The present invention relates to a hot-formed member and a method for manufacturing the same.
background
[2]
Recently, due to the depletion of petroleum energy resources and high interest in the environment, regulations on improving fuel efficiency of automobiles are getting stronger day by day. From a material point of view, one way to improve fuel efficiency of automobiles is to reduce the thickness of steel sheets used in automobiles. Strength improvement should be supported.
[3]
For this reason, the demand for high-strength steel sheets has been continuously generated, and various types of steel sheets have been developed. However, since these steel sheets have high strength by themselves, there is a problem in that the workability is poor. That is, since the product of strength and elongation for each grade of steel sheet always tends to have a constant value, when the strength of the steel sheet increases, there is a problem that the elongation, which is an index of workability, decreases.
[4]
In order to solve this problem, a hot press forming method has been proposed. The hot press forming method is a method of increasing the strength of the final product by forming a low-temperature structure such as martensite in the steel sheet by processing the steel sheet at a high temperature suitable for processing and then cooling the steel sheet to a low temperature. In this case, there is an advantage that the problem of workability can be minimized when manufacturing a member having high strength.
[5]
However, in the case of the hot press forming method, since the steel sheet is heated to a high temperature, the surface of the steel sheet is oxidized, and thus there is a problem that a process of removing oxides from the surface of the steel sheet must be added after press forming. As a method for solving this problem, the technique of US Patent Publication No. 6,296,805 has been proposed. In the US Patent Publication No. 6,296,805, an aluminum-plated steel sheet is used for hot press forming or room temperature forming, followed by heating and rapid cooling (simply 'post heat treatment'), and since the aluminum plating layer exists on the steel sheet surface, when heating The steel sheet is not oxidized.
[6]
However, in the case of hot press forming of a steel sheet subjected to aluminum plating, there is a problem in that mold wear occurs even though the strength of the material during hot forming is very low at a high temperature. In the process of heating the plated steel sheet for hot forming, the base iron is diffused into the aluminum plating layer to form an alloy layer of hard Fe and Al on the surface of the steel sheet. Because it is higher, it is judged that mold wear is severely caused by press molding. For this reason, when hot press forming the aluminum-plated steel sheet, there is a problem in that the manufacturing cost of the hot-formed member is greatly increased because the mold has to be ground or replaced in a short cycle.
DETAILED DESCRIPTION OF THE INVENTION
technical challenge
[7]
An object of the present invention is to provide a hot-formed member with less wear of a hot-formed mold during hot forming, and a method for manufacturing the same.
[8]
The object of the present invention is not limited to the above. Those of ordinary skill in the art to which the present invention pertains will have no difficulty in understanding the additional problems of the present invention from the general description of the present invention.
means of solving the problem
[9]
One aspect of the present invention is a hot-formed member comprising a steel plate and an aluminum alloy plated layer formed on the base steel plate, wherein the aluminum alloy plated layer is formed on the base steel plate, and Al: 5 to 30% by weight an alloying layer comprising (I); an alloying layer (II) formed on the alloying layer (I) and comprising Al: 30-60% by weight; an alloying layer (III) formed on the alloying layer (II) and comprising Al: 20-50% and Si: 5-20% by weight; and an alloying layer (IV) formed continuously or discontinuously on at least a portion of the surface of the alloying layer (III), and comprising 30 to 60% Al: alloying exposed on the outermost surface of the aluminum alloy plating layer It is a hot-formed member whose proportion of layer (III) is 10% or more.
[10]
A plurality of pores may be formed in the alloying layer (III), and the porosity of the alloying layer (III) may be 5 to 50%.
[11]
The base steel sheet is in wt%, C: 0.04 to 0.5%, Si: 0.01 to 2%, Mn: 0.1 to 5%, P: 0.001 to 0.05%, S: 0.0001 to 0.02%, Al: 0.001 to 1%, N: 0.001 to 0.02%, the balance may include Fe and other impurities.
[12]
The base steel sheet may further include one or more of B: 0.001 to 0.01%, Cr: 0.01 to 1%, and Ti: 0.001 to 0.2% by weight%.
