KR100711445B1 - A method for manu- facturing alloyed hot dip galvanized steel sheet for hot press forming having excellent plating adhesion and impact property, the method for manufacturing hot press parts made of it - Google Patents

Abstract

A method for producing an alloyed hot-dip galvanized steel sheet for hot forming, which is mainly used as a structural member or reinforcing material of an automobile body, and has excellent plating adhesion and impact characteristics, and a method for manufacturing hot formed parts using the steel sheet is provided.

The manufacturing method of this steel sheet is weight%, C: 0.1-0.5%, Si: 0.01-1.0%, Mn: 2.0-4.0%, P: 0.1% or less, S: 0.03% or less, soluble Al: 0.1% or less, Steel slabs composed of N: 0.01 to 0.1%, W: 0.1% or less, remaining Fe and other unavoidable impurities are reheated at 1100 to 1300 ° C, and hot finish rolling is finished at Ar ₃ transformation point or more and 1000 ° C or less, and then 500 Winding at ~ 750 ℃, pickling and cold rolling, then hot dip galvanizing for 10 seconds or less in the temperature range of 450 ~ 470 ℃, cooled to room temperature and then heat treatment alloying for 30 seconds or less in the temperature range of 440 ~ 580 ℃ Is done.

According to the present invention, a method for producing an alloyed hot-dip galvanized steel sheet for hot forming processing having excellent plating adhesion, ultrahigh strength of 1470 MPa or more after hot forming, and yield strength change of 100 MPa or more after coating, and a method of manufacturing hot formed parts using the steel sheet Can be provided.

 Automobile structural member, reinforcement, plating adhesion, alloyed hot dip galvanized steel sheet, impact characteristics

Description

A method for manu- facturing alloyed hot dip galvanized steel sheet for hot press forming having excellent plating adhesion and impact property, the method for manufacturing hot press parts made of it}

Korean Unexamined Patent Publication No. 2005-0062194

Korean Unexamined Patent Publication No. 2003-0049731

Japanese Laid-Open Patent Publication 2005-126733

The present invention relates to a method for producing a steel sheet mainly used as a structural member or reinforcement of an automobile body. More specifically, the method for producing a hot-dip alloyed hot-dip galvanized steel sheet having excellent plating adhesion, ultra-high strength of 1470 MPa or more after hot forming, and yield strength change of 100 MPa or more after coating, and a method of manufacturing hot formed parts using the steel sheet It is about.

Recently, as safety regulations of automobile passengers have spread, research on lightweighting the vehicle body and high strength steel plate accordingly has been conducted to improve impact resistance of the vehicle body. However, increasing the strength of automotive steel sheets has a problem of significantly lowering the formability of steel sheets.

In order to solve such a problem, a method of manufacturing a high strength steel sheet having excellent formability is proposed in Korean Unexamined Patent Publication No. 2005-0062194. The prior art is a transformation induced plasma (TRIP) steel sheet using the martensite transformation of the retained austenite, it is possible to manufacture a steel sheet excellent in formability of 980MPa class tensile strength. However, in order to secure more strength, elements such as C and Mn must be added, and thus, manufacturing cost problems occur, and shape freezing inferiority due to high strength and mold damage due to high strength when forming ultra high strength steel sheet A manufacturing problem occurs.

Conventional techniques for improving such a problem include Korean Laid-Open Patent Publication No. 2003-0049731 and Japanese Laid-open Patent Publication 2005-126733. In Korean Patent Laid-Open Publication No. 2003-0049731 of the prior arts, after performing heat treatment and press molding in an austenitic single phase region using low strength and high workability before heat treatment, ultra-high strength in a final product is performed by rapid cooling by a mold. Provided is a method for producing a cold rolled steel sheet. In addition, Japanese Patent Laid-Open No. 2005-126733 discloses a hot press steel sheet having excellent high temperature workability by adding Mo and Nb alone or in combination.

However, the prior arts focus on improving tensile strength after hot forming, and have technical limitations on the method of securing impact characteristics by increasing yield strength after coating.

