TW201835354A - Hot stamp moulded body - Google Patents

Abstract

The present invention provides a hot stamp moulded body which takes into consideration problems to be solved in the prior art, achieves high bendability, high ductility, and hydrogen embrittlement resistance characteristics in order to achieve impact resistance characteristics, and suppresses variation in hardness. A hot stamp moulded body according to the present invention is characterized by being provided with a plate thickness central portion, and a softened layer provided to one or both sides of the plate thickness central portion. The hot stamp moulded body is further characterized in that: the plate thickness central portion has a hardness in the range of 500-800 Hv inclusive; and, in the metal structure from a depth of 20 [mu]m below the surface of the softened layer to a depth of 1/2 of the thickness of the softened layer, when areas surrounded by grain boundaries having a misorientation of 15 DEG or higher, in a cross section parallel to the plate thickness direction, are defined as crystal grains, the total area ratio of crystal grains having a maximum crystal misorientation of 1 DEG or lower inside the crystal grains defined above, and crystal grains having a maximum crystal misorientation in the range of 8-15 DEG inclusive inside the crystal grains defined above is at least 50 %, but less than 85%.

Description

Hot stamping

The invention relates to a hot-embossed molded body used for structural members or reinforcing members of automobiles or structures that require strength, and particularly relates to strength, impact resistance, ductility, and hydrogen embrittlement resistance after hot-embossing. Excellent hot stamped molded body with small hardness variation.

BACKGROUND ART In recent years, from the viewpoints of environmental protection and resource saving, the weight of automobile bodies has been continuously demanded. Therefore, the application of high-strength steel plates to automobile components has continued to accelerate. However, as the strength of the steel sheet is increased, the formability is deteriorated. Therefore, in a high-strength steel sheet, the formability of a member having a complicated shape has become an issue.

In order to solve the above-mentioned problems, the application of hot stamping to press forming after heating a steel plate to a high temperature in the Vosstian iron zone is progressing. Since hot stamping is performed in the mold at the same time as the pressing process, the strength corresponding to the amount of C of the steel sheet can be obtained, and it has attracted attention as a technology that takes into account the forming and strength assurance of automotive components.

However, the conventional hot-embossed parts manufactured by press hardening, because the entire plate thickness area is formed by a hard structure (mainly Asada loose iron), once the car is bent and deformed when it is struck, it will be warped on the part. The largest strain occurs in the curved part, and the fracture will progress from the vicinity of the surface layer of the steel plate, and eventually it will easily break.

For example, if a conventional hot-embossed part such as a hat-shaped member obtained by press-quenching and manufacturing has bending deformation during a car collision, the deformation of the hat-shaped member will be localized due to warping of the hat-shaped member. Reduced load resistance. That is, the maximum load of a component that is a hot-embossed part is affected not only by the strength of the component but also by the degree to which warpage is liable to occur. When the ductility of the steel sheet is high, in a state where the steel sheet is formed into a certain shape as a member, the deformation region becomes difficult to be localized. That is, the component is not easily warped.

In addition, the method of contacting the mold in the hot-embossed molded body is not necessarily the same. For example, the cooling rate is likely to decrease in the vertical wall portion of the cap-shaped member. Therefore, a low hardness region may be formed locally on the steel sheet. The localized softened part deforms during the impact and becomes the main cause of cracking. Therefore, the hardness of the formed body is small, that is, to ensure stable strength, and it is important to ensure the impact resistance.

Therefore, ductility is also important in hot-embossed parts, but generally, the ductility of Asada loose iron is low. In addition, since the density of lattice defects in the surface layer of the steel sheet is high, the invasion of hydrogen is promoted, and there is a problem that the hydrogen embrittlement resistance becomes poor. For the reasons described above, hot-pressed parts manufactured by press hardening have been limited in their application areas to automotive parts in the past.

For the above problems, a technique has been proposed to improve the deformability of hot-pressed parts to suppress cracking. Patent Document 1 discloses a technique for ensuring the hardness of the center of the plate thickness of the hot-pressed part to be 400 Hv or more, and forming a soft layer with a thickness of 20 μm or more and 200 μm or less and 300 Hv or less on the surface layer, thereby ensuring that It has a tensile strength of 1300 MPa or more, and suppresses cracking at the time of automobile collision. Patent Document 2 discloses a technique for reducing the lattice defect density of the surface layer and improving the hydrogen embrittlement resistance by controlling the carbon concentration of the plate thickness surface layer to be less than 1/5 of the carbon concentration of the center portion of the plate thickness. In addition, Patent Document 3 discloses a method in which the central part of the plate thickness is a composite structure of ferrous iron and Asada loose iron, and the ferrous iron structure fraction of the surface layer portion is increased, and the surface layer portion can be alleviated even if it undergoes severe bending deformation. Stress technology.

However, in Patent Literature 1 and Patent Literature 2, since the surface layer portion of the plate thickness is made of a soft structure, and the central portion of the plate thickness is formed by the hard structure, a sharp hardness gradient is generated in the plate thickness direction, so it is subject to bending. When deforming, there is a problem that cracks are likely to occur near the boundary between the soft tissue and the hard tissue that generate a sharp hardness gradient. In Patent Document 3, although the surface layer portion of the plate thickness is a soft structure, and the central portion of the plate thickness is a composite structure of a hard structure and a soft structure, the sharp hardness gradient in the plate thickness direction is reduced. The central part of the plate thickness is a composite structure, so the upper limit of the tensile strength is about 1300 MPa. It is difficult to ensure the tensile strength required for hot-pressed parts of 1500 MPa or more.

Prior Art Literature Patent Literature Patent Literature 1: Japanese Patent Laid-Open No. 2015-30890 Patent Literature 2: Japanese Patent Laid-Open No. 2006-104546 Patent Literature 3: International Patent Publication No. 2015/097882

SUMMARY OF THE INVENTION Problems to be Solved by the Invention In view of the problems of the conventional technology, the present invention aims to provide a hot-embossed molded body that achieves both high bendability, high ductility, and hydrogen embrittlement resistance for achieving impact resistance. , And can suppress hardness unevenness.

Means for Solving the Problems The present inventors have conducted intensive studies on a method for solving the above problems. As a result, in order to improve the hydrogen embrittlement resistance, it is effective to reduce the density of lattice defects in the surface layer of the plate. Therefore, a soft structure must be formed in the surface layer. On the other hand, in order to ensure a tensile strength of 1500 MPa or more, it is necessary to constitute only the central portion of the plate thickness with a hard structure. When the surface layer of the plate thickness is made of a soft structure as described above, and the central portion of the plate thickness is formed by the hard structure, as long as the sharp hardness gradient in the plate thickness direction generated near the boundary between the hard structure and the soft structure can be reduced, To ensure the tensile strength of 1500MPa or more and good resistance to hydrogen embrittlement, and to obtain good bendability.

Then, the inventors investigated the metal structure of a steel plate that obtains good bendability by controlling the soft structure, that is, the structure of the surface layer, and conducted intensive studies repeatedly. As a result, it was found that in the metal structure constituting the surface layer, when the area surrounded by the grain boundary with an azimuth difference of 15 ° or more is defined as the crystal grains in terms of the plate thickness section, the metal structure should preferably be the largest in the aforementioned crystal grains. A crystal grain having a crystal orientation difference of 1 ° or less and a crystal grain having a maximum crystal orientation difference within the aforementioned crystal grains ranging from 8 ° to 15 °. These measurements are performed in a region from a depth position of 20 μm below the surface of the surface layer to a depth position (surface layer center) of 1/2 of the thickness of the surface layer. It was also found that the influence of the surface properties of the hot-embossed molded body and the influence of the migration from the central portion of the plate thickness to the surface layer can be eliminated by the above-mentioned metal structure.

Furthermore, by controlling the amount of Mn and Si added in the central portion of the plate thickness, the ductility is improved, the hardenability is improved, and high strength is stably ensured. As a result, it is possible to suppress cracking during bending deformation, ensure tensile strength above 1500 MPa and good hydrogen embrittlement resistance, and successfully achieve excellent bendability and ductility, and also achieve strength stability. Hot stamped molded body with excellent impact resistance and hydrogen embrittlement resistance.

The present invention has been completed based on the above findings, and the gist thereof is as follows. (1) A hot embossed molded body comprising a central portion of plate thickness and softening layers disposed on both sides or one side of the central portion of plate thickness, the hot embossed portion is characterized in that the central portion of plate thickness is based on mass % Includes: C: 0.20% or more and less than 0.70%, Si: less than 3.00%, Mn: 0.20% or more and less than 3.00%, P: 0.10% or less, S: 0.10% or less, sol.Al: 0.0002% or more and Below 3.000%, N: 0.01% or less, and the remainder is composed of Fe and unavoidable impurities, and has a hardness of 500Hv or more and 800Hv or less; from a depth of 20 μm below the surface of the softened layer to the thickness of the softened layer 1 In a metal structure with a depth of / 2, in terms of a section parallel to the plate thickness direction, when a region surrounded by a grain boundary having an azimuth difference of 15 ° or more is defined as a crystal grain, the maximum crystal orientation difference within the aforementioned crystal grain is within The total area ratio of the crystal grains having a maximum crystal orientation difference between the crystal grains of 1 ° or less and the crystal grains of 8 ° or more and 15 ° or less is 50% or more and less than 85%. (2) The hot stamped molded body according to (1), wherein the Si content is 0.50% or less, and the Mn content is 0.20% or more and less than 1.50%. (3) The hot stamped molded body according to (1), wherein the Si content is 0.50% or less, and the Mn content is 1.50% or more and less than 3.00%. (4) The hot-embossed molded body according to (1), wherein the Si content is greater than 0.50% and less than 3.00%, the Mn content is 0.20% and less than 1.50%, and the central part of the sheet thickness includes 1.0 in terms of area fraction. % And less than 5.0% of residual Vostian iron. (5) The hot-embossed molded body according to (1), wherein the Si content is greater than 0.50% and less than 3.00%, and the Mn content is 1.50% or more and less than 3.00%; % And less than 5.0% of residual Vostian iron. (6) The hot-embossed molded body according to any one of (1) to (5), wherein the central portion of the plate thickness further contains Ni in a mass% of 0.01% or more and 3.00% or less. (7) The hot-embossed molded body according to any one of (1) to (6), wherein the central portion of the plate thickness further includes one or more of the following elements in terms of mass%: Nb: 0.010% or more 0.150% or less, Ti: 0.010% or more and 0.150% or less, Mo: 0.005% or more and 1.000% or less, and B: 0.0005% or more and 0.0100% or less. (8) The hot stamped molded body according to any one of (1) to (7), wherein a plated layer is formed on the softened layer.

