JP5008896B2 - Warm press-molded high-strength member and manufacturing method thereof - Google Patents

Description

  The present invention relates to a warm press-molded high-strength member and a method for producing the same, and more particularly to a warm press-molded high-strength member having high strength and excellent dimensional accuracy in member molding and a method for producing the same.

Conventionally, many studies have been made on warm press molding from the viewpoint of achieving both high strength of automobile members and improvement in dimensional accuracy in member molding.
For example, in order to improve the formability in warm press forming, it has been proposed to reduce the material strength and yield strength in the warm temperature range with respect to the respective strengths at room temperature (see Patent Documents 1 and 2). .)
JP 2001-234282 A JP 2003-113442 A

  However, in high-strength steel sheets with a tensile strength of 980 MPa or more, the material strength and yield strength do not decrease much even in the warm temperature range, and it is difficult to achieve both high strength of members and improvement of dimensional accuracy in member forming. There was a problem.

  The present invention has been made in view of such problems of the prior art, and an object of the present invention is to provide a warm press-molded high-strength member having high strength and excellent dimensional accuracy in member molding, and It is in providing the manufacturing method.

  As a result of intensive studies to achieve the above object, the present inventors have formed a predetermined plastic deformation portion on a high-strength steel sheet having a tensile strength of 980 MPa or more, and press-molded this in a warm temperature range. Thus, the inventors have found that the above object can be achieved and have completed the present invention.

That is, the warm press-formed high-strength member of the present invention is formed by press-forming a high-strength steel plate having a tensile strength of 980 MPa or more in a warm temperature range, and the high-strength steel plate has C: 0.10 to 0.00. 40%, Si: 0.01 to 2.5%, Mn: 0.1 to 1.0%, P: 0.02% or less, S: 0.01% or less, Cu: 0.1 to 3.0 %, Ni: 0.1-3.0%, Cr: 0.01-3.0%, Mo: 0.1-2.0%, the balance being Fe and inevitable impurities, logarithmic strain the plastic deformation portion is 1 or more possess the whole or thickness surface portion, the warm press forming high strength member, characterized in that it contains a precipitate consisting of Mo alloy carbides.

Moreover, the manufacturing method of the warm press-molded high strength member of the present invention is a method of manufacturing the warm press molded high strength member of the present invention, and includes the following steps (1) to (3). Features.
(1) Step of preparing a high-strength steel sheet having a tensile strength of 980 MPa or more (2) A plastic deformation part having a logarithmic strain of 1 or more is formed on the whole of the high-strength steel sheet or on the surface of the plate thickness. Step for obtaining a strain-retained high-strength steel plate (3) Step for press-forming the strain-retained high-strength steel plate in a warm temperature range of 400 to 600 ° C. to obtain a warm press-formed high-strength member

  According to the present invention, a predetermined plastic deformation portion is formed on a high-strength steel plate having a tensile strength of 980 MPa or more, and this is press-molded in a warm temperature range. It is possible to provide a warm press-formed high-strength member excellent in accuracy and a method for manufacturing the same.

Hereinafter, the warm press-molded high-strength member of the present invention will be described in detail. In the present specification and claims, “%” for concentration, content, etc. represents mass percentage unless otherwise specified.
As described above, the warm press-formed high-strength member of the present invention is formed by press-forming a high-strength steel plate having a tensile strength of 980 MPa or more in a warm temperature range.
And this high-strength steel plate is C: 0.10-0.40%, Si: 0.01-2.5%, Mn: 0.1-1.0%, P: 0.02% or less, S : 0.01% or less, Cu: 0.1 to 3.0%, Ni: 0.1 to 3.0%, Cr: 0.01 to 3.0%, Mo: 0.1 to 2.0% And the balance is Fe and inevitable impurities, and the plastic deformation portion having a logarithmic strain of 1 or more is included in the whole or the plate thickness surface portion .
Moreover, this warm press-molded high-strength member contains precipitates made of Mo alloy carbide.
By adopting such a configuration, the strength is high and the dimensional accuracy in member molding is excellent.

Here, the plastic deformation portion may be present on the average (totally) in the thickness direction of the high-strength steel plate, and is concentrated (on the surface portion) on the plate surface side of the high-strength steel plate. May be.

In the present invention, but are not particularly limited in form (transfer) a method of the plastic deformation portion can be formed, for example, by rolling the plastically deformed portion (grant).

Furthermore, in the present invention, it is desirable that the rolling direction in the rolling process described above substantially coincides with the input direction when the high-strength member is used.
At this time, the strength of the member in the input direction can be further improved by the crystal structure that is remarkably elongated in the rolling direction.