[13]
Another aspect of the present invention is to obtain an aluminum-plated steel sheet by aluminum plating and winding the surface of the steel sheet; annealing the aluminized steel sheet to obtain an aluminum-iron alloy coated steel sheet; and hot press forming the aluminum-iron alloy plated steel sheet; as a method of manufacturing a hot forming member comprising; the aluminum plating amount is 30-200 g/m 2 based on one side of the steel sheet, and up to 250° C. after aluminum plating The cooling rate is 20 ° C / sec or less, the winding tension is 0.5 to 5 kg / mm 2 during winding , and the annealing is carried out for 30 minutes to 50 hours in a heating temperature range of 550 to 750 ° C in an upper annealing furnace, When heating from room temperature to the heating temperature during the annealing, the average temperature increase rate is 10 ~ 100 ℃ / h, but the average temperature increase rate in the 400 ~ 500 ℃ section is 1 ~ 15 ℃ / h, the atmosphere in the upper annealing furnace The difference between the temperature and the steel plate temperature is 5 to 80 ° C. During hot press forming, heat treatment is carried out in the temperature range of Ac3 to 950 ° C, and from 200 ° C to the temperature range from Ac3 to 950 ° C, the temperature is increased at a rate of 3 to 18 ° C. , is a method of manufacturing a hot-formed member that is heat-treated for 1 to 15 minutes for a total heating time and then hot press-formed.
[14]
When the hot forming member is produced 500 times by the method for manufacturing the hot forming member, the 10-point average wear depth of the hot forming mold may be 15 μm or less.
Effects of the Invention
[15]
According to the present invention, in the case of manufacturing a hot forming member, the surface hardness of the plating layer is lower than that of the hot forming die, so that the wear of the die is reduced, so that the grinding or replacement period of the hot forming die can be increased, so that the manufacturing cost and production efficiency of the hot forming member There is an effect that can be improved.
[16]
Various and beneficial advantages and effects of the present invention are not limited to the above, and will be more easily understood in the course of describing specific embodiments of the present invention.
Brief description of the drawing
[17]
1 is a scanning electron microscope photograph of a cross-section of a plating layer of a hot-formed member manufactured according to Invention Example 1. FIG.
[18]
FIG. 2 is a scanning electron microscope photograph of a cross-section of a plating layer of a hot-formed member manufactured according to Comparative Example 1. FIG.
Best mode for carrying out the invention
[19]
Hereinafter, a hot-formed member according to an aspect of the present invention will be described in detail. In the present invention, when expressing the content of each element, it should be noted that, unless otherwise specified, it means weight %. In addition, the ratio of crystals or tissues is based on the area unless otherwise indicated.
[20]
[Hot forming member]
[21]
First, the hot-formed member according to an aspect of the present invention includes a base steel plate and an aluminum alloy plating layer formed on the base steel plate, and the aluminum alloy plating layer is formed on the base steel plate, and Al in weight%: 5 to 30 % alloying layer (I); an alloying layer (II) formed on the alloying layer (I) and comprising Al: 30-60% by weight; an alloying layer (III) formed on the alloying layer (II) and comprising Al: 20-50% and Si: 5-20% by weight; and an alloying layer (IV) formed continuously or discontinuously on at least a portion of the surface of the alloying layer (III), and comprising Al: 30-60%.
[22]
Preferably, each of the alloy layers may have the following component ranges. The alloying layer (I) may include Al: 5-30%, Si: 0-10%, residual Fe and other unavoidable impurities due to alloying in wt%, and the alloying layer (II) is, in wt% As Al: 30-60%, Si: 0-5%, residual Fe and other unavoidable impurities due to alloying, the alloying layer (III) is, by weight, Al: 20-50%, Si: 5-20%, residual Fe and other unavoidable impurities due to alloying, and the alloying layer (IV), by weight percent, is Al: 30-60%, Si: 0-5%, residual Fe and other May contain unavoidable impurities due to alloying
[23]
[24]
When heat treatment is performed after plating aluminum on the base steel sheet, Fe of the base steel sheet is diffused into the aluminum plating layer with a high Al content. In the hot-formed member of the present invention, alloying between Al and Fe is made in the plating layer through annealing treatment for alloying and heat treatment during hot press forming, and a layer composed of alloying layers (I) to (IV) depending on the degree of alloying of Fe structure will be formed.