ADVANTAGE OF THE INVENTION According to this invention, the hot stamping molded body which is excellent in bendability, ductility, impact resistance, and hydrogen embrittlement resistance, and has small hardness variation can be provided.

Embodiment of the invention (Structure of the hot-embossed molded body of the present invention) The hot-embossed molding system of the present invention has a structure in which softened layers are arranged on the surfaces of both sides or one side. The softened layer is a region having a hardness that is 10 Hv or more lower than the hardness of the central portion of the plate thickness.

(Board thickness central portion) The plate thickness central portion of the hot-embossed molded article of the present invention is required to have a hardness of 500 Hv or more and 800 Hv or less. The reason for limiting the component composition of the plate thickness center portion so that the hardness of the plate thickness center portion falls within the aforementioned range is described below. Hereinafter, the symbol% regarding the component composition means mass%.

(C: 0.20% or more and less than 0.70%) C is an important element for obtaining a hardness of 500 Hv or more and 800 Hv or less at the center of the plate thickness. If it is less than 0.20%, it will be difficult to ensure 500 Hv or more at the center of the plate thickness, so C is 0.20% or more. And it is preferably at least 0.30%. On the other hand, if it is more than 0.70%, the hardness of the central part of the plate thickness is more than 800 Hv, and the bendability is reduced. Therefore, C is set to 0.70% or less. And it is preferably at most 0.50%.

(Si: less than 3.00%) Si is an element that contributes to strength improvement by solid solution strengthening. In order to obtain the effect of improving the strength of the steel sheet due to the solid solution of Si in the metal structure, the Si addition amount is preferably 0.30% or more, but even if Si is added more than 0.5%, the aforementioned effects are still saturated.

Si also has the effect of generating residual Vosted iron and improving ductility. To obtain this effect, at least 0.50% must be added. On the other hand, even if it is added more than 3.00%, the effect will be saturated, so the amount of Si added is less than 3.00% as the upper limit. And it is preferably less than 2.0%.

(Mn: 0.20% or more and less than 3.00%) Mn is an element that contributes to strength improvement by solid solution strengthening. The effect of increasing the strength of the steel sheet due to the solid solution of Mn in the metal structure cannot be obtained if the amount is less than 0.20%, so it should be added above 0.20%. And it is preferably at least 0.70%. On the other hand, even if it is 1.50% or more, the effect is saturated.

Moreover, Mn also has the effect of improving hardenability. By adding 1.50% or more, the hardenability can be improved and high strength can be stably obtained. The preferable addition amount to obtain the effect of improving hardenability is 1.70% or more. Since the above-mentioned effect is saturated even when 3.00% or more is added, the upper limit of the Mn addition amount is set to 3.00%. And it is preferably less than 2.00%.

(P: 0.10% or less) P is an element that segregates at the grain boundaries and hinders the strength of the grain boundaries. When it is more than 0.10%, the grain boundary strength is significantly reduced, and hydrogen embrittlement resistance and bendability are reduced. Therefore, P is set to 0.10% or less. And it is preferably at most 0.05%. Although the lower limit is not particularly limited, if it is reduced to less than 0.0001%, the cost of P removal will increase significantly, which is quite unfavorable on the economic side. Therefore, 0.0001% is the practical lower limit in practice.

(S: 0.10% or less) S is an element that forms inclusions. When it is more than 0.10%, inclusions are generated, and hydrogen embrittlement resistance and bendability are reduced. Therefore, S is set to 0.10% or less. And preferably it is 0.0025% or less. Although the lower limit is not particularly limited, if it is reduced to less than 0.0015%, the cost of de-S will rise sharply, which is quite unfavorable on the economic side. Therefore, 0.0001% is the practical lower limit in practice.

(sol.Al: 0.0002% or more and 3.000% or less) Al is an element that can exert the effect of deoxidizing molten steel and improving the soundness of the steel. In the present invention, in order to obtain the deoxidation effect, not all Al contained in the steel is specified, but the content range of so-called acid-soluble aluminum (sol.Al) is specified. If the sol.Al content is less than 0.0002%, the deoxidation will be insufficient, so the sol.Al content is set to 0.0002% or more. And it is preferably at least 0.0010%. On the other hand, the effect is saturated even if it is added more than 3.0%, so it is set to 3.000% or less.

(N: 0.01% or less) N is an impurity element and is an element that forms nitrides and hinders flexibility. When it is more than 0.01%, coarse nitrides are formed and the bendability is significantly reduced. Therefore, N is set to 0.01% or less. And it is preferably 0.0075% or less. Although the lower limit is not particularly limited, if it is reduced to less than 0.0001%, the cost of de-N will rise sharply, which is quite unfavorable in terms of economy. Therefore, 0.0001% is the practical lower limit in practice.

(Ni: 0.010% or more and 3.00% or less) Ni is an element that contributes to strength improvement by solid solution strengthening, so it can be added as needed. If it is less than 0.010%, the effect cannot be obtained, so it is necessary to add more than 0.010%. And it is preferably at least 0.5%. On the other hand, even if it is added more than 3.00%, the effect is saturated, so it is set to 3.00% or less. And it is preferably at most 2.50%.

(Nb: 0.010% or more and 0.150% or less) Nb is an element that contributes to strength improvement by solid solution strengthening, so it can be added as needed. If it is less than 0.010%, the effect cannot be obtained, so it is necessary to add more than 0.010%. And it is preferably at least 0.035%. On the other hand, even if it is added more than 0.150%, the effect is saturated, so it is set to 0.150% or less. And it is preferably at most 0.120%.

(Ti: 0.010% or more and 0.150% or less) Ti is an element that can improve strength by solid solution strengthening, so it can be added as needed. If the effect is less than 0.010%, the effect cannot be obtained, so it is set to 0.010% or more. And it is preferably at least 0.020%. On the other hand, even if it is added more than 0.150%, the effect is saturated, so it is set to 0.150% or less. And it is preferably at most 0.120%.

(Mo: 0.005% or more and 1.0% or less) Mo is an element that contributes to strength improvement by solid solution strengthening, so it can be added as needed. If it is less than 0.005%, the effect cannot be obtained, so it is set to 0.005% or more. And it is preferably at least 0.0100%. On the other hand, the effect is saturated even if it is added more than 1.000%, so it is set to 1.000% or less. And it is preferably 0.800% or less.

(B: 0.0005% or more and 0.0100% or less) B is an element that segregates at the grain boundaries and contributes to the improvement of the strength of the grain boundaries. Therefore, it can be added as needed. If it is less than 0.0005%, the addition effect cannot be fully obtained, so it is necessary to add more than 0.0005%. And it is preferably at least 0.0010%. On the other hand, even if it is added more than 0.0100%, the effect is saturated, so it is set to 0.0100% or less. And it is preferably 0.0075% or less.

The remainder of the component composition at the center of the plate thickness is Fe and unavoidable impurities. The unavoidable impurities are elements that are unavoidably mixed in from the steel raw material and / or during the steel making process, and are allowed within a range that does not impede the characteristics of the hot stamped formed body of the present invention.

(Hardness of the central part of the plate thickness: 500 Hv or more and 800 Hv or less) When the hardness of the central part of the plate thickness is 500 Hv or more, the tensile strength of the hot stamped molded product of the present invention can be ensured to be 1500 MPa or more. And it is preferably at least 600 Hv. On the other hand, when the hardness of the center portion of the plate thickness is more than 800 Hv, the hardness difference from the softened layer becomes too large and deterioration of bendability is caused. Therefore, 800 Hv is set as the upper limit. And it is preferably below 720Hv.

The method for measuring the hardness at the center of the plate thickness is as follows. After a cross section perpendicular to the plate surface of the hot-embossed formed body is taken, a sample for the measurement surface is prepared and subjected to a hardness test. The method for preparing the measuring surface can be implemented in accordance with JIS Z 2244. For example, after grinding the measuring surface with # 600 to # 1500 silicon carbide paper, use diamond powder with a particle size of 1 μm to 6 μm to disperse in a diluent such as alcohol or pure water. The obtained liquid can be processed into a mirror surface. The hardness test may be performed by the method described in JIS Z 2244. A micro-Vickers hardness tester is used to measure 10 points at a position of 1/2 of the plate thickness at a load of 1 kgf and at intervals of 3 times or more the indentation. The average value is used as the hardness of the center portion of the plate thickness of the hot stamped body.

(Metal structure in the central part of the plate thickness) The central part of the plate thickness contains 1% or more residual Vosted iron in terms of area fraction, thereby improving the ductility. In addition, the area fraction of the residual Vosstian iron in the central part of the plate thickness is preferably 2% or more. However, when the area fraction of the residual Vossteel is made 5% or more, the bendability is deteriorated, so the upper limit is set to less than 5%. And it is preferably less than 4.5%.

The area fraction of the residual Vosstian iron can be measured by the following method. After taking a sample from the hot stamped component, the surface is cut from the normal direction of the rolled surface to a depth of 1/2 of the plate thickness, and the surface obtained by the surface cutting is subjected to X-ray diffraction measurement. From the image obtained by the X-ray diffraction method using the Kα line of Mo, the area ratio Vγ of the residual Vostian iron can be obtained by the following formula. Vγ = (2/3) {100 / (0.7 × α (211) / γ (220) +1)} + (1/3) {100 / (0.78 × α (211) / γ (311) +1) } Here, α (211) is the X-ray diffraction intensity of the (211) plane of fertile grain iron, γ (220) is the X-ray diffraction intensity of the (220) plane of Vostian Iron, and γ (311) system X-ray diffraction intensity of the (311) plane of Vostian Iron.

(Softened layer) As described above, the so-called softened layer in the present invention is formed in the thickness direction of the plate thickness section of the hot-press formed body, and decreases from the hardness (the hardness at the position of 1/2 of the plate thickness) in the center portion of the plate thickness. The position from 10 Hv to the surface of the aforementioned molded body.

(Metal structure of the softened layer) As a result of investigations by the inventors and other metal structures of the steel plate having good bendability, it was found that the metal structure constituting the softened layer had an azimuth difference of 15 ° or more in terms of the plate thickness section. When the area surrounded by the grain boundaries is defined as crystal grains, the metal structure should preferably be such that the maximum crystal orientation difference between the crystal grains within the aforementioned crystal grains is less than 1 ° and the maximum crystal orientation difference within the aforementioned crystal grains is 8 ° ~ 15 ° Crystal grains. These measurements are performed in a region from a depth position of 20 μm below the surface of the softened layer to a depth position (the center of the softened layer) of 1/2 of the thickness of the softened layer. As a result of intensive studies conducted by the present inventors, it has been found that from the viewpoint of effects such as bendability, the tissue fraction from the position of 20 μm from the surface of the softened layer to the depth of 1/2 of the thickness of the softened layer is important. of. With the above-mentioned metal structure, the influence of the surface properties of the hot-embossed molded body and the influence of the migration from the central portion of the plate thickness to the softened layer can be eliminated.