The present invention is to improve the above-mentioned conventional problems, by performing hot forming at a relatively low temperature to secure excellent plating adhesion, processing into a product of a complex shape and then quenching to secure high tensile strength after coating heat treatment The present invention provides a method for producing an alloyed hot-dip galvanized steel sheet for hot forming which has a high yield strength increase and secures excellent impact characteristics, and a method for producing a hot formed part using the steel sheet.

The present invention for achieving the above object, in weight%, C: 0.1-0.5%, Si: 0.01-1.0%, Mn: 2.0-4.0%, P: 0.1% or less, S: 0.03% or less, soluble Al : 0.1% or less, N: 0.01% to 0.1%, W: 0.1% or less, steel slab composed of remaining Fe and other unavoidable impurities is reheated at 1100 to 1300 ° C, hot rolled at an Ar ₃ transformation point or more and 1000 ° C or less. After finishing, wound at 500 ~ 750 ℃, pickling and cold rolling, and then hot dip galvanized for 10 seconds or less in the temperature range of 450 ~ 470 ℃, cooled to room temperature and then in the temperature range of 440 ~ 580 ℃ The present invention relates to a method for producing an alloyed hot-dip galvanized steel sheet for hot forming, which has excellent plating adhesion and impact characteristics, which is subjected to alloying heat treatment in 30 seconds or less.

In addition, the present invention is heated to a temperature of 1 ~ 100 ℃ / sec to 700 ~ 850 ℃ temperature range of the alloyed hot-dip galvanized steel sheet prepared by the above method and maintained for 10 to 1000 seconds after hot forming 10 ~ 500 ℃ / The present invention relates to a method for manufacturing a hot formed part having excellent plating adhesion and impact characteristics which are rapidly cooled at a high speed.

EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated in detail.

In the present invention, the term 'hot formed part' refers to a workpiece obtained by processing a steel plate in a certain form, and includes all parts applied to applications in which the physical properties of the steel of the present invention can be used.

The inventors of the present invention, while studying a method for securing the impact characteristics of the hot-formed steel sheet, it was found that the yield strength can be sharply increased after the addition of N properly. In other words, in the manufacture of hot-formed parts, by adding carbon appropriately and securing 80% or more martensite structure in the quenching process after processing, by adding N appropriately to the steel plate which greatly improved the strength, the yield strength after coating is increased to increase the impact characteristics. This excellent steel sheet can be secured.

In addition, the present invention is characterized in that excellent plating adhesion can be ensured by performing Zn plating on the surface of the steel sheet and performing hot forming at a relatively low temperature. That is, in order to secure sufficient corrosion resistance after hot forming, Zn plating is performed in the present invention. However, when hot forming at a high temperature, the Zn plating layer has a problem in that the plating adhesion is degraded and sufficient corrosion resistance of the steel sheet is not obtained. In order to solve this problem, while maintaining sufficient strength even at low temperature hot forming, it is of importance to manufacture a steel sheet excellent in plating adhesion.

In addition, the present invention may further add Mo, Cr, B and the like to improve the hardenability to further increase the high strength through rapid cooling after processing into a product of a complex shape at a relatively low temperature. First, the composition range of the steel component of the present invention will be described.

C: 0.1 to 0.5% is preferable.

The C is an essential element for increasing the strength of the steel sheet. In order to generate hard phases such as austenite and martensite, and to obtain a strength of 1470 MPa or more, the C content should be added at least 0.1%. If the content is less than 0.1%, it is difficult to secure the target strength even if heat treatment is performed in the austenitic single phase region. In addition, if the content exceeds 0.5%, the likelihood of deterioration of toughness and weldability increases, making it difficult to weld the steel sheet in the pickling and rolling process of the hot rolled steel sheet, and significantly increasing the strength of the steel sheet in the annealing and plating processes. This may cause serious problems in the manufacturing process, such as poor mailing performance. Therefore, the content of C is preferably limited to 0.1 to 0.5%.

Si: 0.01 to 1.0% is preferable.