[25]
The alloying layer (IV) may be continuously or discontinuously formed on at least a portion of the surface of the alloying layer (III). That is, the alloying layer (IV) may be formed on a partial surface of the alloying layer (III) rather than on the entire surface.
[26]
In addition, as the alloying layer (IV) is formed on at least a portion of the surface of the alloying layer (III), a portion of the surface of the alloying layer (III) may be exposed to the outermost surface of the aluminum alloy plating layer. Here, the outermost surface refers to the outermost surface of the aluminum alloy plating layer opposite to the base steel sheet. If the oxide layer is formed on the surface of the aluminum alloy plating layer, it means the uppermost surface of the remaining layers except for the oxide layer.
[27]
At this time, the ratio of the alloying layer (III) exposed on the outermost surface of the aluminum alloy plating layer is preferably 10% or more. Here, the ratio of the alloying layer (III) exposed to the outermost surface may be defined as the ratio of the length of the region where the alloying layer (III) is exposed to the total length of the outermost portion when the cross-section of the alloy plating layer is observed, and in some cases may be defined as the area ratio of the surface area of ​​the alloying layer (III) exposed to the outermost surface to the surface area of ​​the outermost surface of the aluminum alloy plating layer. Among the alloying layers, the hardness of the alloying layer (II) and the alloying layer (IV) is very high at a level of about 900 Hv, whereas the hardness of the alloying layer (I) and the alloying layer (III) is at a level of about 300 to 700 Hv of the alloying layer (II) ) and alloying layer (IV). Therefore, when the exposed area of ​​the alloying layer (III) having a relatively low hardness on the outermost surface of the aluminum alloy plating layer in contact with the mold during hot press forming is increased, the overall average hardness of the outermost surface is lowered, thereby reducing the wear of the mold.
[28]
When the proportion of the alloying layer (III) exposed on the outermost surface is less than 10%, the difference between the outermost surface average hardness and the mold hardness becomes small, and it becomes impossible to effectively suppress the wear of the mold. From the viewpoint of suppression of mold wear, the lower the outermost surface hardness of the aluminum alloy plating layer, the more preferable, so there is no need to separately limit the upper limit of the ratio. Preferably, the ratio may be 15% or more, and in some cases, 20% or more.
[29]
Meanwhile, a plurality of pores may be formed in the alloying layer (III). When an aluminum alloy plated steel sheet is manufactured by alloying an aluminum plated steel sheet under predetermined conditions in an upper annealing furnace, a plurality of alloy layers are formed on the aluminum alloy plated steel sheet, and Fe, Al, Si A plurality of voids are formed in the upper alloy layer due to the difference in the interdiffusion coefficient. At this time, a plurality of pores are formed toward the upper end of the alloy layer, so the porosity is high. When the aluminum alloy plated steel sheet is heated and hot press formed, the uppermost alloy layer having a high density of pores is broken by press forming to form small grains. The lubricity between the mold and the steel plate increases because the rolling friction generated by the rolling of these small grains is smaller than the sliding friction between the steel plate and the mold. Here, the porosity may be defined as a ratio of the pore area to the area of ​​each alloy layer (or alloying layer) when the cross section of the alloy layer (or alloying layer) is observed.
[30]
However, as can be seen in FIG. 1 , since most regions of the alloying layer (IV) are broken by press forming during hot press forming, it is difficult to measure the porosity of the alloying layer (IV) in the hot forming member, The characteristics of the present invention were shown through the porosity of the alloying layer (III), which was slightly affected by press forming and closely related to the porosity of the alloying layer (IV) before press forming.