In the aforementioned metal structure of the softened layer, the total area ratio of the crystal grains with a maximum crystal orientation difference of 1 ° or less inside the crystal grains and the crystal grains with a maximum crystal orientation difference of 8 ° ~ 15 ° within the crystal grains is 50 % Or more, and more preferably 55% or more. On the other hand, if the total area ratio of the aforementioned metal structure of the softened layer is 85% or more, the hardness difference between the softened layer and the center of the plate thickness becomes too large, and it is impossible to obtain a reduction in the thickness direction of the plate during bending deformation. The effect of the hardness gradient is sharp, so it is set to less than 85%. And it is preferably 80% or less.

In addition, the hardness of the softened layer from the depth position 1/2 (the center of the softened layer) to the center of the plate thickness is set to the hardness of the softened layer on the side of the plate thickness center (the boundary with the center of the plate thickness). When HvA is set, and the hardness of the center of the softened layer is set to HvB, the relationship is HvA-HvB ≧ 10Hv.

A method for determining a region from 20 μm below the surface of the softened layer to a position where the thickness of the softened layer is 1/2 will be described below. A cross-section (plate thickness cross-section) perpendicular to the surface of the hot-embossed molded body of the measurement object is taken, and then a sample for the measurement surface is prepared and subjected to a hardness test. The method for preparing the measuring surface can be implemented in accordance with JIS Z 2244. For example, after grinding the measuring surface with # 600 to # 1500 silicon carbide paper, use diamond powder with a particle size of 1 μm to 6 μm to disperse in a diluent such as alcohol or pure water. The obtained liquid can be processed into a mirror surface. According to the method described in JIS Z 2244, a micro-Vickers hardness tester was used to perform two measurements on the prepared sample. The first time is from the area within 20 μm from the surface in the plate thickness direction of the hot stamped body to the center of the plate thickness (position of 1/2 of the plate thickness), in a direction perpendicular to the surface ( In the thickness direction), the measurement was performed at a load of 0.3 kgf and at intervals of three times or more the indentation. However, when a plating layer is present, the measurement is performed from a region within 20 μm directly below the alloy layer of the plating or plating and softening layer material. A position where the hardness at the center of the plate thickness (hardness at a position of 1/2 of the plate thickness) starts to decrease by 10 Hv or more is determined, and a softened layer is set from the plate thickness position to the surface of the hot stamped molded body. When the softened layer is present on both sides, the second measurement is performed on the surface (back surface) on the opposite side to the first measurement in the same manner, and the position where the hardness of the central portion of the plate thickness decreases by 10 Hv or more is determined.

Next, a calculation method of the area ratio of the metal structure of the softened layer will be described. A sample was cut out from the hot-embossed molded body so that a cross section (plate thickness cross section) perpendicular to its surface could be observed. The length of the sample varies depending on the measurement device, but it is preferably about 50 μm. EBSD analysis was performed on the area from the surface of the softened layer to a position 1/2 of the thickness of the softened layer (the center of the softened layer) at a measurement interval of 0.2 μm in the thickness direction of the sample to obtain crystal orientation information. Here, the EBSD analysis uses a device consisting of a thermal field emission scanning electron microscope (JSM-7001F manufactured by JEOL) and an EBSD detector (DVC5 type detector manufactured by TSL), and the analysis speed is 200 to 300 points / second. Implementation.

Secondly, based on the obtained crystal orientation information, the area surrounded by grain boundaries with an orientation difference of 15 ° or more is defined as a crystal grain, and a crystal orientation distribution map in the direction of the plate surface is produced. Use the obtained crystal orientation distribution map to find the intersection of the long axis of a crystal grain and the crystal grain boundary. Using any one of the two intersections as a starting point and the other as an end point, the azimuth difference between all measurement points included in the long axis of the crystal grains is calculated. The maximum value of the obtained azimuth difference is taken as the maximum crystalline azimuth difference of the crystal grains, and after the above analysis is performed on all crystal grains included in the measurement area, the average value of these values is defined as crystals of 15 ° or more Maximum crystal orientation difference within the area enclosed by the boundary.

The maximum crystal orientation difference defined above can be easily calculated by using the "Inverse Pole Figure Map" and "Profile Vector" functions included in the software "OIM Analysis (registered trademark)" attached to the EBSD analysis device. The "Inverse Pole Figure Map" function can depict grain boundaries with an inclination angle of 15 ° or more as high-angle grain boundaries, and can also produce a crystal orientation distribution map in the direction of the plate surface. The "Profile Vector" function can calculate the Misorientation Angle (Crystal Orientation Difference) between all measurement points included on an arbitrary straight line. Perform the above analysis on all crystal grains included in the measurement area (excluding crystal grains located at the end of the measurement area), and calculate crystals with a maximum crystal orientation difference of 1 ° or less inside the area surrounded by grain boundaries of 15 ° or more The total area ratio of grains and crystal grains with a crystal orientation difference of 8 ° ~ 15 °. When the softened layer is formed on both sides, the above procedure is also performed on the back surface side of the hot stamped molded body, and the average value of the area ratios obtained from the front surface side and the back surface side is used.

(Composition of the softened layer) The composition of the softened layer is not particularly limited except P, S, and N, which are unavoidable elements that impede strength and / or bendability, but in order to ensure that the strength of the hot stamped molded article can be displayed The steel with excellent bendability should preferably have the following composition.

The composition of the softened layer is preferably one or more of the C content, the Si content, and the Mn content are 0.6 times or less the corresponding element content in the central part of the plate thickness. The preferred range of each component in this case is as follows .

(C: 0.05% or more and less than 0.42%) To increase the strength, C may be added in an amount of 0.05% or more. From the viewpoint of improving the load resistance as a component to improve the impact characteristics, it is preferably 0.10% or more. In order to make the hardness of the softened layer lower than the hardness of the center portion of the plate thickness, it is desirable to make it less than that of the center portion of the plate thickness. For this purpose, the C content of the softened layer is preferably less than 0.42%, and more preferably 0.35% or less.

(Si: less than 2.00%) Since Si is an element that can contribute to strength improvement by solid solution strengthening, it is added to increase strength. However, in order to make the hardness of the softened layer lower than the hardness of the center portion of the plate thickness, it is desirable to make it less than that of the center portion of the plate thickness.

When the Si content in the central portion of the plate thickness is 0.50% or less, the preferred Si content in the softened layer is 0.30% or less, and more preferably 0.20% or less. In addition, when the Si content in the central portion of the plate thickness is greater than 0.50% and less than 3.00%, the preferred Si content of the softened layer is less than 2.00%, and more preferably 1.50% or less.

(Mn: 0.12% or more and less than 1.80%) Mn is an element that contributes to strength improvement by solid solution strengthening. Therefore, in order to increase strength, 0.12% or more may be added. However, in order to make the hardness of the softened layer lower than the hardness of the center portion of the plate thickness, it is desirable to make it less than that of the center portion of the plate thickness.

When the Mn content in the central portion of the plate thickness is 0.20% or more and less than 1.50%, the preferred Mn content of the softened layer is less than 0.90%, and more preferably 0.70% or less. In addition, when the Mn content in the central portion of the plate thickness is 1.50% or more and less than 3.00%, the preferred Mn content of the softened layer is less than 1.80%, and preferably 1.40% or less.

(P: 0.10% or less) P is an element that segregates at the grain boundaries and hinders the strength of the grain boundaries. When it is more than 0.10%, the grain boundary strength is significantly reduced, and hydrogen embrittlement resistance and bendability are reduced. Therefore, P is set to 0.1% or less. And it is preferably at most 0.05%. Although the lower limit is not particularly limited, if it is reduced to less than 0.0001%, the cost of P removal will increase significantly, which is quite unfavorable on the economic side. Therefore, 0.0001% is the practical lower limit in practice.

(S: 0.10% or less) S is an element that forms inclusions. When it is more than 0.10%, inclusions are generated, and hydrogen embrittlement resistance and bendability are reduced. Therefore, S is set to 0.10% or less. It should be below 0.0025%. Although the lower limit is not particularly limited, if it is reduced to less than 0.0015%, the cost of de-S will rise sharply, which is quite unfavorable on the economic side. Therefore, 0.0001% is the practical lower limit in practice.

(sol.Al: 0.0002% or more and 3.000% or less) Al is an element that can exert the effect of deoxidizing molten steel and improving the soundness of the steel. In the present invention, in order to obtain the deoxidation effect, not all Al contained in the steel is specified, but the content range of so-called acid-soluble aluminum (sol.Al) is specified. If the content of sol.Al is less than 0.0002%, deoxidation will be insufficient, so sol.Al should be set to 0.0002% or more. And it is preferably at least 0.0010%. On the other hand, the effect is saturated even if it is added more than 3.000%, so it is set to 3.000% or less.

(N: 0.01% or less) N is an impurity element and is an element that forms nitrides and hinders flexibility. When it is more than 0.01%, coarse nitrides are formed and the bendability is significantly reduced. Therefore, N is set to 0.01% or less. And it is preferably 0.0075% or less. Although the lower limit is not particularly limited, if it is reduced to less than 0.0001%, the cost of de-N will rise sharply, which is quite unfavorable in terms of economy. Therefore, 0.0001% is the practical lower limit in practice.

In addition, with regard to the components of the softened layer, one or more of the C content, Si content, and Mn content relative to the C content, Si content, and Mn content of the center of the plate thickness should be 0.6 times or less, respectively, except that it will be obstructed. Other than the upper limits of P, S, and N, which are unavoidable elements of strength and / or bendability, there are no particular restrictions on other components. In general, the softened layer may be arbitrarily selected to contain one or two or more of the following components in addition to C, Si, and Mn.

(Ni: 0.01% or more and 3.00% or less) Ni is an element that contributes to strength improvement by solid solution strengthening, so it can be added as needed. When less than 0.01%, the effect will not be obtained, so it should be added above 0.01%. And it is preferably at least 0.50%. On the other hand, even if it is added more than 3.00%, the effect is saturated, so it is set to 3.00% or less. And it is preferably at most 2.50%.

(Nb: 0.010% or more and 0.150% or less) Nb is an element that contributes to strength improvement by solid solution strengthening, so it can be added as needed. When less than 0.010%, the effect will not be obtained, so it should be added more than 0.010%. And it is preferably at least 0.035%. On the other hand, even if it is added more than 0.150%, the effect is saturated, so it is set to 0.150% or less. And it is preferably at most 0.120%.

