speed: 40 revolutions / minute.

  The results are shown in FIG. 4 (a bar graph showing the effect of B addition). By containing B, it is understood that good formability is achieved while preventing hot formability deterioration due to Si inclusion. .

  In the steel sheet of the present invention, the above effects can be exhibited basically by controlling Si and B to appropriate amounts, but it is also useful to contain a predetermined amount of Nb if necessary. As will be described in detail later, this Nb exhibits the effect of reducing the thickness reduction rate, and as a result, it is possible to prevent breakage as much as possible.

  The inventor investigated the influence of the addition of Nb on the sheet thickness reduction rate. Of the chemical composition shown in Table 1 above, for steel sheets with B content of 0.0017%, cold rolling and annealing for steel sheets containing 0.05% Nb and steel sheets not containing Nb. The material was cut into strip-shaped blanks (length: 30 mm, width: 210 mm) and heated to 900 ° C. for experiments.

  The blank in the heated state taken out from the heating furnace is hot-formed using a 45 mm square mold with a crease presser (square tube die and square tube punch) installed in a crank press (see Fig. 2), and formed. The height was set to 37 mm, and after holding at the bottom dead center for 20 seconds, it was removed from the mold. The wrinkle pressing force at this time was 4 kN, and the molding speed was 40 revolutions / minute in terms of the number of rotations of the crank. The plate thickness reduction rate (rate in which the amount of reduction was expressed as minus) was measured at the measurement positions (1 to 13) shown in FIG. 5 (schematic diagram showing the cross section of the molded product). The result is shown in FIG. 6, and it is understood that the plate thickness reduction rate is suppressed when Nb is contained.

In the steel sheet of the present invention, it is necessary to regulate the chemical component composition while appropriately controlling the contents of Si and B described above, and it is also effective to contain Nb if necessary, but these elements are also included. The reason for limiting the range of each element defined in the present invention is as follows. C: 0.1 to 0.35%
C is an important element that determines the material strength (hardness) after hot forming, but if its content is less than 0.1%, sufficient strength (Hv300 or more) cannot be obtained after hot forming. However, if the C content is excessive and exceeds 0.35%, the strength of the part after molding becomes too high, and the deformability (ductility at the time of crushing) as a part is lowered. In addition, the minimum with preferable C content is 0.15%, and a preferable upper limit is 0.30%.

Si: 0.7-2.5%
Si is hardened and strengthened by hot forming, and it is important to improve the joint strength of spot joints, especially the joints of cross joints, for parts with high strength that are composed of martensite microscopically. It is an element. Within the range of the C content in the present invention, the effect is exhibited when the Si content is 0.7% or more with respect to the Si content (see FIG. 3). However, if the Si content exceeds 2.5%, the toughness after hot forming deteriorates. In addition, the minimum with preferable Si content is 1.0%, and a preferable upper limit is 2.0%.

Mn: 0.5-5%
Mn is an element useful for improving the hardenability of the steel sheet and reducing the variation in hardness after forming. In order to exhibit such an effect, it is necessary to contain 0.5% or more of Mn. However, even if the Mn content becomes excessive and exceeds 5%, the effect is saturated and the cost increases. In addition, the minimum with preferable Mn content is 1.0%, and a preferable upper limit is 3.5%.

Al: 0.01 to 0.5%
Al is an element useful in deoxidation of molten steel, and in order to exert its effect, its content needs to be 0.01% or more. Moreover, improvement of hot formability (deep drawability) can be expected by containing 0.01% or more of Al. In particular, the effect can be expected particularly when the material is once heated to the Ac ₃ transformation point or higher and then cooled and then heated again to the Ac ₁ transformation point or more and the Ac ₃ transformation point and then hot forming is performed as it is. However, when the Al content becomes excessive and exceeds 0.5%, the Ac ₃ transformation point rises to near 1000 ° C., and the coarsening of the steel sheet microstructure (γ grain size) due to heating becomes significant, and the resulting forming Since the toughness of the product deteriorates, it should be suppressed to 0.5% or less. In addition, the minimum with preferable Al content is 0.015%, and a preferable upper limit is 0.3%.

B: 0.0003 to 0.005%
B is an element that improves the hardenability of the steel material, but also exhibits the effect of improving the hot drawability at the same time. In the steel sheet of the present invention, the inclusion of Si increases the strength of the spot welded joint, but on the other hand, the hot formability deteriorates. However, by containing B at the same time, it is possible to further improve while preventing deterioration of hot formability (particularly deep drawability) by containing Si (see FIG. 4).