Si contributes to the increase in strength of the steel sheet as a solid solution strengthening element. If the content is less than 0.01%, it is difficult to remove the surface scale (scale) of the hot-rolled steel sheet, but if it exceeds 1.0%, there is a problem of increasing the manufacturing cost, it is preferable to limit the content to 0.01 ~ 1.0%.

Mn: 2.0 to 4.0% is preferable.

Mn not only contributes greatly to the strength increase as a solid solution element, but also plays an important role in delaying the transformation of austenite to ferrite. In addition, as an element useful for lowering the Ac 3 temperature, in order to improve the plating adhesion, which is very important in the present invention, the hot forming temperature must be lowered. Therefore, it is preferable to add Mn content of 2.0% or more. If the content is less than 2.0%, the steel sheet is difficult to heat-treat in the austenitic single-phase zone, and thus it is difficult to secure the target strength in the present invention. However, if the content exceeds 4.0%, problems such as weldability and hot rolling are caused. It is preferable to limit the content to 2.0 to 4.0%.

P: 0.1% or less is preferable.

The P shows the effect of strengthening the steel, but is preferably limited to 0.1% or less because the workability may be degraded by the addition of excess P.

S: 0.03% or less is preferable.

Since S is a high impurity element in steel, it is highly desirable to limit the ductility and weldability of the steel sheet to 0.03% or less.

Soluble Al: 0.1% or less is preferable.

The soluble Al is an element added for deoxidation of steel. When the content exceeds 0.1%, the effect is not only saturated, but there is a problem in that the yield strength is suppressed due to the decrease of the solid solution N by forming AlN by forming excessive inclusions such as Al ₂ O ₃ . Therefore, the content of the soluble Al is preferably limited to 0.1% or less.

N: 0.01 to 0.1% is preferable.

N is a very important component in the present invention. N is a solid solution strengthening element and combines with Ti, Nb, Al and the like to form nitride to increase yield strength. In addition, in the present invention, sufficient N is added to increase the yield strength after coating, which causes N to remain as solid solution N in the crystal grains before coating, thereby increasing the yield point by preventing the transfer of dislocation after coating, thereby rapidly increasing the yield strength. It acts as a major factor. When the content of N is less than 0.01%, it is difficult to expect such an effect. When the content of N is more than 0.1%, it is difficult to dissolve and play the steel sheet, as well as problems in manufacturing processes such as workability degradation or blow hole during welding. May result. Therefore, the content of N is preferably limited to 0.01 ~ 0.1%. Preferably the content of N is 0.011% to 0.1%. More preferably, the content of N is 0.02 to 0.1%.

W: 0.1% or less is preferable.

W is an element which improves the heat treatment hardenability of the steel sheet, and is a very important element in the present invention because the W-containing precipitate acts advantageously to secure the strength. When the content of W exceeds 0.1%, not only this effect is saturated, but there is a problem in that the manufacturing cost increases. Therefore, the content of W is preferably limited to 0.1% or less.

In addition to the steel formed as described above, at least one member selected from Mo and Cr as the hardenability enhancing element, at least one member selected from Ti and Nb as the precipitation enhancing element and at least one member selected from Cu and Ni as the strength enhancement element And B may be added.

At least one selected from Mo and Cr: 0.01 to 1.5% is preferable.

The Mo and Cr not only increases the hardenability but also increases the toughness of the heat-treated steel sheet, so that the effect of Mo and Cr is very high when added to a steel sheet characterized by high impact energy absorption. In addition, since the hardenability is improved, the strength reduction of the portion not directly contacting the mold during high temperature molding processing can be prevented. If the content of Mo or Cr is less than 0.01%, sufficient hardenability cannot be obtained. Even if the amount of the addition is continuously increased, the hardenability does not increase significantly. Therefore, it is preferable to limit the amount to 1.5% because it greatly increases the manufacturing cost required for steel sheet production. Do.

1 or more types chosen from Ti and Nb: 0.001 to 0.1% is preferable.

The Ti and Nb are elements that improve the strength of the steel sheet, refine the grain size and improve the heat treatment characteristics. If the content of Ti and Nb is less than 0.001%, such an effect cannot be secured. If the content exceeds 0.1%, the production cost is increased and the target strength and yield strength is secured due to excessive carbon and nitride production. it's difficult. Therefore, it is preferable to limit the content to 0.001 to 0.1%.