[31]
Accordingly, the porosity of the alloying layer (III) of the hot-formed member according to an aspect of the present invention may be 5 to 50%. If the porosity is less than 5%, it is difficult to expect a lubricating effect due to a rolling friction effect during hot press forming. On the other hand, if the porosity exceeds 50%, the structure of the alloying layer (III) of the hot-formed member becomes too weak, and there may be a problem in that the mold contamination due to the grains falling from the plating layer in the mold during continuous hot forming becomes severe. Therefore, in the present invention, the porosity is preferably 5 to 50%, and in some cases may be 7 to 50%.
[32]
Meanwhile, the base steel sheet of the present invention is a steel sheet for hot press forming, and its composition is not particularly limited if used for hot press forming. However, according to one aspect of the present invention, in weight%, C: 0.04 to 0.5%, Si: 0.01 to 2%, Mn: 0.1 to 5%, P: 0.001 to 0.05%, S: 0.0001 to 0.02%, Al: 0.001~1%, N: 0.001~0.02%, the balance contains Fe and other impurities. Hereinafter, each component system will be described in detail.
[33]
C: 0.04~0.5%
[34]
The C may be added in an appropriate amount as an essential element in order to increase the strength of the heat treatment member. That is, in order to sufficiently secure the strength of the heat treatment member, 0.04% or more of C may be added. Preferably, the lower limit of the C content may be 0.1% or more. However, if the content is too high, in the case of producing a cold rolled material, when the hot rolled material is cold rolled, the strength of the hot rolled material is too high, so that the cold rolling property is greatly inferior, and the spot weldability is greatly reduced. In order to secure weldability, 0.5% or less may be added. In addition, the C content may be 0.45% or less, and more preferably, the C content may be limited to 0.4% or less.
[35]
Si: 0.01~2%
[36]
The Si not only has to be added as a deoxidizer in steelmaking, but also serves to suppress the formation of carbides, which have the greatest influence on the strength of the hot press-formed member. In the present invention, it may be added in an amount of 0.01% or more in order to secure retained austenite by concentrating carbon at the martensite lath grain boundary after martensite is formed in hot press forming. In addition, the upper limit of the Si content may be set to 2% in order to secure sufficient plating property when aluminum plating is performed on the steel sheet after rolling. Preferably, the Si content may be limited to 1.5% or less.
[37]
Mn: 0.1~5%
[38]
The Mn may be added in an amount of 0.1% or more in order to not only secure a solid solution strengthening effect, but also lower a critical cooling rate for securing martensite in a hot press-formed member. In addition, the Mn content may be limited to 5% or less in terms of securing the workability of the hot press forming process by properly maintaining the strength of the steel sheet, reducing the manufacturing cost, and improving the spot weldability.
[39]
P: 0.001~0.05%
[40]
The P is present as an impurity in the steel, and it is advantageous as the content thereof is as small as possible. Therefore, in the present invention, the P content may be limited to 0.05% or less, preferably limited to 0.03% or less. Since P is an impurity element that is advantageous as it is small, it is not necessary to specifically set an upper limit of its content. However, in order to excessively lower the P content, there is a concern that the manufacturing cost may increase, and in this case, the lower limit may be set to 0.001%.
[41]
S: 0.0001~0.02%
[42]
S is an impurity in steel, and since it is an element that impairs ductility, impact properties and weldability of members, the maximum content is limited to 0.02%, preferably 0.01% or less. In addition, if the minimum content is less than 0.0001%, the manufacturing cost may increase, so the lower limit of the content may be 0.0001%.
[43]
Al: 0.001~1%
[44]
The Al may increase the cleanliness of the steel by deoxidizing it together with Si, and may be added in an amount of 0.001% or more to obtain the above effect. In addition, the Al content may be limited to 1% or less in order to prevent the Ac3 temperature from becoming too high so that heating required for hot press molding can be performed in an appropriate temperature range.