(Ti: 0.010% or more and 0.150% or less) Ti is an element that can improve strength by solid solution strengthening, so it can be added as needed. If it is less than 0.010%, the effect cannot be obtained, so it should be set to 0.010% or more. And it is preferably 0.020%. On the other hand, even if it is added more than 0.150%, the effect is saturated, so it is set to 0.150% or less. And it is preferably at most 0.120%.

(Mo: 0.005% or more and 1.000% or less) Mo is an element that contributes to strength improvement by solid solution strengthening, so it can be added as needed. If it is less than 0.005%, the effect cannot be obtained, so it should be set to 0.005% or more. And it is preferably at least 0.010%. On the other hand, the effect is saturated even if it is added more than 1.000%, so it is set to 1.000% or less. And it is preferably 0.800% or less.

(B: 0.0005% or more and 0.0100% or less) B is an element that segregates at the grain boundaries and contributes to the improvement of the strength of the grain boundaries. Therefore, it can be added as needed. If it is less than 0.0005%, the effect of addition will not be fully obtained, so it should be added more than 0.0005%. And it is preferably at least 0.0010%. On the other hand, even if it is added more than 0.0100%, the effect is saturated, so it is set to 0.0100% or less. And it is preferably 0.0075% or less.

(Sectional hardness distribution of the hot stamped molded body) For a cross section perpendicular to the surface of the hot stamped molded body, it is preferable that the hardness distribution in the central portion of the plate thickness is uniform and uniform. In the hat-shaped structure, the hardness may decrease because the cooling rate is reduced because the mold does not easily contact the vertical wall portion. If there is a region where the hardness is reduced by more than 100 HV with respect to a cross section perpendicular to the long-side direction of the cap-shaped body, the deformation will be concentrated in the softened portion at the time of impact and will break at an early stage, so high impact characteristics cannot be obtained. Therefore, there must be no point lower than the average value of the hardness distribution (hereinafter referred to as "cross-section average hardness") of 100 HV in a cross section perpendicular to the surface of the hot stamped molded body. The hardness distribution of the cross section and the average hardness of the cross section adopt a Vickers hardness tester (with a load of 1 kgf) to take a cross section perpendicular to the long side direction at any position in the long side direction of the long hot stamped molded body. And obtained by measuring the Vickers hardness between the ends of the cross section at an equal interval of 1 mm or less at a plate thickness center position including the entire cross section area of the longitudinal wall.

(Formation of Plating Layer) For the purpose of improving corrosion resistance and the like, a plating layer may be formed on the surface of the softened layer. The plating layer may be either a plating layer or a molten plating layer. Examples of the electroplated layer include an electroplated zinc layer and an electroplated Zn-Ni alloy layer. Examples of the hot-dip plating layer include a hot-dip galvanized layer, an alloyed hot-dip galvanized layer, a hot-dip aluminum coating, a hot-dip Zn-Al alloy coating, a hot-dip Zn-Al-Mg alloy coating, and a hot-dip Zn-Al-Mg-Si alloy. Plating, etc. The amount of the plating layer is not particularly limited, and may be a general amount of adhesion.

(Manufacturing method of the hot-embossed molded body of the present invention) Next, the form of the manufacturing method for obtaining the hot-embossed molded body of the present invention will be described, but the present invention is not limited to the form of the multilayer steel sheet described below.

As an embodiment of the manufacturing method of the present invention, first, the surface and / or the back surface of the steel plate that satisfies the component composition requirements of the central portion of the plate thickness is ground to remove surface oxides, and then the layer is softened on the ground side. Steel sheet for layer formation (hereinafter referred to as "steel sheet for surface layer"). The method for fixing the steel sheet for the surface layer and the steel sheet for the center portion of the plate thickness is not particularly limited, but may be performed by arc welding. In addition, it is preferable that any one or two or more of the C content, the Si content, and the Mn content of the laminated layer be 0.6 times or less the corresponding element content in the central portion of the sheet thickness, and the steel sheet for the surface layer is preferable.

In the continuous casting step of the steel sheet for the surface layer, by controlling the casting speed above ton / min, the microsegregation of Mn in the steel sheet for the surface layer can be suppressed, and the Mn concentration distribution in the steel sheet for the surface layer can be uniformly distributed. . Mn can increase the undulating strength of Vostian iron, and affect the formation behavior of grain boundaries in the metamorphic structure. Therefore, the area surrounded by grain boundaries with an orientation difference of 15 ° or more is defined as crystal grains. It has the effect of promoting the formation of crystal grains with a maximum crystal orientation difference within the crystal grains of 8 ° to 15 °. Therefore, in order to promote the generation of the above-mentioned microstructure, in the continuous casting step of the steel sheet for the surface layer, the casting speed can also be controlled to 6 ton / min or more.

In addition, it is preferable to further maintain the multilayer steel plate produced by the above method at a temperature of 1100 ° C or higher and 1350 ° C or lower for 20 minutes or longer and less than 60 minutes. Moreover, the maintained multilayer steel sheet is preferably used as the steel sheet for the hot-embossed formed body of the present invention. As a result of the review by the inventors, it can be seen that by performing a heat treatment at a temperature of 1100 ° C to 1350 ° C for 20 minutes to 60 minutes, when a region surrounded by a grain boundary having an orientation difference of 15 ° or more is defined as crystal grains, In the metal structure in a region from a depth of 20 μm below the surface of the softened layer to the center of the softened layer, the maximum crystal orientation difference between the crystal grains with a maximum crystal orientation difference of 1 ° or less inside the crystal grains and the inside of the aforementioned crystal grains is 8 The total area ratio of the crystal grains of ° to 15 ° will be 50% or more and less than 85%, and excellent bendability and hydrogen embrittlement resistance can be obtained.

The hot-embossed molded body of the present invention can be obtained by subjecting the laminated body (multilayer steel plate) produced by the above-mentioned manufacturing method to hot rolling, cold rolling, hot stamping, continuous melt plating, and the like.

The hot rolling may be performed under normal conditions. For example, as long as the completion temperature is also in a temperature range of 810 ° C or higher, it is not necessary to specify the subsequent cooling conditions, and the coiling is performed in a temperature range of 750 ° C or lower. Further, a reheating treatment may be performed for the purpose of softening the multilayer steel sheet after hot rolling.

However, in order to further promote the formation of the central part of the sheet thickness, the hot rolling of the multi-layered steel sheet after the heat treatment described above includes rough rolling and finished rolling, and the rough rolling reduction should be 5 in the thickness reduction per pass. % Or more and less than 50%, and the time between passes is 3 seconds or more, and it is performed twice or more at the temperature of 1100 degreeC or more.

Specifically, in order to further promote the formation of the plate thickness central portion of the present invention, it is necessary to control the alloying elements, and in particular, it is necessary to control the C atom concentration to be smoothly distributed. The distribution of C concentration can be obtained by the diffusion of C atoms, and the diffusion frequency of C atoms increases at higher temperatures. Therefore, in order to control the C concentration, the control from hot rolling to rough rolling becomes important. In the hot rolling heating, in order to promote the diffusion of C atoms, it is necessary to increase the heating temperature, preferably 1100 ° C or higher and 1350 ° C or lower, more preferably 1150 ° C or higher and 1350 ° C or lower. Changes in (i) and (ii) shown in Fig. (1) occur during hot rolling. (i) The diffusion of C atoms from the central portion of the plate thickness to the surface layer, and (ii) The decarburization reaction of C that is detached from the surface layer to the outside. And according to the equilibrium of the diffusion and detachment of the C atoms of (i) and (ii), a distribution will be generated in the C concentration. If it is lower than 1100 ° C., due to insufficient reaction of (i), a better C concentration distribution cannot be obtained. On the other hand, if the temperature is higher than 1350 ° C., the reaction of (ii) may be excessively generated, so a better concentration distribution cannot be obtained.

After adjusting the hot rolling heating temperature to control to a better C concentration distribution, in order to obtain the optimal C concentration distribution, the control of the passes in the rough rolling becomes extremely important. The rough rolling is performed twice or more under the conditions that the rough rolling temperature is 1100 ° C or higher, the thickness reduction per pass is 5% or more and less than 50%, and the time between passes is 3 seconds or more. This is because the strain introduced by the rough rolling can promote the diffusion of C atoms in (i) in FIG. (1). If a conventional method is used to rough-roll and finish-roll a steel slab after controlling the C concentration to a better state by hot rolling, the sheet thickness will be reduced in a state where C atoms cannot sufficiently diffuse in the surface layer. Therefore, if a conventional method of hot rolling is used to manufacture a hot-rolled steel sheet with a thickness of several millimeters from a steel slab having a thickness of more than 200 mm, it will become a steel sheet with a sharp change in the C concentration in the surface layer, and gentle hardness cannot be obtained. Variety. The method found in order to solve this situation is the above-mentioned rough rolling pass control. The diffusion of C atoms is not only affected by temperature, but also greatly affected by strain (differential row density). Especially, compared with the lattice diffusion, the diffusion frequency of the differential row diffusion will be increased by more than 10 times, so it needs to work hard to leave the differential row density and make the plate thickness thinner by rolling. Curve 1 in FIG. 2 shows the change in differential density after rolling passes when the reduction in plate thickness per pass of the rough rolling is small, and it can be seen that the strain persists for a long time. By allowing the strain to remain in the surface layer for a long time as described above, the diffusion of C atoms in the surface layer is sufficiently generated, and an optimal C concentration distribution can be obtained. On the other hand, curve 2 is the change in differential discharge density in the case of a large reduction in sheet thickness. When the amount of strain introduced by rolling increases, it will become easier to promote recovery, and the differential discharge density will decrease sharply. . Therefore, in order to obtain the optimal C concentration distribution, it is necessary to prevent the variation in the row density such as curve 2 from occurring. From the above point of view, the upper limit of the plate thickness reduction rate per pass will be less than 50%. In addition, in order to promote the diffusion of C atoms in the surface layer, a certain amount of differential row density and maintenance time must be ensured. Therefore, the lower limit of the plate thickness reduction rate will be 5%, and the time between passes must be ensured to be more than 3 seconds.

The cold rolling may be a cold rolling performed at a general rolling reduction rate, for example, 30 to 90%. The hot-rolled steel sheet and the cold-rolled steel sheet also include a steel sheet maintained in its original state, or a steel sheet obtained by subjecting the aforementioned hot-rolled steel sheet or cold-rolled steel sheet to recrystallization annealing under normal conditions, or a steel sheet obtained by temper rolling under normal conditions. .

The heating, molding and cooling steps during hot stamping can also be performed under normal conditions. For example, the hot rolled steel sheet after the hot rolled steel sheet coiled in the hot rolling step is rolled back, or the cold rolled steel sheet after the rolled hot rolled steel sheet is rolled back and cold rolled, or cold rolled The steel sheet is plated and heated at a heating rate of 0.1 ° C / s or higher to 200 ° C / s to a temperature of 810 ° C or higher and 1000 ° C or lower, and the steel sheet that has been maintained at this temperature is formed by ordinary hot stamping. It is a predetermined shape.