At least one selected from Cu: 0.005 to 1.0% or Ni: 0.005 to 2.0% is preferred.

The Cu is an element that produces fine Cu precipitates to improve strength. When the content of Cu is less than 0.005%, sufficient strength cannot be obtained, and when the content of Cu is more than 1.0%, it is accompanied by processing deterioration. Therefore, the content is preferably limited to 0.005 to 1.0%.

Ni is an element that improves strength and heat treatment characteristics. If the content of Ni is less than 0.005%, the effect is hardly exhibited. If the content of Ni is more than 2.0%, an increase in manufacturing cost and deterioration of workability may occur. Therefore, the content is preferably limited to 0.005 to 2.0%.

B: 0.0001 to 0.01% is preferable

B is an element having a very high hardenability, and even if a small amount is added, high strength can be ensured in the heat-treated steel. If the content of B is less than 0.0001%, sufficient hardenability cannot be obtained, and even if the amount thereof is continuously increased, the hardenability does not increase significantly, resulting in deterioration of hot workability.

The present invention is composed of Fe and other unavoidable impurities in addition to the above components.

Hereinafter, the manufacturing method of the alloying hot-dip galvanized steel sheet which has the steel comprised as mentioned above is demonstrated in detail.

First, the steel slab formed as described above is reheated at 1100 ~ 1300 ℃. When the reheating temperature is less than 1100 ° C, the tissue uniformity and re-use of Ti, Nb, etc. are not sufficient, and when the reheating temperature exceeds 1300 ° C, the steel sheet structure is easily coarsened, and manufacturing problems are likely to occur. Therefore, the reheating temperature is preferably limited to 1100 ~ 1300 ℃.

Thereafter, hot finish rolling is terminated at an Ar ₃ transformation point or more and 1000 ° C. or less. Below the hot finish rolling temperature Ar ₃ transformation point, hot deformation resistance is likely to increase sharply and manufacturing problems may occur, and if it exceeds 1000 ° C., too thick oxidation scale may occur and steel sheet may be coarsened. Therefore, the hot finishing rolling temperature is preferably limited to more than Ar ₃ transformation point to less than 1000 ℃.

Subsequently, the hot rolled steel sheet is wound at 500 to 750 ° C. When the coiling temperature is less than 500 ℃ excessive martensite or bainite is produced to cause an excessive increase in strength of the hot rolled steel sheet may cause a manufacturing problem such as a shape defect due to the load during cold rolling. On the other hand, if it exceeds 750 ℃ excessive precipitates such as Ti, Nb, Mo becomes coarse, it is preferable to limit the winding temperature to 500 ~ 750 ℃.

Thereafter, the wound hot rolled sheet is pickled and cold rolled at a reduction ratio of 30 to 80%. If the cold reduction rate is less than 30%, the target thickness is difficult to secure and the shape correction of the steel sheet is difficult, while if the cold reduction rate exceeds 80%, there is a high possibility of cracking at the edge of the steel sheet, and cold rolling There is a problem that brings load. Therefore, the cold reduction rate is preferably limited to 30 to 80%.

In the present invention, the cold rolled steel sheet may be continuously annealed at a temperature range of 750 to 900 ° C. before hot forming. If the annealing temperature is less than 750 ℃ tends to not secure sufficient processability, if the temperature exceeds 900 ℃ is likely to increase the manufacturing cost and surface quality deterioration.

Subsequently, hot dip galvanizing is performed on the cold rolled steel sheet or the continuously cold-rolled cold rolled steel sheet in a temperature range of 450 to 470 ° C. for 10 seconds or less. When the hot dip galvanizing temperature is less than 450 ℃ zinc plating is insufficient, when the hot dip galvanizing excessively exceeds 470 ℃, the hot dip galvanizing temperature range is preferably limited to 450 ~ 470 ℃.

In addition, since the zinc plating becomes excessive when the hot dip galvanizing time exceeds 10 seconds, the hot dip galvanizing time is preferably limited to 10 seconds or less.