In the present invention, a high-strength steel plate to be used may have a constant plate thickness, but a plate having a thickness distribution, that is, a plate having a different thickness depending on the position (so-called differential thickness steel plate) can also be used.
For example, the strength of the member can be increased more accurately by matching the thickness distribution with the strength distribution required for the member.
The thickness of the high-strength steel plate to be used may be the same as that of a conventional high-strength steel plate and may be 0.6 to 4 mm. However, since the strength is higher, the same strength can be obtained with a thin plate thickness. it can.

Furthermore, in this invention, it does not specifically limit about the surface state of the high strength steel plate to be used, For example, what has a plating film can also be used.
Examples of such a plating film include zinc plating and aluminum plating.

Here, the high-strength steel sheet used will be described in more detail.
As one embodiment of a high-strength steel plate, for example, it contains elements according to molybdenum (Mo), tungsten (W), vanadium (V), titanium (Ti) or niobium (Nb), and any combination thereof. The base structure is lower bainite, tempered lower bainite or tempered martensite, and the prior austenite grain size is 30 μm or less.

  With such a configuration, while having a tensile strength of 980 MPa or more, the conventional high-strength steel sheet exhibits a formability sufficient to satisfy, for example, a demand as an automotive part. Moreover, the secondary effect that delayed fracture resistance is improved is also obtained.

  In the high-strength steel sheet, the tensile strength of the high-strength steel sheet becomes 980 MPa or more by using the lower bainite structure, the tempered lower bainite, or the tempered martensite which are hard phases. More preferably, the tensile strength of the high-strength steel plate is 1180 MPa or more.

  Furthermore, the prior austenite particle size can be reduced to 1-30 μm. When the prior austenite particle size exceeds 30 μm, the effect of improving deep drawability, stretchability, and shape freezeability is small. Further, when the prior austenite particle size is less than 1 μm, the mechanical properties are likely to deteriorate, and the production tends to be difficult.

  Furthermore, the prior austenite particle size is preferably 3 to 10 μm. At this time, since the deep drawability, the stretchability, and the shape freezing property can be further improved, it is possible to satisfy the formability required when, for example, automobile parts are formed using the high-strength steel plate.

  Moreover, such a high-strength steel sheet contains carbon (C) and chromium (Cr) as additive components in proportions of C: 0.10 to 0.40% and Cr: 0.01 to 3.0%. And molybdenum (Mo), tungsten (W), vanadium (V), titanium (Ti), niobium (Nb), and any combination thereof, Mo: 0.10 to 2.0%, W : 0.20 to 1.5%, V: 0.002 to 1.0%, Ti: 0.002 to 1.0% and Nb: 0.005 to 1.0%, Impurity phosphorus (P) and sulfur (S) are contained in proportions of P: ≦ 0.02%, S: ≦ 0.01%, and the balance is substantially iron (Fe) and inevitable impurities. Is preferred.

At this time, by containing fine alloy carbides, a high-strength steel sheet having excellent delayed fracture resistance while securing formability can be obtained.
Each component will be described below.

C: C is the most effective element for increasing the strength. In order to obtain a strength of 980 MPa or more, it is preferable to contain 0.1% or more. However, if it exceeds 0.4%, it tends to cause toughness deterioration, so 0.10 to 0.40% is contained. good.

Cr: Cr is an element effective for improving the hardenability, and is an element effective for increasing the strength of the steel sheet by solid solution in cementite. Therefore, it is preferable to contain at least 0.01%. The content is preferably 1% or more, but if added excessively, the effect is saturated and the toughness is lowered, so the upper limit is preferably made 3.0%.

Mo: Mo is an important element in the high-strength steel sheet to be used. In addition to improving hardenability, Mo is effective for fine graining by forming an alloy carbide and also effective for hydrogen replacement. However, if it is less than 0.10%, formation of alloy carbide tends to be difficult. On the other hand, since Mo is an expensive alloy element, it is preferable to contain 0.1 to 2.0%.

  In order to ensure good delayed fracture resistance while securing formability, it is preferable to contain at least one element of Mo, W, V, Ti, and Nb. However, W, V, Nb, and Ti also has the same addition effect as Mo, so it is preferable to set the upper limit and the lower limit of the above content.

P: P is an element to be removed as much as possible in order to reduce the grain boundary strength, and the upper limit is preferably made 0.02%.

S: S is an element to be removed as much as possible in order to reduce the grain boundary strength, and the upper limit is preferably made 0.01%.

Furthermore, such a high-strength steel sheet contains, as an additive component, one or both of copper (Cu) and nickel (Ni), Cu: 0.1-3.0%, Ni: 0.1-3. It is good to contain in the ratio of 0%.
Each component will be described below.

Cu: Since Cu is effective for strengthening and its fine precipitation contributes to the improvement of delayed fracture, it is preferable to contain 0.1% or more. Moreover, since excessive addition causes deterioration of workability, the upper limit is preferably set to 3.0%.