The maintenance time is not particularly limited as long as it is set according to the form. Further, the molded body after the hot stamping, which can be performed for 30 seconds to 600 seconds, for example, can be cooled to room temperature.

The cooling rate may be set to a general condition. For example, the average cooling rate in a temperature range from a heating temperature to more than 400 ° C may be 50 ° C / s or more. If the Si content in the central part of the sheet thickness is greater than 0.50% and less than 3.00%, and the Mn content in the central part of the sheet thickness is 0.20% or more and less than 1.50%, and the Si content in the central part of the sheet thickness is more than 0.50% When the steel sheet is less than 3.00% and the Mn content in the central part of the plate thickness is 1.50% or more and less than 3.00%, the purpose of increasing the amount of residual Vostian iron and improving ductility is to cool it after heating and maintenance. The average cooling rate in the temperature range from 200 ° C to 400 ° C should be controlled to less than 50 ° C / s.

In addition, for the purpose of adjusting strength and the like, tempering treatment can also be performed on the formed body that has been cooled to room temperature in the range of 150 ° C to 600 ° C.

In the manufacturing method of the hot-embossed molded body of the said embodiment, the center part of a plate | board thickness and a softening layer are each comprised with a different steel plate. However, the hot-embossed molded body of the present invention is not limited to the multilayer steel sheet obtained by laminating two steel sheets as described above. The central part of the plate thickness and the softened layer can also be formed in a single-material steel plate. For example, a single-layer steel sheet can be decarburized to soften the surface layer, thereby producing a high strength composed of the softened layer and the central part of the plate thickness. Steel plate.

Examples Next, the examples of the present invention will be described. However, the conditions in the examples are only one example of conditions used to confirm the feasibility and effect of the present invention, and the present invention is not limited by the one example of conditions. As long as the purpose of the present invention can be achieved without departing from the gist of the present invention, the present invention can adopt various conditions.

[Manufacturing Example A] The surface of the steel plate Nos. 1 to 18 ("Steel Nos. 1 to 18" in the table) of the plate thickness central portion having the chemical composition shown in Table A-1-1 was ground to remove surface oxides. . Then, on both sides or on one side of the steel plate for the central portion of each plate thickness, a steel plate for a surface layer having a chemical composition shown in Table A-1-2 was laminated by arc welding to prepare a laminate for a hot stamped molded body. Steel plate No.1 ~ 43. In addition, the total plate thickness of the steel sheet for the surface layer and the steel sheet for the central part after the arc welding is set to 200 mm to 300 mm, and the thickness of the steel sheet for the surface layer is set to about 1/3 of the thickness of the steel sheet for the central part (if For one side, it is about 1/4). The laminated steel plate No. 37 is steel in which a steel plate for a surface layer is welded to only one surface. Among the laminated steel plates Nos. 1 to 43 in Tables A-1-1 to A-1-2, the steel plate for the central portion of the plate thickness does not satisfy the composition requirements of the central portion of the plate thickness of the hot stamped molded body of the present invention. "Comparative steel" is displayed in the remarks column.

For laminated steel plates Nos. 1 to 43, the pre-hot rolling heat treatment, rough rolling, and hot rolling were performed under the conditions of manufacturing conditions No. 1 to 43 shown in Table A-2-1 to Table A-2-2. It is cold rolled and made into a steel sheet. Next, the steel plates were heat-embossed by performing the heat treatment shown in Tables A-2-1 to A-2-2 ("Heat Treatment of Hot-Stamped Molded Body" in the table) to produce No. 1A ~ 43A hot-embossed formed body (item "formed body" in Table A-3). In addition, for the hot-embossed molded bodies No. 35A and 36A, aluminum plating with an adhesion amount of 120 to 160 g / m ² is performed on the surface of the hot-dip plating line.

In the table, the item "sheet thickness reduction rate" of "rough rolling" means the sheet thickness reduction rate per pass of rough rolling, and the item "number of rolling times" refers to the time between passes of 3 seconds Rolling times under the above conditions. In addition, the item "Heating rate (° C / s)" in the table means the temperature increasing rate of the heating temperature that reaches the "heat treatment during hot stamping" after the cold rolling step. In addition, the item "heating temperature (° C)" in the "heat treatment during hot embossing" in the table refers to the temperature at the time of hot embossing, and the "average cooling rate (° C / s) (greater than 400 ° C)" means from the foregoing The average cooling rate (° C / s) in the temperature range from the heating temperature to more than 400 ° C, and the "average cooling rate (° C / s) (400 ° C or less)" refers to the temperature range from 200 ° C to 400 ° C Average cooling rate (℃ / s). In addition, in the table, a field with a symbol "-" indicates that the process has not been performed.

Table A-3 shows the metal structure and characteristics of the hot stamped molded bodies Nos. 1A to 43A. The components obtained by analyzing the plate thickness 1/2 position of the sample taken from the hot stamped molded body and the position 20 μm from the surface of the softened layer are shown in Table A-1-1 to Table A-1-2. Nos. 1 to 43 have the same composition as the steel plate for the center portion and the steel plate for the surface layer.

The metal structure of the steel sheet after hot embossing was measured by the method described previously, and the hardness of the steel sheet for the thickness center part constituting the center of the thickness and the thickness from the surface of the steel sheet for the surface layer constituting the softened layer to a thickness of 1/2 were calculated. The total area ratio of the crystal grains with the largest crystal orientation difference within 1 ° and the crystal grains with the crystal orientation difference between 8 ° and 15 ° in the metal structure of the area surrounded by the grain boundaries above 15 °. The calculated value of the aforementioned area ratio is shown in the item of Table A-3, "The total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less within the high-angle grain boundary and crystal grains with a maximum crystal orientation difference of 8 ° ~ 15 ° ( %) ".

A tensile test of the hot-embossed molded body was performed. The results are shown in Table A-3. The tensile test was carried out by preparing a test piece No. 5 described in JIS Z 2201 and performing the test in accordance with JIS Z 2241.

The hydrogen embrittlement resistance of the hot stamped formed body was evaluated using a test piece cut out from the formed body. Generally, a hot stamping molding system uses a joining method such as spot welding to join other parts, and applies a twist to the hot stamped molded body according to the shape accuracy of the part to add stress. The stress varies depending on the position of the part, and it is difficult to calculate it correctly, but it is considered that there is no practical problem as long as the delayed damage is not caused by the reduced stress. Therefore, a test piece having a thickness of 1.2 mm × width 6 mm × length 68 mm was cut out from the formed body, and a strain equivalent to a reduced stress was imparted by a four-point bending test, and then immersed in hydrochloric acid at pH 3 for 100 hours, and then evaluated for the occurrence of cracks Resistance to hydrogen embrittlement. A pass (○) was determined when no break was found, and a pass (×) was determined when there was a break.

For the purpose of evaluating the impact resistance characteristics of the hot stamped molded body, the evaluation was performed under the following measurement conditions according to the VDA standard (VDA238-100) stipulated by the German Automobile Industry Association. In the present invention, the displacement at the maximum load obtained in the bending test was converted to an angle based on the VDA standard, and the maximum bending angle was obtained, thereby evaluating the impact resistance characteristics of the hot stamped molded body.

Test piece size: 60mm (rolling direction) × 60mm (direction perpendicular to rolling) or 30mm (rolling direction) × 60mm (direction perpendicular to rolling) Bending edge: direction perpendicular to rolling Test method: roll support, punch extrusion roll diameter: φ30mm punch shape: front end R = 0.4mm distance between rolls: 2.0 × plate thickness (mm) + 0.5mm extrusion speed: 20mm / min testing machine: SIMAZU AUTOGRAPH 20kN

In the case where the tensile strength is 1500 MPa or more, the maximum bending angle (°) is 70 (°) or more, and the hydrogen embrittlement resistance is acceptable, the impact resistance and hydrogen embrittlement resistance are excellent, and are considered as examples of the invention. If any of the above three properties is not satisfied, it is regarded as a comparative example.

In the hot-embossed molded body of the example of the present invention, crystal grains having a maximum crystal orientation difference of 1 ° or less in a region surrounded by grain boundaries of 15 ° or more in the metal structure from the surface of the steel sheet for the surface layer to a thickness of 1/2. The total area ratio of crystal grains with a crystal orientation difference of 8 ° to 15 ° is 50% or more and less than 85%. In addition, the hot stamped molded body of the examples of the present invention is excellent in tensile strength, bendability, and hydrogen embrittlement resistance.

In contrast, the hot stamped molded body of No. 5A has a low carbon content in the steel plate for the center portion of the plate thickness, so the hardness at the center portion of the plate thickness becomes insufficient, and the tensile strength becomes insufficient. Since the hot stamped molded body of No. 9A has too much carbon content in the steel plate for the central part of the plate thickness, the hardness of the central part of the plate thickness also becomes too high, and the target bendability cannot be obtained. Moreover, since the Mn content of the steel plate for the center part of a plate thickness was scarce in the hot stamping molded body of No. 11A, the hardness of the center part of a plate thickness became inadequate, and the tensile strength became inadequate.

The hot stamping system No. 30A to 32A is a comparative example produced by using a laminated steel plate for a hot stamped molded body that has not been subjected to a preferable heat treatment before the hot stamping step. No. 30A hot-embossed molded body has a low heat treatment temperature before the hot embossing step, and No. 31A hot-embossed molded body has a thickness of 1 from the surface of the softened layer due to the short heat treatment time before the hot embossing step. Among the metal structures of the softened layer up to / 2, the growth of the soft structure and the intermediate hardness metal structure becomes insufficient, and the target bendability cannot be obtained. In addition, the hot stamped molded body of No. 32A had an excessively high heat treatment temperature before the hot stamping step, so that it was not possible to obtain the effect of reducing the sharp hardness gradient in the thickness direction during bending deformation.

The hot rolling embossing body of No. 41A has a low rolling temperature for rough rolling. Moreover, the thickness reduction rate of the rough rolling of the hot stamped molded body of No. 42A was low. In addition, the hot-embossed molded body of No. 43A has a small number of rolling times under the condition that the pass-through time is 3 seconds or more. These hot-embossed molded bodies were not manufactured under appropriate rough rolling conditions, so the soft structure and the intermediate hardness metal structure did not grow sufficiently, and the strain caused by bending deformation could not be alleviated, and the target bending could not be obtained. Sex.