After the hot dip galvanizing, it is cooled to room temperature and alloyed heat treatment for 30 seconds or less in the temperature range of 440 ~ 580 ℃ to form a galvanized alloy plating layer. The alloying heat treatment is for alloying the hot dip galvanizing layer in the hot dip galvanizing step, the alloying heat treatment temperature is less than 440 ℃ alloying unstable, the alloying heat treatment temperature is 440 ~ 580 ℃ even if it exceeds 580 ℃ It is desirable to limit to 580 ° C.

In addition, when the alloying heat treatment time exceeds 30 seconds, the alloying is excessive, it is preferable to limit the alloying heat treatment time to 30 seconds or less.

Hereinafter, the microstructure of the hot formed part which heat-treated the steel plate for hot forming process is demonstrated.

The steel formed as described above may be given a desired physical property by managing the microstructure through a suitable heat treatment as a hot formed part. In the present invention, the hot formed part has a fraction of martensite of 80% or more. If the martensite fraction is less than 80%, it is because the high tensile strength targeted in the present invention cannot be secured. A more preferable range for showing the effect of the present invention is that the fraction of martensite is 90% or more. In addition, in the present invention, the hot formed parts may be coated to secure yield strength change rate (ΔYS) of 100 MPa or more.

Hereinafter, the manufacturing method of the hot formed part which has the steel and a structure | tissue which were formed as mentioned above is demonstrated in detail.

The alloyed hot-dip galvanized steel sheet produced as described above was heated at a rate of 1 to 100 ° C./sec in a temperature range of 700 to 850 ° C. and maintained at 10 to 1000 sec, after hot forming in a mold, followed by 10 to 500 ° C./sec. Quench at speed. If the heat treatment temperature is less than 700 ℃ sufficient austenite is not produced, so that sufficient martensite is not produced after hot forming, it is difficult to secure the target strength. On the other hand, when the temperature exceeds 850 ° C., it is difficult to obtain member toughness and clean shape due to oxidation of the steel sheet surface and coarsening of austenite, as well as Zn plating adhesion is inhibited, which lowers the corrosion resistance of the steel sheet. It is preferable to limit to 700-850 degreeC.

In addition, when the temperature increase rate is less than 1 ° C / sec, the manufacturing efficiency tends to fall, and when it exceeds 100 ° C / sec, excessive manufacturing equipment is required. In addition, when the heat treatment time is less than 10 seconds, the austenite transformation is not sufficient, while when the heat treatment time exceeds 1000 seconds, an increase in manufacturing cost and coarsening of austenite are likely to occur.

In addition, when the cooling rate is less than 10 ° C / sec, it is difficult to obtain a structure composed of martensite as a main phase, and thus it is difficult to secure the target strength. On the other hand, when it exceeds 500 ° C / sec, it is preferable to limit the manufacturing cost to 10 to 500 ° C / sec because the manufacturing cost increases due to excessive manufacturing equipment investment and the strength does not increase significantly. The hot formed part has a characteristic that the yield strength change rate increases by 100 MPa or more during the baking process after coating.

Hereinafter, the present invention will be described in more detail with reference to Examples.

EXAMPLE

The steel slab formed as shown in Table 1 was vacuum-dissolved, heated in a reheating temperature of 1150 ~ 1250 ° C for 1 hour in a heating furnace and wound up after hot rolling. At this time, the hot rolling was finished hot rolling in the temperature range of 850 ~ 950 ℃, the winding temperature was set to 650 ℃. Pickling was performed using a hot rolled steel sheet and cold rolling was performed at a cold rolling reduction of 50%. The cold rolled steel sheet was annealed at 800 ° C. and then subjected to continuous annealing with an overage temperature of 400 ° C.

Thereafter, after hot-dip galvanizing for 5 seconds by heating to 460 ℃, after the alloying treatment for 10 seconds at 500 ℃ for alloying of the plating layer, and cooled to room temperature to produce an alloyed hot-dip galvanized steel sheet. Subsequently, the plated steel sheet manufactured as described above was heated at a rate of 10 ° C./sec under the heat treatment temperature conditions as shown in Table 2 and heated for 5 minutes, and then transferred to a mold to process the heated steel sheet. And quenched at the rate of 80 ° C./sec concurrently with processing.