[45]
N: 0.001~0.02%
[46]
The N is an element included as an impurity in steel, and in order to reduce the sensitivity to cracking during continuous casting of the slab, and to secure impact properties, the lower the content, the more advantageous, and thus may be included in 0.02% or less. Although it is necessary to specifically set the lower limit, the N content may be set to 0.001% or more in consideration of the increase in manufacturing cost.
[47]
The aluminum-iron alloy plated steel sheet according to an aspect of the present invention may further include one or more of B: 0.001 to 0.01%, Cr: 0.01 to 1%, and Ti: 0.001 to 0.2% in addition to the alloy composition described above. can
[48]
B: 0.001~0.01%
[49]
B is an element capable of not only improving hardenability even with a small amount of addition, but also segregating at prior austenite grain boundaries to suppress the brittleness of the hot press-formed member due to grain boundary segregation of P and/or S. Therefore, B may be added in an amount of 0.0001% or more. However, if it exceeds 0.01%, the effect is not only saturated, but also causes brittleness in hot rolling, so the upper limit may be set to 0.01%, and preferably, the B content may be 0.005% or less.
[50]
Cr: 0.01~1%
[51]
The Cr is an element added to improve the solid solution strengthening effect and hardenability during hot forming similarly to Mn, and may be added in an amount of 0.01% or more to obtain the above effect. However, in order to secure the weldability of the member, the content may be limited to 1% or less, and if it exceeds 1%, the effect of improving hardenability compared to the amount added is also weak, which is disadvantageous in terms of cost.
[52]
Ti: 0.001~0.2%
[53]
The Ti is effective in increasing the strength of the heat-treated member by forming fine precipitates and improving the collision performance of the member due to grain refinement. . In order to obtain the above effect, Ti may be added in an amount of 0.001% or more. However, since coarse TiN formation caused as the Ti content increases makes the collision performance of the member inferior, the content may be limited to 0.2% or less.
[54]
The remainder other than the above-mentioned components may include iron (Fe) and unavoidable impurities, and additional addition is not particularly limited as long as the components may be included in the steel sheet for hot press forming.
[55]
In the case of manufacturing a hot-formed member having the above-described alloy composition and layer structure, the ratio of the low-hardness alloying layer (III) on the surface of the aluminum alloy plated steel sheet during hot press forming increases to lower the average hardness of the surface, so the hardness The wear of the mold due to the difference can be effectively reduced. In particular, even if the hot forming member is produced 500 times or more, the 10-point average wear depth of the hot forming mold may be 15 μm or less.
[56]
In addition, a plurality of voids are formed in the alloying layers (III) and (IV), which are the upper layers of the aluminum alloy plating layer during hot press forming. It is possible to obtain a lubricating effect by
[57]
[58]
Hereinafter, a method for manufacturing a hot-formed member according to another aspect of the present invention will be described in detail. However, the following method of manufacturing a hot-formed member is only an example, and the hot-formed member of the present invention does not necessarily have to be manufactured by the present manufacturing method, and any manufacturing method is a method that satisfies the claims of the present invention. It should be noted that there is no problem in implementing each embodiment of the invention.
[59]
[Manufacturing method of hot forming member]
[60]
The hot-formed member of the present invention prepares a hot-rolled or cold-rolled base steel sheet, and performs aluminum plating on the surface of the base steel sheet and heat-treats the alloy in an upper annealing furnace to obtain an aluminum alloy-plated steel sheet, and then hot under predetermined conditions It can be obtained by press molding.
[61]
First, preparing a base steel sheet having the above-described alloy composition, aluminum plating on the surface of the base steel sheet under suitable conditions, and winding it to obtain an aluminum plated steel sheet (coil) is performed.
[62]
First , aluminum plating can be performed on the surface of the rolled steel sheet at a coating amount of 30 to 200 g/m 2 on one side . Aluminum plating is usually AlSi plating, which is called type I (contains 80% or more of Al and 5 to 20% of Si, additional elements may be included if necessary), but contains 90% or more of Al called type II and is required Depending on the type of plating, any plating containing additional elements may be used. To form a plating layer, hot-dip aluminum plating may be performed, and an annealing treatment may be performed on the steel sheet before plating. Appropriate coating amount for plating is 30~200g/m 2 based on one side . If the amount of plating is too large, it may take too much time to alloy to the surface. On the contrary, if the amount of plating is too small, it is difficult to obtain sufficient corrosion resistance.