Ni: Ni is an element effective in improving the corrosion resistance while ensuring the strength of the steel sheet by enhancing the hardenability of the steel sheet. If it is less than 0.1%, the desired effect cannot be obtained. On the other hand, if it exceeds 3.0%, the workability deteriorates, so 0.1 to 3.0% is preferably contained.

Furthermore, such a high-strength steel sheet contains, as an additive component, one or both of silicon (Si) and manganese (Mn), Si: 0.01 to 2.5%, Mn: 0.1 to 1 It is good to contain in the ratio of 0.0%.
Each component will be described below.

Si: Si is an element effective for deoxidation and strength increase. Therefore, it is preferable to make the content 0.2% or more including those added as a deoxidizer and remaining in the steel. However, since excessive addition may cause toughness deterioration, the upper limit is preferably 2.5%.

Mn: Mn is an element effective for increasing the strength of the steel sheet. If it is less than 0.1%, it is difficult to obtain a desired effect. On the other hand, when the content is too large, not only co-segregation of P and S is promoted, but also toughness deterioration may be caused.

  Moreover, such a high-strength steel plate preferably contains aluminum (Al) as an additive component in a ratio of Al: 0.001 to 0.1%.

Al: Al is added for deoxidation, but if the addition amount is too large, inclusions increase and workability deteriorates, so 0.001 to 0.1% is preferably contained.

Next, the manufacturing method of the warm press-molded high strength member of the present invention will be described in detail.
As described above, the method for producing a warm press-molded high strength member of the present invention is a method for producing the warm press molded high strength member of the present invention, and includes the following steps (1) to (3). .
(1) Step of preparing a high-strength steel sheet having a tensile strength of 980 MPa or more (2) A plastic deformation part having a logarithmic strain of 1 or more is formed on the whole of the high-strength steel sheet or on the surface of the plate thickness. Step of obtaining a strain-retained high-strength steel plate (3) Step of press-forming the strain-retained high-strength steel plate in a warm temperature range of 400 to 600 ° C. to obtain a desired warm press-formed high-strength member

  By adopting such a configuration, it is possible to obtain a high-strength and excellent dimensional accuracy in member molding, but the warm press-molded high-strength member of the present invention was produced by the above manufacturing method. It is not limited to things.

Hereinafter, it demonstrates in detail for every process.
In the step (1), a high-strength steel plate as described above may be prepared.
Specifically, a high-strength steel plate may be prepared by heat treatment so that the desired effect of each component described above is exhibited. Typically, the steel ingot is heated to 1200 ° C., and then rough rolled. The thickness of the sheet is adjusted, and immediately after that, finish rolling is started at a temperature of 900 to 1050 ° C. The finish rolling step is completed at a temperature of 800 to 900 ° C. while performing rolling reduction and cooling between the rolls as necessary, and coil winding is performed at 350 to 550 ° C. while cooling immediately.

  In the step (2), the forming method is not particularly limited as long as a plastically deformed portion having a logarithmic strain of 1 or more is formed on at least a part of the high-strength steel plate to obtain a strain-maintaining high-strength steel plate. Absent. For example, it may be formed by rolling.

In the step (3), the hot pressing conditions are not particularly limited as long as the strain-retaining high-strength steel plate is press-formed in a warm temperature range to obtain a desired warm-press-formed high strength member. The warm temperature range, from the viewpoint of maximizing the precipitation effect of M o alloy carbides requires that a 400 to 600 ° C..
In the present invention, it is considered that both high strength and dimensional accuracy are achieved by the dynamic recovery effect during press molding in the warm temperature range.

  EXAMPLES Hereinafter, although an Example and a comparative example demonstrate this invention further in detail, this invention is not limited to these Examples.

( Reference Example 1, Example 2 to Example 5, Reference Example 6 to Reference Example 10, Comparative Example 1 and Comparative Example 2)
High-strength steel plate A (tensile strength: 1280 MPa, stress reduction (SD): 240 MPa, prior austenite grain size: 8 μm) and high-strength steel plate B (tensile strength: 1140 MPa, stress reduction (SD) with chemical composition shown in Table 1 : 190 MPa, former austenite grain size: 10 μm) (both are based on the lower bainite), and the plastic deformation part (strain) application conditions shown in Table 2 and the warm press conditions shown in Table 3 are produced. Depending on conditions, warm press-formed high-strength members of each example were produced. Here, the prior austenite grain size was measured in accordance with JIS G0551 for the base structure having the lower bainite.

  In Table 2, Condition 1 is equivalent to logarithmic strain 1 on average in the plate thickness direction, and Condition 2 is particularly concentrated in the surface portion of the plate thickness, and its logarithmic strain is equivalent to 1. 3 indicates that no strain is applied by rolling.