And after the end of the processing was cut to the portion that can be cut tensile specimens to prepare a JIS No. 5 tensile test piece. The adhesion of the Zn plated layer and the steel sheet was observed through the optical microscope at the 90 degree bending hot forming site. In addition, in order to simulate the material after the coating in the structural member for automobiles, the tensile test prepared above was boiled in oil at 170 ° C. for 20 minutes and then subjected to a tensile test.

Table 2 shows the structure and mechanical properties after hot forming processing of the inventive steel and comparative steel.

Steel grade Chemical composition C Si Mn P S Al N W B Etc Inventive Steel A 0.22 0.27 2.37 0.012 0.002 0.042 0.016 0.05 0.0006 Ti: 0.023, Cr: 0.02 Inventive Steel B 0.24 0.15 2.16 0.011 0.005 0.036 0.012 0.03 0.0010 Nb: 0.015, Mo: 0.05 Invention Steel C 0.23 0.13 2.26 0.015 0.004 0.052 0.020 0.07 0.0022 Cu: 0.05, Ni: 0.05 Comparative Steel D 0.23 0.26 1.02 0.012 0.002 0.02 0.005 - 0.0020 Cr: 0.05, Mo: 0.05 Comparative Steel E 0.07 0.133 2.98 0.012 0.002 0.016 0.004 - 0.0017 Ti: 0.01, Cr: 1.01

Steel grade Heat treatment temperature Tissue after hot forming process  YS (MPa)  TS (MPa)  El (%)  DYS (MPa)  Plating adhesion  Remarks Martensite fraction (%) Other organizations A 750 96 ferrite 951 1568 6.5 124 O Invention 1 A 800 99 Bainite 1172 1651 7.9 189 O Invention 2 B 750 94 ferrite 923 1532 7.2 103 O Invention 3 B 800 98 Bainite 1156 1621 7.4 135 O Invention 4 C 750 95 ferrite 947 1575 6.9 134 O Invention 5 C 800 99 Bainite 1185 1673 7.5 152 O Invention 6 A 900 97 Bainite 1127 1587 7.4 116 X Comparative Material 1 B 900 97 Bainite 1136 1578 7.3 121 X Comparative Material 2 C 900 98 Bainite 1167 1598 7.4 146 X Comparative Material 3 D 800 86 ferrite 806 1337 4.8 30 △ Comparative Material 4 D 900 96 Bainite 1017 1506 7.6 55 X Comparative Material 5 E 800 75 ferrite 947 1150 6.8 81 △ Comparative Material 6 E 900 78 ferrite 950 1185 7.3 22 X Comparative Material7 (1) O: excellent, △: inferior, X: poor

As shown in Table 1 and 2, in the case of the invention material (1 ~ 6) that satisfies the component range and manufacturing conditions of the present invention exhibits an ultra high strength of 1470 MPa or more in the final product. In addition, the change in yield strength after 20 minutes coating simulation at 170 ℃ can be used as a structural member and reinforcement of the vehicle body excellent in impact characteristics as the invention materials (1-6) all increase to 100MPa or more. And excellent plating adhesion was also shown.

However, the comparative materials (1 to 3, 5, and 7) which did not satisfy the hot forming heat treatment conditions of the present invention exhibited poor plating adhesion by performing hot forming at high temperature.

In addition, in the case of the comparative material 4 prepared using the comparative strength D in which the content of Mn and N is outside the range limited by the present invention, not only the fraction of the target martensite is secured, but also the tensile strength and the yield strength increase are increased. Shortage. In the case of Comparative Material 5 manufactured using Comparative Steel D, the strength was secured by heat treatment at high temperature, but the plating adhesion was inferior.

In addition, in the case of the comparative material 6,7 manufactured by using the comparative steel E whose contents of C and N are outside the range limited by the present invention, the addition amount of carbon is low, so that the martensite structure is sufficiently secured after heat treatment and mold processing. As a result, high tensile strength could not be secured in the final product, and the yield strength was insufficient due to the low nitrogen content.