Manufacture No.44 hot stamping system. In the continuous casting step of the steel sheet for the surface layer, the steel sheet is controlled to a casting speed of 6ton / min or more, and the metal can be increased from the surface of the steel sheet for the surface layer to a thickness of 1/2. The total area ratio (%) of the crystal grains with the largest crystal orientation difference within 1 ° and the crystal grain orientation difference between 8 ° ~ 15 ° within the area surrounded by the grain boundaries of 15 ° or more in the structure, and excellent bendability .

[Table A-1-1]

[Table A-1-2]

[Table A-2-1]

[Table A-2-2]

[Table A-3]

[Manufacturing example B] Grinding the surface of steel plate Nos. 1 to 18 ("Steel Nos. 1 to 18" in Table B-1-1) for the plate thickness central portion having the chemical composition shown in Table B-1-1 Remove surface oxides. Then, on both sides or on one side of the steel sheet for the central portion of each plate thickness, a steel sheet for a surface layer having a chemical composition shown in Table B-1-2 was laminated by arc welding to prepare a laminate for a hot stamped molded body. Steel plates No.1 ~ 41. In addition, the total plate thickness of the steel sheet for the surface layer and the steel sheet for the central part after the arc welding is set to 200 mm to 300 mm, and the thickness of the steel sheet for the surface layer is set to about 1/3 of the thickness of the steel sheet for the central part (if For one side, it is about 1/4). The laminated steel plate No. 37 is steel in which a steel plate for a surface layer is welded to only one surface. Laminated steel sheets other than No. 37 are steel sheets for surface layers welded to both surfaces of the steel sheet for the central portion of each plate thickness. In the laminated steel plate Nos. 1 to 41 of Table B-1-3, the steel plate for the central portion of the plate thickness that does not satisfy the composition requirements of the central portion of the plate thickness of the hot stamped body of the present invention is displayed in the remarks column as "Comparison steel".

For laminated steel sheets No. 1 to 41, the pre-hot rolling heat treatment, rough rolling, and hot rolling rolling were performed under the conditions of manufacturing conditions No. 1 to 41 shown in Tables B-2-1 to Table B-2-2. It is cold rolled and made into a steel sheet. Next, the steel plates were heat-embossed by performing the heat treatment shown in Tables B-2-1 to B-2-2 ("Heat treatment of hot-embossed formed bodies" in the table) to produce No., respectively. 1B ~ 41B hot-embossed molded articles (items "molded articles" in Table B-3-1 and Table B-3-2). In addition, for the hot-embossed molded bodies No. 35B and 36B, aluminum plating with an adhesion amount of 120 to 160 g / m ² is performed on the surface of the hot-dip plating line. In addition, the items in Table B-2-1 to Table B-2-2 correspond to the items in Table A-2-1 to Table A-2-2, respectively. In addition, in the table, a field with a symbol "-" indicates that the process has not been performed.

Table B-3-1 and Table B-3-2 show the metal structure and characteristics of the hot stamped molded body Nos. 1B to 41B. The components obtained by analyzing the plate thickness 1/2 position (plate thickness center portion) of the sample taken from the hot stamped molded body and the position 20 μm from the surface of the softened layer are shown in Table B-1-1 to Table B- The components of the laminated steel plates No. 1 to No. 1 to No. 1 to No. 1 to No. 1 to No. 1 in the central portion of the plate thickness and those in the surface layer are equivalent.

The metal structure of the steel sheet after hot embossing was measured by the method described previously, and the hardness of the steel sheet for the thickness center part constituting the central part of the thickness and the thickness from the surface of the steel sheet for the surface layer constituting the softened layer to the softened layer were calculated. Total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less and crystal grains with a crystal orientation difference of 8 ° to 15 ° in a region surrounded by grain boundaries of 15 ° or more in a metal structure up to 1/2 (% ). The calculated values of the aforementioned area ratios are shown in the items in Table B-3-1 to Table B-3-2, "The maximum crystal orientation difference within 1 ° in the high-angle grain boundary is 8 ° ~ 15 and the maximum crystal orientation difference. Total area ratio (%) of crystal grains ".

For each hot-embossed molded body No. 1B to 41B, the average hardness (HV) and the minimum hardness (HV) of the center portion of the plate thickness (the position where the plate thickness is 1/2) were measured by the method described previously. The measurement results are shown in Tables B-3-1 to B-3-2. The difference between the average hardness (HV) and the minimum hardness (HV) for each hot-embossed molded body Nos. 1B to 41B is shown in Table B-3-1 to Table B-3-2, "Hardness Variation in Cross Section". In addition, those having a cross-section hardness variation of 100 HV or more were considered unacceptable.

A tensile test of the hot-embossed molded body was performed. The results are shown in Tables B-3-1 to B-3-2. The tensile test was carried out by preparing a test piece No. 5 described in JIS Z 2201 and performing the test in accordance with JIS Z 2241.

The hydrogen embrittlement resistance of the hot stamped molded body was evaluated in the same manner as in Production Example A using a test piece cut out from the molded body. That is, a test piece having a plate thickness of 1.2 mm × width 6 mm × length 68 mm was cut out from the formed body, and a strain equivalent to a reduced stress was applied by a four-point bending test, and then immersed in hydrochloric acid at pH 3 for 100 hours, and then cracked with or without cracks. Evaluation of hydrogen embrittlement resistance. A pass (○) was determined when no break was found, and a pass (×) was determined when there was a break.

For the purpose of evaluating the impact resistance characteristics of the hot stamped molded body, the evaluation was performed under the same measurement conditions as those in Production Example A in accordance with the VDA standard (VDA238-100) prescribed by the German Automobile Industry Association. In the present invention, the displacement at the maximum load obtained in the bending test was converted to an angle based on the VDA standard, and the maximum bending angle was obtained, thereby evaluating the impact resistance characteristics of the hot stamped molded body.

In the case where the tensile strength is 1500 MPa or more, the maximum bending angle (°) is 70 (°) or more, and the hydrogen embrittlement resistance is acceptable, the impact resistance and hydrogen embrittlement resistance are excellent, and are considered as examples of the invention. If any of the above three properties is not satisfied, it is regarded as a comparative example.

In the hot-embossed molded body of the example of the present invention, crystal grains having a maximum crystal orientation difference of 1 ° or less in a region surrounded by grain boundaries of 15 ° or more in the metal structure from the surface of the steel sheet for the surface layer to a thickness of 1/2. The total area ratio (%) of the crystal grains with a crystal orientation difference of 8 ° to 15 ° is 50% or more and less than 85%. In addition, the hot stamped molded body of the examples of the present invention is excellent in tensile strength, bendability, and hydrogen embrittlement resistance.

In contrast, the hot stamped molded body of No. 5B has a low carbon content in the steel plate for the center portion of the plate thickness, so the hardness at the center portion of the plate thickness becomes insufficient, and the tensile strength becomes insufficient. The hot stamped molded body of No. 9B has too much carbon content in the steel plate for the central portion of the plate thickness, and therefore the hardness of the central portion of the plate thickness is too high, and the target bendability cannot be obtained. Moreover, since the Mn content of the steel plate for the center part of plate thickness is scarce in the hot stamping molded body of No. 11B, the hardness of the center part of a plate thickness becomes inadequate, and the tensile strength becomes inadequate.

The hot stamping forming system No. 30B to 32B is a comparative example produced by using a laminated steel sheet for a hot stamped formed body without applying a preferable heat treatment before the hot stamping step. No. 30B hot-embossed molded body has a low heat treatment temperature before the hot-embossing step, and No. 31B hot-embossed molded body has a thickness of 1 from the surface of the softened layer due to the short heat-treatment time before the hot-imprinting step Among the metal structures of the softened layer up to / 2, the growth of the soft structure and the intermediate hardness metal structure becomes insufficient, and the target bendability cannot be obtained. In addition, the hot stamping molded body of No. 32B had an excessively high heat treatment temperature before the hot stamping step, so it was not possible to obtain an effect of reducing a sharp hardness gradient in the thickness direction during bending deformation.

The hot rolling embossing body of No. 38B has a low rolling temperature for rough rolling. Moreover, the thickness reduction rate of the rough rolling of the hot stamped molded body of No. 39B was low. In addition, the hot-embossed molded body of No. 40B has a small number of rolling times under the condition that the time between passes is 3 seconds or more. These hot-embossed molded bodies were not manufactured under appropriate rough rolling conditions, so the soft structure and the intermediate hardness metal structure did not grow sufficiently, and the strain caused by bending deformation could not be alleviated, and the target bending could not be obtained. Sex.

The hot stamping system of No41B controls the casting speed of the steel sheet above 6ton / min in the continuous casting step of the steel sheet for the surface layer, and can increase the metal structure from the surface of the steel sheet to the thickness of 1/2 The total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less and crystal grains with a crystal orientation difference of 8 ° to 15 ° in the area surrounded by the grain boundaries above the degree is excellent in bendability.

[Table B-1-1]

[Table B-1-2]

[Table B-1-3]

[Table B-2-1]

[Table B-2-2]

[Table B-3-1]

[Table B-3-2]

[Manufacturing Example C] The surface of a steel plate for a center portion of a plate having a chemical composition shown in Tables C-1-1 to C-1-2 was ground to remove surface oxides. Then, on both sides or on one side of the steel sheet for the central portion of each plate thickness, a steel sheet for a surface layer having a chemical composition shown in Tables C-1-3 to C-1-4 was laminated by arc welding, and heat was produced. Laminated steel plates Nos. 1 to 49 for embossed molded bodies. In addition, the total plate thickness of the steel sheet for the surface layer and the steel sheet for the central part after the arc welding is set to 200 mm to 300 mm, and the thickness of the steel sheet for the surface layer is set to about 1/3 of the thickness of the steel sheet for the central part (if For one side, it is about 1/4). The laminated steel plate No. 31 is a steel in which a steel plate for a surface layer is welded to only one surface. Among the laminated steel plates Nos. 1 to 53 in Tables C-1-1 to C-1-4, the steel plate for the central portion of the plate thickness does not satisfy the composition requirements of the central portion of the plate thickness of the hot stamped molded product of the present invention. "Comparative steel" is displayed in the remarks column.

Table C-1-3 to Table C-1-4 "C, Si, Mn content ratios to the steel sheet for the surface layer with respect to the steel sheet for the central part of the thickness" shows the laminated steel sheet No. for each hot stamped formed body .1 to 53, the ratio of the C, Si, and Mn contents of the steel sheet for the surface layer to the C, Si, and Mn contents of the steel sheet for the central part of the thickness.