  However, B is very easily combined with N in the steel, and once it is combined with N, it hardly decomposes even when heated during hot forming. The deep drawability improving effect by B needs to exist in a free state (solid solution state) that is not bonded to other elements in the steel sheet during hot forming, so N is added to Ti by Ti addition. It is necessary to fix it as a compound and prevent binding with B. For these reasons, it is necessary to contain Ti and N in a well-balanced manner so as to satisfy the relationship of the formula (1). Further, in order to exert the above-described effects due to B, B existing in a free form needs to be contained at least 0.0003% or more. However, if the amount of solute B exceeds 0.005%, coarse iron nitride precipitates in the molded product and the toughness of the molded product deteriorates. B also exhibits an effect of suppressing the growth of austenite grains during heating. From this viewpoint, the content of solute B is preferably 0.0015% or more, more preferably 0.0020. % Or better. Moreover, the upper limit with preferable B content is about 0.0040%, It is good to set it as 0.0035% or less more preferably.

Ti: 0.005 to 0.05%, N: 0.001 to 0.01% (however, these elements satisfy the relationship of the formula (1))
As described above, Ti is an element having a role of fixing N. Although it is sufficient to contain a Ti amount corresponding to the N content, it is necessary to contain Ti so as to satisfy the expression (1) for the purpose described above. On the other hand, when the N content is excessive, the amount of nitride deposited increases and the toughness after hot forming deteriorates. For these reasons, the N content needs to be 0.01% or less. What is necessary is just to set Ti content according to the nitrogen content in a steel plate. If the N content in the steel exceeds 0.01%, the spot weld strength deteriorates, and from this point of view, the Ti content should be 0.035% or less. The amount is desirably 0.01% or less. Further, the smaller the N content is, the smaller the Ti content is. However, to make it extremely small, it costs too much on steel making, so the lower limit of the N content is 0.001%.

  The basic components in the steel sheet of the present invention are as described above, and the balance is composed of iron and inevitable impurities (for example, P, S, O, As, Sb, Sn, etc.). From the viewpoint of the bonding strength of the spot bonded portion, and S are preferably reduced to P: 0.02% or less and S: 0.02% or less, respectively. Further, if necessary, (a) Cr and / or Mo in total 0.01 to 1%, (b) Nb in 0.01 to 0.1%, (c) Ni and / or Cu in total 0 It is also effective to contain 0.01 to 0.5%, etc., and the properties of the steel sheet are further improved depending on the components to be contained. The reason for limiting the range when these components are contained is lacking.

Cr and / or Mo: 0.01 to 1% in total
Cr and Mo are effective elements for improving the hardenability of the steel sheet, and by containing these elements, reduction in hardness variation in the molded product can be expected. In order to exert such an effect, it is preferable to contain 0.01% or more of one or two of them (total). However, if their content becomes excessive and exceeds 1%, the effect is saturated and the cost increases.

Nb: 0.01 to 0.1%
Nb is an effective element for increasing the high temperature strength of the steel sheet because it forms a stable carbide at high temperature. A moderate increase in the high-temperature strength of the steel sheet exhibits the effect of suppressing the reduction in the thickness of the hot-formed product. In order to exert such an effect, the Nb content is preferably set to 0.01% or more. However, when the Nb content is excessive and exceeds 0.1%, the increase in strength becomes too large, and molding is performed. Sometimes breakage tends to occur, and the cost increases.

Ni and / or Cu: 0.01 to 0.5% in total
When it is desired to give the naked product corrosion resistance and delayed fracture resistance, Ni or Cu is added as necessary. In order to exhibit such an effect, it is preferable to use 0.01% or more of one or two of them (in total). However, when these contents become excessive and exceed 1%, it causes the generation of surface flaws during the production of the steel sheet.

  The method for producing the steel sheet of the present invention is not particularly limited, and it may be performed by casting, heating, hot rolling, further cold rolling after pickling, and annealing as necessary. good.

When hot forming using the steel sheet of the present invention as described above, the steel sheet is heated to a temperature equal to or higher than the Ac ₃ transformation point and austenitized according to a normal method, and then forming is completed at a temperature of 550 ° C. or higher. (When the mold reaches the bottom dead center position). However, the heating conditions are such that the austenite grain growth is suppressed by controlling the holding time at a temperature equal to or higher than the Ac ₃ transformation point to 30 minutes or less, preferably 15 minutes or less. An improvement in toughness can be expected.