As described above, according to the present invention, the alloyed hot-dip galvanized steel sheet can secure excellent plating adhesion while securing strength of 1470 MPa or more even at low temperature hot forming. In addition, there is an effect that can provide a hot forming steel sheet for excellent impact characteristics due to the rise in yield strength of 100MPa or more after coating.

Claims (13)

By weight%, C: 0.1-0.5%, Si: 0.01-1.0%, Mn: 2.0-4.0%, P: 0.1% or less, S: 0.03% or less, soluble Al: 0.1% or less, N: 0.01-0.1% , W: 0.1% or less, B: a re-heating 0.0001 ~ 0.01%, and balance of Fe and other steel slab which is the composition as inevitable impurities at 1100 ~ 1300 ℃ and ends the hot finish rolling at below 1000 ℃ more than Ar ₃ transformation point, and then, Winding at 500 ~ 750 ℃, pickling and cold rolling to obtain cold rolled steel sheet, hot dip galvanizing for 10 seconds or less at 450 ~ 470 ℃ temperature range, cooling to room temperature, and then 30 at 440 ~ 580 ℃ temperature range. A method for producing an alloyed hot-dip galvanized steel sheet for hot forming, which has excellent plating adhesion and impact characteristics, which is subjected to alloying heat treatment in seconds or less. The method for manufacturing an alloyed hot dip galvanized steel sheet having excellent plating adhesion and impact characteristics according to claim 1, wherein 0.01 to 1.5% of Mo or Cr is added to the steel slab. The method of claim 1, wherein at least one of Ti or Nb is added in an amount of 0.001 to 0.1% to the steel slab. The method of claim 1, wherein at least one of Cu: 0.005 ~ 1.0%, Ni: 0.005 ~ 2.0% is added to the steel slab of the alloy hot-dip galvanized hot-dip galvanized steel sheet having excellent plating adhesion and impact characteristics. Manufacturing method. delete The method of claim 1, wherein the cold rolled steel sheet is continuously annealed at a temperature of 750 to 900 ° C. 3. By weight%, C: 0.1-0.5%, Si: 0.01-1.0%, Mn: 2.0-4.0%, P: 0.1% or less, S: 0.03% or less, soluble Al: 0.1% or less, N: 0.01-0.1% , W: 0.1% or less, B: a re-heating 0.0001 ~ 0.01%, and balance of Fe and other steel slab which is the composition as inevitable impurities at 1100 ~ 1300 ℃ and ends the hot finish rolling at below 1000 ℃ more than Ar ₃ transformation point, and then, Winding at 500 ~ 750 ℃, pickling and cold rolling to obtain cold rolled steel sheet, hot dip galvanizing for 10 seconds or less at 450 ~ 470 ℃ temperature range, cooling to room temperature, and then 30 at 440 ~ 580 ℃ temperature range. The alloyed hot-dip galvanized steel sheet obtained by performing the alloying heat treatment under ultra-high temperature was heated at a speed of 1 to 100 ° C./second in the temperature range of 700 to 850 ° C. and maintained at 10 to 1000 seconds for hot forming, followed by a speed of 10 to 500 ° C./second. Manufacturing method of hot formed parts with excellent quenching adhesion and impact characteristics. [8] The method for manufacturing hot formed parts having excellent plating adhesion and impact characteristics according to claim 7, wherein at least one of Mo or Cr is added to the steel slab. [8] The method of claim 7, wherein the steel slab is added with 0.001 to 0.1% of at least one of Ti or Nb. The method of manufacturing a hot formed component having excellent plating adhesion and impact characteristics according to claim 7, wherein at least one of Cu: 0.005 to 1.0% and Ni: 0.005 to 2.0% is added to the steel slab. delete 8. The method of claim 7, wherein the hot formed part has a martensite structure fraction of at least 80%. The method of claim 7, wherein the cold rolled steel sheet is continuously annealed at a temperature of 750 ° C. to 900 ° C. 9.