For laminated steel plates No. 1 to 53, respectively, heat treatment before hot rolling, rough rolling, and hot rolling are performed under the conditions of manufacturing conditions No. 1 to 53 shown in Tables C-2-1 to Table C-2-2. It is cold rolled and made into a steel sheet. Next, the steel plates were heat-embossed by performing the heat treatment shown in Tables C-2-1 to C-2-2 ("Heat treatment of hot-embossed formed bodies" in the table) to produce No., respectively. 1C ~ 53C hot-embossed molded article (item "molded article" of Table C-3-1 ~ Table C-3-2). In addition, for the hot-embossed molded body No. 30C, aluminum plating was performed on the surface of the hot-dip plating line with an adhesion amount of 120 to 160 g / m ² . In addition, the items in Table C-2-1 to Table C-2-2 correspond to the items in Table A-2-1 to Table A-2-2, respectively. In addition, in the table, a field with a symbol "-" indicates that the process has not been performed.

Tables C-3-1 to C-3-2 show the metal structure and characteristics of the hot stamped molded body Nos. 1C to 53C. The components obtained by analyzing the plate thickness 1/2 position (plate thickness center portion) of the sample taken from the hot stamped molded body and the position 20 μm from the surface of the softened layer are shown in Table C-1-1 to Table C- The components of the laminated steel plates No. 1 to No. 1 to No. 1 to No. 1 to No. 1 to No. 53 are equal to those of the steel plate for the central portion and the steel plate for the surface layer.

The metal structure of the steel sheet after hot embossing was measured by the method described previously, and the hardness of the steel sheet for the thickness center part constituting the central part of the thickness and the thickness from the surface of the steel sheet for the surface layer constituting the softened layer to the softened layer were calculated. The total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less and crystal grains with a crystal orientation difference of 8 ° to 15 ° in a region surrounded by grain boundaries of 15 ° or more in a metal structure up to 1/2. The calculated values of the aforementioned area ratios are shown in the items in Tables C-3-1 to C-3-2, "The maximum crystal orientation difference within 1 ° in high-angle grain boundaries is less than 8 ° and the maximum crystal orientation difference. Total area ratio (%) of crystal grains ".

A tensile test of the hot-embossed molded body was performed. The results are shown in Tables C-3-1 to C-3-2. The tensile test was carried out by preparing a test piece No. 5 described in JIS Z 2201 and performing the test in accordance with JIS Z 2241.

The hydrogen embrittlement resistance of the hot stamped molded body was evaluated in the same manner as in Production Example A using a test piece cut out from the molded body. That is, a test piece having a plate thickness of 1.2 mm × width 6 mm × length 68 mm was cut out from the formed body, and a strain equivalent to a reduced stress was applied by a four-point bending test, and then immersed in hydrochloric acid at pH 3 for 100 hours, and then cracked with or without cracks. Evaluation of hydrogen embrittlement resistance. A pass (○) was determined when no break was found, and a pass (×) was determined when there was a break.

For the purpose of evaluating the impact resistance characteristics of the hot stamped molded body, the evaluation was performed under the same measurement conditions as those in Production Example A in accordance with the VDA standard (VDA238-100) prescribed by the German Automobile Industry Association. In the present invention, the displacement at the maximum load obtained in the bending test was converted to an angle based on the VDA standard, and the maximum bending angle was obtained, thereby evaluating the impact resistance characteristics of the hot stamped molded body.

When the tensile strength is 1500 MPa or more, the maximum bending angle (°) is 70 (°) or more, the uniform elongation is 5% or more, and the cases where the hydrogen embrittlement resistance is acceptable are impact resistance, hydrogen embrittlement resistance, and extension. It has excellent properties and is regarded as an invention example. If any of the above three properties is not satisfied, it is regarded as a comparative example.

In the hot-embossed molded body of the example of the present invention, the maximum crystal orientation difference in the region surrounded by grain boundaries of 15 ° or more in the metal structure from the surface of the steel sheet for the surface layer to 1/2 of the thickness of the steel sheet for the surface layer is 1 The total area ratio of crystal grains below ° and crystal grains with a crystal orientation difference between 8 ° and 15 ° is 50% or more and less than 85%. In addition, the hot stamped molded body of the examples of the present invention is excellent in tensile strength, bendability, and hydrogen embrittlement resistance.

On the other hand, in the hot-embossed molded body of No. 5C, since the carbon content of the steel plate for the central portion of the plate thickness is small, the hardness of the central portion of the plate thickness becomes insufficient, and the tensile strength becomes insufficient. Since the hot stamped molded body of No. 9C has too much carbon content in the steel plate for the central part of the plate thickness, the hardness of the central part of the plate thickness also becomes too high, and the target bendability cannot be obtained. In addition, the content of Si in the steel plate for the central portion of the plate thickness central portion of No. 11C was low, and the area fraction of the residual Vostian iron (γ) in the metal structure of the central portion of the plate thickness was less than 1.0%, which was uniform. Low elongation.

No. 25C ~ 27C, 49C hot stamping forming system is a comparative example produced by using a laminated steel plate for a hot stamped molded body which is not applied with a preferable heat treatment before the hot stamping step. Since the heat treatment temperature before the hot embossing step is too low in No. 25C, the growth of soft structure and intermediate hardness metal structure becomes insufficient, and the influence of the surface properties of the hot embossed body cannot be ruled out. And the influence of the migration from the central part of the plate thickness to the softened layer, and excellent bendability cannot be obtained.

In addition, in the hot-embossed molded body of No. 26C, since the heat treatment time before the hot-embossing step is too long, the growth of the soft structure and the intermediate-hardness metal structure becomes excessive, and the hardness difference between the softened layer and the center portion of the plate thickness changes If it is too large, the effect of reducing the sharp hardness gradient in the thickness direction of the plate during bending deformation cannot be obtained. Therefore, the target bendability cannot be obtained by manufacturing the hot stamped molded body of No. 26C.

In addition, in the hot-embossed molded bodies of Nos. 27C and 49C, the heat treatment time before the hot-embossing step was too long, so the hardness difference between the softened layer and the center of the plate thickness became too large, and because the heat treatment temperature was too high, The effect of reducing the sharp hardness gradient in the thickness direction of the plate during bending deformation is obtained. Therefore, the target bendability could not be obtained in the hot-embossed molded bodies manufactured in Nos. 27C and 49C.

The hot rolling embossing body No. 50C has a low rolling temperature for rough rolling. Moreover, the thickness reduction rate of the rough rolling of the hot stamping molded body of No. 51C was low. In addition, the hot-embossed molded body of No. 52C has a small number of rolling times under the condition that the time between passes is 3 seconds or more. These hot-embossed molded bodies were not manufactured under appropriate rough rolling conditions, so the soft structure and the intermediate hardness metal structure did not grow sufficiently, and the strain caused by bending deformation could not be alleviated, and the target bending could not be obtained. Sex.

The hot stamping system of No.53C controls the casting speed of the steel sheet above 6ton / min in the continuous casting step of the steel sheet for the surface layer, and can improve the metal structure from the surface of the steel sheet for the surface layer to a thickness of 1/2. In the area surrounded by grain boundaries of 15 ° or more, the total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less and crystal grains with a crystal orientation difference of 8 ° ~ 15 °, and excellent bendability.

[Table C-1-1]

[Table C-1-2]

[Table C-1-3]

[Table C-1-4]

[Table C-2-1]

[Table C-2-2]

[Table C-3-1]

[Table C-3-2]

[Manufacturing example D] Grinding steel plate Nos. 1 to 37 for plate thickness central portions having chemical compositions shown in Tables D-1-1 and D-1-2 ("Steel Nos. 1 to 37" in the table) Surface, remove surface oxides. Then, on both sides or on one side of the steel plate for the central portion of each plate thickness, a steel plate for a surface layer having a chemical composition shown in Tables D-1-3 and D-1-4 was laminated by arc welding to produce a heat. Laminated steel plates No. 1 to 60 for embossed molded bodies. In addition, the total plate thickness of the steel sheet for the surface layer and the steel sheet for the central part after the arc welding is set to 200 mm to 300 mm, and the thickness of the steel sheet for the surface layer is set to about 1/3 of the thickness of the steel sheet for the central part (if For one side, it is about 1/4). The laminated steel plate No. 37 is steel in which a steel plate for a surface layer is welded to only one surface. Laminated steel sheets other than No. 37 are steel sheets for surface layers welded to both surfaces of the steel sheet for the central portion of each plate thickness. In the laminated steel plates No. 1 to 60 of Table D-1-1 to Table D-1-4, the steel plate for the central portion of the plate thickness does not satisfy the composition requirements of the central portion of the plate thickness of the hot stamped molded product of the present invention. "Comparative steel" is displayed in the remarks column.

For laminated steel plates No. 1 to 60, heat treatment before hot rolling, rough rolling and hot rolling are performed under the conditions of manufacturing conditions No. 1 to 60 shown in Tables D-2-1 to D-2-3. It is cold rolled and made into a steel sheet. Next, the steel plates were heat-embossed by performing the heat treatment shown in Tables D-2-1 to D-2-3 ("Heat treatment of hot-embossed formed bodies" in the table) to produce No., respectively. 1D ~ 60D hot-embossed molded article (item "molded article" in Table D-3-1 ~ D-3-3). In addition, for the hot-embossed molded bodies No. 38D and 39D, aluminum plating was performed on the surface of the hot-dip plating line with an adhesion amount of 120 to 160 g / m ² . In addition, the items in Table D-2-1 to Table D-2-3 correspond to the items in Table A-2-1 to Table A-2-2, respectively. In addition, in the table, a field with a symbol "-" indicates that the process has not been performed.

Tables D-3-1 to D-3-3 show the metal structure and characteristics of the hot stamped molded body Nos. 1D to 60D. The components obtained by analyzing the plate thickness 1/2 position (plate thickness center portion) of the sample taken from the hot stamped molded body and the position 20 μm from the surface of the softened layer are shown in Table D-1-1 to Table D- The components of the laminated steel plates No. 1 to No. 1 to No. 1 to No. 1 to No. 60 are equal to those of the steel plate for the central portion and the steel plate for the surface layer.

The metal structure of the steel sheet after hot embossing was measured by the method described previously, and the hardness of the steel sheet for the thickness center part constituting the central part of the thickness and the thickness from the surface of the steel sheet for the surface layer constituting the softened layer to the softened layer were calculated. The total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less and crystal grains with a crystal orientation difference of 8 ° to 15 ° in a region surrounded by grain boundaries of 15 ° or more in a metal structure up to 1/2. The calculated values of the aforementioned area ratios are shown in the items of Tables D-3-1 to D-3-3, "The crystal grains with a maximum crystal orientation difference of 1 ° or less in the high-angle grain boundary and the maximum crystal orientation difference of 8 ° ~ 15 °. The total area ratio (%) of the crystal grains ".

The tensile test of the hot-embossed molded body Nos. 1D to 60D was performed. The results are shown in Tables D-3-1 to D-3-3. The tensile test was carried out by preparing a test piece No. 5 described in JIS Z 2201 and performing the test in accordance with JIS Z 2241.