[63]
Next, after aluminum plating, cooling can be performed at a cooling rate of up to 250°C of 20°C/sec or less. The cooling rate after aluminum plating affects the formation of the diffusion suppression layer between the plating layer and the base iron. If the cooling rate after aluminum plating is too fast, the diffusion suppression layer cannot be formed uniformly, so the alloying behavior of the coil during the subsequent annealing treatment is reduced. may become non-uniform. Therefore, the cooling rate up to 250°C after aluminum plating can be 20°C/sec or less.
[64]
When a coil is obtained by winding a steel plate after plating, the winding tension of the coil can be adjusted to 0.5-5 kg/mm 2 . According to the adjustment of the winding tension of the coil, the alloying behavior and surface quality of the coil may be changed during the subsequent annealing treatment.
[65]
[66]
Thereafter, the aluminum-plated steel sheet may be annealed under the following conditions to obtain an aluminum-iron alloy plated steel sheet.
[67]
The aluminum-coated steel sheet (coil) is heated in a batch annealing furnace (BAF). When heating a steel sheet, the target heat treatment temperature and holding time are 30 minutes to 50 minutes within the range of 550 to 750° C. It is desirable to keep time. Here, the holding time is the time from when the coil temperature reaches the target temperature to the start of cooling. If the alloying is not made sufficiently, the plating layer may be peeled off during roll leveling, so the heating temperature may be set to 550° C. or higher for sufficient alloying. In addition, in order to prevent excessive formation of oxides on the surface layer and secure spot weldability, the heating temperature may be 750° C. or less. In addition, in order to sufficiently secure the plating layer and to prevent a decrease in productivity, the holding time may be set to 30 minutes to 50 hours. In some cases, the temperature of the steel sheet may have a heating pattern in which the temperature continues to rise without a cooling process until the heating temperature is reached, and a heating pattern in which the temperature is raised after maintaining the temperature below the target temperature for a certain period of time is applied You may.
[68]
When heating a steel sheet to the above-mentioned heating temperature, in order to ensure sufficient productivity and uniformly alloy the plating layer in the entire steel sheet (coil), the steel sheet (coil) temperature for the entire temperature section (the section from room temperature to the heating temperature) The average temperature increase rate may be 10 to 100° C./h. The overall average temperature increase rate can be controlled within the above numerical range, but in one embodiment of the present invention, the rolling oil remains in the temperature section at which the mixed rolling oil is vaporized during rolling, preventing surface stains, etc., while preventing sufficient productivity In order to secure the temperature, it can be heated at an average temperature increase rate of 1 to 15 °C/h in the 400 to 500 °C section.
[69]
In addition, the difference between the ambient temperature in the upper annealing furnace and the temperature of the steel sheet may be 5 to 80°C. The general heating of the upper annealing furnace takes the method of heating the steel sheet (coil) through an increase in the atmospheric temperature in the annealing furnace rather than the method of directly heating the steel sheet (coil). In this case, the difference between the ambient temperature and the coil temperature is unavoidable, but in order to minimize the variation in material and plating quality for each location in the steel plate, the difference between the ambient temperature and the steel plate temperature should be 80°C or less based on the time the heat treatment target temperature is reached. have. It is ideal to make the temperature difference as small as possible, but it may be difficult to satisfy the overall average temperature increase rate condition by slowing the temperature increase rate. Here, the temperature of the steel plate means measuring the temperature of the bottom (meaning the lowest part of the coil) charged steel plate (coil), and the ambient temperature means the temperature measured at the center of the inner space of the heating furnace. .