The inventor investigated the relationship between the holding time and the austenite grain size when heated to a temperature equal to or higher than the Ac ₃ transformation point. Of the chemical composition shown in Table 1 above, a steel plate having a B content of 0.0017% is hot rolled, pickled, cold rolled to a thickness of 1.2 mm according to a conventional method, and 700 ° C. The test piece was prepared by holding for 60 seconds and then air-cooling. The test piece was held at 850 to 930 ° C. for 3 to 30 minutes in a salt bath, and then the test piece was water-cooled. Thereafter, the prior austenite particle size of the test piece was measured by a comparative method. The result is shown in FIG. 7, by setting the retention time to 30 minutes or less, it is possible to ensure at least 8 or more by the granularity number, and preferably to ensure 9 or more by the granularity number by setting it to 15 minutes or less. I understand that.

When hot forming using the steel sheet of the present invention as described above, the structure can be refined by heating to a temperature not lower than the Ac ₁ transformation point and not higher than the Ac ₃ transformation point of the steel sheet. An improvement in hot drawability can be expected. In particular, before performing the heating necessary for hot forming, the steel plate is once heated to the Ac ₃ transformation point or higher and then cooled to a temperature below the Ms point of the steel plate at a cooling rate of 20 ° C./second or more (cooled to room temperature as it is). A low temperature transformation product such as martensite and bainite is included in the steel sheet microstructure, and then the temperature necessary for hot forming again (above the Ac ₁ transformation point and below the Ac ₃ transformation point). Further improvement of deep drawability can be expected by heating to a temperature of (5).

  The effect of using the steel plate of the present invention is remarkably exhibited when forming (that is, draw forming) using a mold having a wrinkle presser, but in addition to these requirements, the technique previously proposed It is also useful to use together. That is, it is also useful to adopt the mold configuration shown in FIG. 2 to achieve temperature uniformity of the steel sheet, and by using these techniques together, the effects of the present invention are more effectively exhibited. .

  Further, as is clear from the above-mentioned purpose, the molded product according to the present invention is not limited to a hot-drawn molded product molded using a wrinkle retainer, but also includes a product obtained by hot bending molding. Even in the case of manufacturing, the effect of the steel plate of the present invention is achieved.

  Hereinafter, the effects of the present invention will be described more specifically by way of examples. However, the following examples are not intended to limit the present invention, and any design changes in accordance with the gist of the preceding and following descriptions are technical aspects of the present invention. It is included in the range.

Example 1
Various steel materials having chemical composition shown in the following Tables 2 and 3 were melted at a laboratory level, and the obtained steel ingot was heated to 1200 ° C. and roughly rolled to a thickness of 30 mm to obtain a steel plate. Thereafter, the steel sheet having a thickness of 30 mm was heated again to 1250 ° C. and then hot-rolled to a thickness of 2.6 mm. The rolling end temperature at this time was set to 880 ° C., and the steel sheet after rolling was cooled to 600 ° C. at a cooling rate of 50 ° C./second, subsequently placed in a heating furnace maintained at 600 ° C., held for 30 seconds, and cooled in the furnace.

  The hot-rolled steel sheet was pickled, cold-rolled to a thickness of 1 mm or 1.2 mm, subsequently immersed in a salt bath maintained at 700 ° C. for 60 seconds, and then air-cooled.

  Test pieces were sampled from various steel plates produced under the above-described conditions, and a spot welding experiment with a 1 mm material and a hot forming experiment with a 1.2 mm material were performed. These experimental conditions are as follows.

[Spot welding experiment]
The assembly of an automobile body is carried out by manufacturing a conventional cold forming or hot forming and joining single components by spot welding or the like. In the case of a hot-formed product, the joining is performed with the parts being hardened and hardened. Therefore, in the experiment, in order to simulate the conditions, the cold-rolled and annealed material was heated to 900 to 950 ° C., held at that temperature for 30 seconds, and then immediately water-cooled material was used for the spot welding experiment. The specific conditions for spot welding were as follows, and the strength (cross joint breaking load) of the joint was measured.
Test piece conditions: Cross tension test piece (conforming to JIS Z3137)
Welding machine: Single-phase AC spot welding machine Electrode: Dome radius type with tip diameter of φ6mm Pressure: 4kN
Initial pressurization time: 60 cycles Energization time: 10 cycles (power frequency 60 Hz)

[Hot forming experiment]
In the hot forming experiment, a cold-rolled and annealed material was formed into strip-shaped blanks (length: 30 mm, width: 210 mm) and circular blanks (diameters: 80, 90, 92.5, 95.0, 97.5). , 100 mm) was heated to 900 to 950 ° C. for experiments. The heating at this time was performed in the air, and was heated by allowing a blank (strip shape, circular shape) to stay for 3 to 4 minutes (depending on the size of the blank) in a heating furnace maintained at 930 to 980 ° C. .