The hydrogen embrittlement resistance of the hot stamped molded body was evaluated in the same manner as in Production Example A using a test piece cut out from the molded body. That is, a test piece having a plate thickness of 1.2 mm × width 6 mm × length 68 mm was cut out from the formed body, and a strain equivalent to a reduced stress was applied by a four-point bending test, and then immersed in hydrochloric acid at pH 3 for 100 hours, and then cracked with or without cracks. Evaluation of hydrogen embrittlement resistance. A pass (○) was determined when no break was found, and a pass (×) was determined when there was a break.

For the purpose of evaluating the impact resistance characteristics of the hot stamped molded body, the evaluation was performed under the same measurement conditions as those in Production Example A in accordance with the VDA standard (VDA238-100) prescribed by the German Automobile Industry Association. In the present invention, the displacement at the maximum load obtained in the bending test was converted to an angle based on the VDA standard, and the maximum bending angle was obtained, thereby evaluating the impact resistance characteristics of the hot stamped molded body.

The impact resistance of the hot stamped molded body was also evaluated from the viewpoint of ductility. Specifically, the uniform elongation of the steel sheet is obtained by a tensile test of the steel sheet after hot stamping to evaluate the impact resistance characteristics. The tensile test is performed by preparing test piece No. 5 described in JIS Z 2201 and implementing it in accordance with the test method described in JIS Z 2241. The elongation at which the maximum tensile load can be obtained is uniform elongation.

The localized softened part deforms during the impact and becomes the main cause of cracking. Therefore, the hardness of the formed body is small, that is, to ensure stable strength, and it is important to ensure the impact resistance. Therefore, the impact resistance characteristics of the hot stamped molded body were also evaluated from the viewpoint of uneven hardness. A cross section perpendicular to the long side direction was taken at an arbitrary position in the long side direction of the long hot-embossed molded body, and the hardness at the center of the thickness of the entire cross-sectional area including the vertical wall was measured. During the measurement, a Vickers test machine was used, and the measurement load was set to 1 kgf, the number of measurement points was set to 10 points, and the measurement interval was set to 1 mm. The difference between the average cross-section hardness and the minimum hardness is shown in Tables D-3-1 to D-3-3. In the case where no measurement point is lower than the average value of 100Hv of all measurement points, the hardness variation is small, that is, the strength stability is excellent, and as a result, it is considered to be excellent in impact resistance, so it is qualified, and it has a low 100Hv. Failed at the measurement point.

The tensile strength is 1500 MPa or more, and the uniform elongation is 5% or more. The hardness is qualified, the maximum bending angle (°) is 70.0 (°) or more, and the hydrogen embrittlement resistance is evaluated as impact resistance and resistance. Hot-embossed molded bodies (hydrogen embrittlement) having excellent hydrogen embrittlement properties (Examples of inventions in Tables D-3-1 to D-3-3). On the other hand, if any of the above five properties is not satisfied, it is regarded as a comparative example.

In the hot-embossed molded body of the example of the present invention, crystal grains having a maximum crystal orientation difference of 1 ° or less in a region surrounded by grain boundaries of 15 ° or more in the metal structure from the surface of the steel sheet for the surface layer to a thickness of 1/2. The total area ratio of crystal grains with a crystal orientation difference of 8 ° to 15 ° is 50% or more and less than 85%. In addition, the hot stamped molded body of the examples of the present invention is excellent in tensile strength, bendability, and hydrogen embrittlement resistance.

In contrast, the hot stamped molded body of No. 5D has a low carbon content in the steel plate for the center portion of the plate thickness, so the hardness at the center portion of the plate thickness becomes insufficient, and the tensile strength becomes insufficient. Since the hot stamped molded body of No. 9D has too much carbon content in the steel plate for the center of the plate thickness, the hardness of the center of the plate thickness also becomes too high, and the target bendability cannot be obtained. In addition, the hot-embossed molded bodies of No. 10D and No. 11D had insufficient Si content in the steel plate for the central portion of the plate thickness, and therefore had insufficient uniform elongation. In addition, in the hot-embossed molded body of No. 12D, the Mn content was insufficient, so the hardness at the center of the plate thickness was insufficient, and the tensile strength was insufficient. The hot stamped molded bodies of No. 14D and No. 15D are deficient in Si content and Mn content, so the area fraction of residual Vosted iron becomes less than 1.0%, and the uniform elongation is insufficient. In addition, the hot stamped molded bodies No. 12D to No. 15D are unqualified regardless of hardness.

The hot stamping forming system No. 33D to 35D is a comparative example made by using a laminated steel plate for a hot stamped formed body without applying a preferable heat treatment before the hot stamping step. No. 33D hot-embossed molded body has a low heat treatment temperature before the hot-embossing step, so among the metal structure of the softened layer from the surface of the softened layer to a thickness of 1/2, the soft structure and the metal structure of intermediate hardness The growth becomes insufficient, and the target flexibility cannot be obtained. No.34D hot-embossed molded body has a high heat treatment temperature before the hot-embossing step, so the microstructure fraction from the position of 20 μm from the surface of the softened layer to the depth of 1/2 of the thickness of the softened layer will develop to greater than 85%. Therefore, in the hot-embossed molded body of No. 34D, since the hardness difference between the softened layer and the center of the plate thickness becomes too large, the effect of reducing the sharp hardness gradient in the direction of the plate thickness generated during bending deformation cannot be obtained. In addition, the hot stamped molded body of No. 35D has a short heat treatment time before the hot stamping step. Therefore, among the metal structure of the softened layer from the surface of the softened layer to a thickness of 1/2, the soft structure and intermediate hardness The growth of the metal structure becomes insufficient, and the target bendability cannot be obtained.

No. 40D hot-embossed molded body has excessive Si content, so the residual Vosted iron is excessively generated to an area fraction of more than 5%. Therefore, the hot stamped molded body of No. 40D is inferior in flexibility. Since the hot-embossed molded body No. 41D has an excessive Mn content, the tensile strength of the hot-embossed molded body Nos. 1D to 56D becomes the largest and the bendability deteriorates. The hot stamped molded body of No. 42D is deficient in the content of acid-soluble aluminum, so that oxygen-containing inclusions are excessively formed, and the flexibility is deteriorated. In addition, since the hot-embossed molded body of No. 45D contains excessive aluminum, an oxide mainly composed of aluminum is excessively generated, and the flexibility is deteriorated.

The hot rolling embossing body of No. 57D has a low rolling temperature for rough rolling. Moreover, the thickness reduction rate of the rough rolling of the hot stamped molded body of No. 58D was low. In addition, the hot-embossed molded body of No. 59D has a small number of rolling times under the condition that the time between passes is 3 seconds or more. These hot-embossed molded bodies were not manufactured under appropriate rough rolling conditions, so the soft structure and the intermediate hardness metal structure did not grow sufficiently, and the strain caused by bending deformation could not be alleviated, and the target bending could not be obtained. Sex.

The hot stamping system of No60D controls the casting speed of the steel sheet above 6ton / min in the continuous casting step of the steel sheet for the surface layer, and can increase the metal structure from the surface of the steel sheet for the surface layer to a thickness of 1/2. 15 The total area ratio of crystal grains with a maximum crystal orientation difference of 1 ° or less and crystal grains with a crystal orientation difference of 8 ° to 15 ° in the area surrounded by the grain boundaries above the degree is excellent in bendability.

[Table D-1-1]

[Table D-1-2]

[Table D-1-3]

[Table D-1-4]

[Table D-2-1]

[Table D-2-2]

[Table D-2-3]

[Table D-3-1]

[Table D-3-2]

[Table D-3-3]

Industrial Applicability The hot-embossed molded article of the present invention is excellent in strength, ductility, bendability, impact resistance, and hydrogen embrittlement resistance, and has small hardness variations, so it is suitable for use in automobiles or structures that require strength. Structural members and reinforcement members.

FIG. 1 is a schematic diagram illustrating the diffusion of C atoms during the manufacture of the hot-embossed molded article of the present invention. FIG. 2 is a graph showing a change in differential row density after rolling passes related to the rough rolling used in the method for producing a hot-embossed molded article of the present invention.

Claims (8)

A hot-embossed molded body comprising a central portion of plate thickness and softening layers disposed on both sides or one side of the central portion of the plate thickness, the hot-embossed portion includes the central portion of the plate thickness in mass% : C: 0.20% or more and less than 0.70%, Si: less than 3.00%, Mn: 0.20% or more and less than 3.00%, P: 0.10% or less, S: 0.10% or less, sol.Al: 0.0002% or more and 3.000% or more Below, N: 0.01% or less, and the remainder is composed of Fe and unavoidable impurities, and has a hardness of 500 Hv or more and 800 Hv or less; from a depth of 20 μm below the surface of the softened layer to 1/2 of the thickness of the softened layer In a deep metal structure, in terms of a section parallel to the plate thickness direction, when a region surrounded by a grain boundary having an azimuth difference of 15 ° or more is defined as a crystal grain, the maximum crystal orientation difference inside the crystal grain is 1 ° or less The total area ratio of the crystal grains having the largest crystal orientation difference between the crystal grains of the above and the crystal grains of 8 ° or more and 15 ° or less is 50% or more and less than 85%. For example, the hot-embossed molded article of claim 1 has a Si content of 0.50% or less and a Mn content of 0.20% or more and less than 1.50%. For example, the hot-embossed molded article of claim 1 has a Si content of 0.50% or less and a Mn content of 1.50% or more and less than 3.00%. For example, the hot-embossed molded article of claim 1 has a Si content of more than 0.50% and less than 3.00%, an Mn content of 0.20% and less than 1.50%, and the aforementioned plate thickness central portion includes 1.0% or more in terms of area fraction and Less than 5.0% of residual Vostian iron. For example, the hot-embossed molded article of claim 1 has a Si content of more than 0.50% and less than 3.00%, an Mn content of 1.50% and more and less than 3.00%, and the aforementioned plate thickness central portion includes 1.0% or more in terms of area fraction and Less than 5.0% of residual Vostian iron. The hot-embossed molded body according to any one of claims 1 to 5, wherein the central part of the plate thickness further contains Ni in mass%: 0.01% or more and 3.00% or less. The hot-embossed molded body according to any one of claims 1 to 6, wherein the central portion of the aforementioned plate thickness further includes one or more of the following elements in mass%: Nb: 0.010% or more and 0.150% or less, Ti: 0.010% or more and 0.150% or less, Mo: 0.005% or more and 1.000% or less, and B: 0.0005% or more and 0.0100% or less. The hot stamped molded body according to any one of claims 1 to 7, wherein a plated layer is formed on the softened layer.