[70]
[71]
After manufacturing the aluminum alloy plated steel sheet by the above-described manufacturing method, hot press forming may be performed on the aluminum alloy plated steel sheet to manufacture a hot formed member. In this case, the hot press forming may use a method generally used in the art, and as a non-limiting embodiment, heat treatment at a temperature range of Ac3 to 950°C, but from 200°C to a temperature range of Ac3 to 950°C 3 It can be heated at a temperature increase rate of ˜18° C./s, heat-treated for 1 to 15 minutes as a total heating time, and then hot press-molded. Here, the total heating time may be defined as a heating time including both the heating time in the temperature rising temperature section and the heating time in the temperature range of Ac3 to 950°C.
Modes for carrying out the invention
[72]
Hereinafter, the present invention will be described in more detail through examples. However, it is necessary to note that the following examples are only for exemplifying the present invention and not limiting the scope of the present invention. This is because the scope of the present invention is determined by the matters described in the claims and matters reasonably inferred therefrom.
[73]
(Example)
[74]
First, a cold-rolled steel sheet for hot press forming having the composition shown in Table 1 below was prepared as a base steel sheet, and the surface of the steel sheet was plated with a type I plating bath having a composition of Al-9%Si-1.5%Fe on the surface of the steel sheet. During plating, the plating amount was adjusted to 75 g/m 2 per side , and after cooling the cooling rate to 250° C. at 10° C./sec after aluminum plating, the coiling tension was adjusted to 3 kg/mm 2 and wound to obtain an aluminum-plated steel sheet.
[75]
[Table 1]
element C Si Mn Al P S N Cr Ti B Ac3
content(%) 0.23 0.2 1.25 0.03 0.01 0.002 0.005 0.21 0.034 0.0022 822℃
[76]
Thereafter, the plated steel sheet was subjected to alloying heat treatment in an upper annealing furnace under the conditions shown in Table 2 below, and then subjected to hot press forming 500 times each to obtain a hot formed member. However, in Comparative Example 1, the above-described aluminum plated steel sheet was not subjected to alloying heat treatment, but hot press forming was performed under the conditions shown in Table 2 below to obtain a hot formed member.
[77]
[Table 2]
division alloying heat treatment conditions Hot Press Forming Conditions
Temperature (℃) Average temperature increase rate (℃/h) Average temperature increase rate in 400~500℃ temperature section (℃/h) Temperature difference between atmosphere and steel plate at heating temperature (℃) time (h) Temperature increase rate (℃/s) Temperature (℃) Total heating time (min)
Invention Example 1 630 21 6 25 14 5.8 930 5
Invention Example 2 590 25 10 30 30 8.5 900 6
Invention example 3 680 27 12 25 8 6.2 930 5
Comparative Example 1 - - - - - 3.4 930 5
Comparative Example 2 500 35 20 25 8 4.7 900 6
[78]
Thereafter, for the molds used in each invention example and comparative example, the wear depth was measured at random 10 points after 500 productions, and the average value is shown in Table 3. After taking a sample and observing the cross section with a scanning electron microscope to confirm the occupancy of the outermost layer of the alloying layer (III), the average value of the occupancy is shown together in Table 3 below. In addition, the porosity of the alloying layer (III) was measured, and the results are shown in Table 3 below. In the same embodiment (invention example or comparative example), it was confirmed that the deviation of the occupancy rate and the porosity of the outermost layer of the alloying layer (III) was not large.
[79]
[Table 3]
division Proportion of alloying layer (III) exposed on the outermost surface (%) Average mold wear depth after 500 productions (㎛) Alloying layer (III) porosity (%)
Invention Example 1 35 7 7.2
Invention Example 2 12 9 5.7
Invention example 3 47 4 13.1
Comparative Example 1 7 39 1.7
Comparative Example 2 9 23 3.2
[80]
As can be seen in Table 3 above, in the case of Inventive Examples 1 to 3, in which the area ratio of the alloying layer (III) exposed on the outermost surface is 10% or more and the porosity is 5% or more, hot according to Inventive Examples 1 to 3 Even if the molding member was produced 500 times, it was confirmed that the average wear depth of the mold was 15 μm or less, confirming that the wear of the hot forming mold was effectively suppressed. On the other hand, in Comparative Example 1, a conventional Al-Si plated steel sheet was hot press-formed, and the area ratio of the alloying layer (III) exposed on the outermost surface was less than 10%, and the porosity was low, so that the wear of the mold compared to the invention example. It can be seen that there has been a significant increase in
[81]
In Comparative Example 2, although the alloying heat treatment of the aluminum plating layer was performed, the alloying heat treatment temperature was low, so that sufficient alloying was not achieved. Accordingly, it can be seen that the area ratio of the alloying layer (III) exposed to the outermost surface was less than 10%, and the porosity was low, so that the wear of the mold was greatly increased as in Comparative Example 1.