  The blank in the heated state taken out from the heating furnace is hot-formed using a 45 mm square mold with a crease presser (square tube die and square tube punch) installed in a crank press (see FIG. 1 above). The height was set to 37 mm, and after holding at the bottom dead center for 20 seconds, it was removed from the mold. The wrinkle holding force (BHF) at this time was 4 kN, and the molding speed was 40 revolutions / minute in terms of the number of rotations of the crank. Lubrication was performed by applying a hot forming lubricant to the mold. In addition, in order to minimize the temperature drop of the blank due to the contact between the crease presser and the blank after the mold and the heated blank are in contact, a plurality of movable pins are attached to the crease presser. It was installed (see 7 in FIG. 2), and the experiment was conducted so as to suppress the temperature drop of the blank.

  The hot drawability was evaluated by comparing the blank diameters that could be formed without breaking. The molding hardness and thickness distribution (thickness reduction rate) and the prior austenite particle size (old γ particle size) were also measured using a molded product obtained by hot forming a strip-shaped blank. These results are shown in Tables 4 and 5 below.

  As is apparent from this result, it is understood that the steel sheet of the present invention (Test Nos. 2, 3, 6 to 33) achieves good drawability while maintaining the bonding strength.

  On the other hand, it is understood that at least one of the bonding strength and the drawability is deteriorated in those lacking any of the requirements defined in the present invention (Test Nos. 1, 4, and 5).

Example 2
Some of the steel sheets shown in Table 1 (Test Nos. 3, 6, 12, 16, 21, 25, 26, 27, 29) were subjected to hot forming experiments. At this time, the hardness and squeezeability were evaluated when the material that had been once heated and cooled prior to hot forming was heated again and hot formed. The results are shown in Table 6 below. In Table 6, the Ac ₁ transformation point temperature and Ac ₃ transformation point temperature (calculated values) are shown simultaneously with the preheating conditions (preheating temperature / time, cooling rate, cooling stop temperature).

As is clear from this result, the steel sheet is once heated to the Ac ₃ transformation point or higher, and given a thermal history of cooling to a temperature below the Ms point of the steel sheet at a cooling rate of 20 ° C./second or more. It can be seen that the deep drawability between them is further improved.

It is a schematic explanatory drawing which shows the metal mold | die structure for implementing hot forming. It is a schematic explanatory drawing which shows the structure of the metal mold | die developed previously. It is a graph which shows the influence which addition of Si has on the joint strength of spot welding. It is the bar graph shown about the influence which addition of B has on hot formability. It is explanatory drawing which shows the measurement position of board thickness reduction | decrease amount. It is a graph which shows the relationship between Nb content and sheet thickness reduction | decrease rate. Ac ₃ is a graph showing the relationship between the retention time and prior austenite grain size number of at least transformation point temperature.

Explanation of symbols

1 Punch 2 Die 3 Blank holder 4 Steel plate (blank)
7 pin

Claims (6)

A steel plate used to obtain a molded product by hot forming,
C: 0.1 to 0.35% (meaning mass%, the same applies hereinafter), Si: 0.7 to 2.5%, Mn: 0.5 to 5%, Al: 0.01 to 0.5% Ti: 0.005 to 0.05%, B: 0.003 to 0.005%, N: 0.001 to 0.01%, respectively, and satisfying the relationship of the following formula (1), A steel sheet for hot forming excellent in bonding strength and hot formability of a spot weld, wherein the balance is made of Fe and inevitable impurities.
([Ti] /47.9) × 14.0− [N] ≧ 0 (mass%) (1)
However, [Ti] and [N] indicate the contents (mass%) of Ti and N, respectively.   The steel sheet for hot forming according to claim 1, further comprising 0.01 to 1% of Cr and / or Mo in total.   The steel sheet for hot forming according to claim 1 or 2, further comprising 0.01 to 0.1% of Nb.   The steel sheet for hot forming according to any one of claims 1 to 3, further comprising 0.01 to 0.5% of Ni and / or Cu in total. The steel sheet according to any one of claims 1 to 4, wherein the steel sheet is heated to a temperature equal to or higher than the Ac ₃ transformation point of the steel sheet, held at that temperature for 30 minutes or less, and then hot-formed. Hot-formed product. Heat produced by using the steel sheet according to any one of claims 1 to 4 and heating the steel sheet to a temperature not lower than the Ac ₁ transformation point and not higher than the Ac ₃ transformation point, and then hot forming. Inter-molded product.

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