  Further, in Table 3, when performing the warm press forming, the press was maintained at the bottom dead center for 5 minutes in any condition, and the temperature during that time was maintained at the condition shown in Table 3. Moreover, the warm press-molded high-strength member for warm press-molding has a hat shape, and the dimensions are: height: 80 mm, bottom face width hitting the punch bottom: 60 mm, flange width: 25 mm, vertical wall And the bottom of the punch was 93 °. Table 3 also shows the relative positional relationship between the strain applying direction and the forming direction of the high-strength steel sheet.

[Performance evaluation]
The warm press-molded high-strength member of each example was evaluated for formability and strength improvement. The obtained test results are shown in Table 4. Moreover, each characteristic evaluation was implemented in the following way.

(1) Formability evaluation The formability of the warm press-formed high-strength member was evaluated visually from the viewpoint of the precision of the part forming shape. In Table 4, “◯” indicates good, “Δ” indicates that if a member shape is selected, “X” indicates that the member is good, and “X” indicates that the member is defective.

(2) Strength improvement evaluation Evaluation of the strength improvement effect (tensile strength in the longitudinal direction of the member) after warm press forming with respect to the initial steel plate strength using a JIS Z2201 No. 5 test piece and performing a tensile test based on JIS Z2241 (See FIG. 1). The strength improvement effect is evaluated in three stages. “Large” indicates that the strength improvement effect is large, “Medium” indicates that the strength improvement effect is moderate, “Small” indicates that the strength improvement effect is small, and “-” indicates that It shows that the strength improvement effect was not recognized.

As shown in Table 4, the warm press-molded high-strength members of Examples 2 to 5 belonging to the scope of the present invention are high-strength, and the warm press-molded high-strength members excellent in dimensional accuracy in member molding Become. In other words, while forming (giving) a plastic deformation portion (strain) in the thickness direction of the high-strength steel plate in an average or concentrated on the entire surface, the strength is maintained or improved in the warm temperature range. It can be seen that the dimensional accuracy can be improved.
On the other hand, it can be seen that Reference Example 1, Reference Example 6 to Reference Example 10, Comparative Example 1 and Comparative Example 2 outside the present invention cannot form a member having sufficient dimensional accuracy.
A remarkable strength improvement effect is obtained in the high-strength steel sheet A, and at this time, Examples 2 to 5 are considered to give good results.
This is presumably because fine alloy carbide precipitates during warm forming due to plastic deformation.

It is a schematic diagram which shows the stress-strain diagram by the tension test using a plate-shaped test piece (For example, No. 5 test piece and No. 13 test piece prescribed | regulated to JISZ2201).

Claims (8)

A hot press-formed high-strength member formed by press-forming a high-strength steel plate having a tensile strength of 980 MPa or more in a warm temperature range,
The high-strength steel sheets are : C: 0.10 to 0.40%, Si: 0.01 to 2.5%, Mn: 0.1 to 1.0%, P: 0.02% or less, S: 0 0.01% or less, Cu: 0.1 to 3.0%, Ni: 0.1 to 3.0%, Cr: 0.01 to 3.0%, Mo: 0.1 to 2.0% and the balance is Fe and inevitable impurities, possess all or thickness surface portion plastically deformed portion is logarithmic strain 1 or more,
The warm press-molded high-strength member, wherein the warm-press molded high-strength member contains a precipitate made of a Mo alloy carbide . The warm-press-formed high-strength member according to claim 1, wherein the high-strength steel sheet has a prior austenite grain size of 1 to 30 µm and the base structure is lower bainite. The warm press-molded high-strength member according to claim 1 or 2 , wherein the plastic deformation portion is formed by rolling. Said rolling the rolling direction in the processing, the high-strength member warm press forming high strength member according to claim 3, characterized in that the input direction allowed one Itasa during use. The warm press-formed high-strength member according to any one of claims 1 to 4 , wherein the high-strength steel plate is a differential thickness steel plate . The warm press-formed high-strength member according to any one of claims 1 to 5 , wherein the high-strength steel plate has a plating film. It is a method of manufacturing the warm press-molded high-strength member according to any one of claims 1 to 6, and the following steps (1) to (3)
(1) A step of preparing a high-strength steel plate having a tensile strength of 980 MPa or more,
(2) forming a plastic deformation portion having a logarithmic strain of 1 or more on the entire high-strength steel plate or the surface portion of the plate thickness , and obtaining a strain-retaining high-strength steel plate provided with the plastic deformation portion;
(3) a step of press-forming the strain-retaining high-strength steel sheet in a warm temperature range of 400 to 600 ° C. to obtain a warm press-formed high-strength member;
A method for producing a warm press-molded high-strength member, comprising: In the said process (2), when forming the said plastic deformation part, it rolls, The manufacturing method of the warm press-molding high strength member of Claim 7 characterized by the above-mentioned.

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