[82]
Although it has been described with reference to the above embodiments, those skilled in the art will understand that various modifications and changes can be made to the present invention without departing from the spirit and scope of the present invention as set forth in the following claims. will be able
Claims
[Claim 1]
As a hot-formed member comprising a base steel plate and an aluminum alloy plating layer formed on the base steel plate, the aluminum alloy plating layer is formed on the base steel plate, and Al: 5-30% by weight of an alloying layer (I) ); an alloying layer (II) formed on the alloying layer (I) and comprising Al: 30-60% by weight; an alloying layer (III) formed on the alloying layer (II) and comprising Al: 20-50% and Si: 5-20% by weight; and an alloying layer (IV) formed continuously or discontinuously on at least a portion of the surface of the alloying layer (III), and containing 30 to 60% Al: alloying exposed on the outermost surface of the aluminum alloy plating layer A hot-formed member in which the proportion of layer (III) is 10% or more.
[Claim 2]
The hot-formed member according to claim 1, wherein a plurality of pores are formed in the alloying layer (III), and the porosity of the alloying layer (III) is 5 to 50%.
[Claim 3]
The method according to claim 1, wherein the base steel sheet is, by weight, C: 0.04 to 0.5%, Si: 0.01 to 2%, Mn: 0.1 to 5%, P: 0.001 to 0.05%, S: 0.0001 to 0.02%, Al : 0.001 to 1%, N: 0.001 to 0.02%, the remainder Fe and other impurities, characterized in that it contains a hot-formed member.
[Claim 4]
The hot-formed member according to claim 3, wherein the base steel sheet further comprises at least one of 0.001 to 0.01%, Cr: 0.01 to 1%, and Ti: 0.001 to 0.2% by weight%.
[Claim 5]
Obtaining an aluminum-plated steel sheet by aluminum plating and winding the surface of the base steel sheet; annealing the aluminized steel sheet to obtain an aluminum-iron alloy coated steel sheet; and hot press forming the aluminum-iron alloy plated steel sheet; as a method of manufacturing a hot forming member comprising; the aluminum plating amount is 30-200 g/m 2 based on one side of the steel sheet, and up to 250° C. after aluminum plating The cooling rate is 20 ° C / sec or less, the winding tension is 0.5 to 5 kg / mm 2 during winding , and the annealing is carried out for 30 minutes to 50 hours in a heating temperature range of 550 to 750 ° C in an upper annealing furnace, When heating from room temperature to the heating temperature during the annealing, the average temperature increase rate is 10 ~ 100 ℃ / h, but the average temperature increase rate in the 400 ~ 500 ℃ section is 1 ~ 15 ℃ / h, the atmosphere in the upper annealing furnace The difference between the temperature and the steel plate temperature is 5~80℃, and during hot press forming, heat treatment in the temperature range of Ac3~950℃, from 200℃ to the temperature range of Ac3~950℃, at a temperature increase rate of 3~18℃/s A method of manufacturing a hot-formed member by heating, heat-treating for 1 to 15 minutes for a total heating time, and then performing hot press forming.
[Claim 6]
A method of manufacturing a hot-formed member, characterized in that the 10-point average wear depth of the hot-forming mold is 15 μm or less when the hot-formed member is produced 500 times by the method for manufacturing the hot-formed member according to claim 5.