JP5277658B2 - Manufacturing method of hot press member - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a hot-pressed member having excellent edge surface cracking resistance related to a worked edge surface, formed by shearing work and blanking work, such as trimming and piercing applied after hot-pressing. <P>SOLUTION: The hot-pressed member is produced through following steps. A steel sheet, having the chemical compositions composed of 0.15-0.45% C, 0.5-3.0% Mn+Cr, further one or more kinds of &le;0.05% P, &le;0.03% S, &le;0.5% Si, &le;2% Ni, &le;1% Cu, &le;1% V and &le;1% Al and the balance Fe with inevitable impurities, is subjected to the hot-pressing after being held in the temperature zone of Ac<SB>3</SB>point to (Ac<SB>3</SB>point+100&deg;C) for &le;5 min. Successively, the steel sheet is subjected to a quenching treatment for cooling to an Mf point at a cooling rate equal to or higher than an upper part criticality cooling speed, to obtain a tensile strength to &ge;1.2 GPa, then the steel sheet is subjected to the shearing work or the blanking work, and the worked edge surface formed by the above shearing work or the blanking work is subjected to a heat-treatment for holding it in the temperature range of 300-400&deg;C for &le;10 min. <P>COPYRIGHT: (C)2009,JPO&amp;INPIT

Description

  The present invention relates to a method for manufacturing a hot press member that is suitably used for, for example, machine structural parts such as automobile body structural parts and underbody parts.

  In recent years, in order to reduce the weight of automobiles, efforts have been made to increase the strength of steel materials and reduce the weight used. And in the steel plate widely used for a motor vehicle, since press formability falls with the increase in intensity | strength, it has become difficult to manufacture a complicated shape. Specifically, there arises a problem that the ductility is lowered and the rupture occurs at a portion where the degree of processing is high, or the dimensional accuracy is deteriorated due to an increase in springback and wall warpage. Accordingly, it is not easy to produce a formed member by pressing a steel sheet having high strength, particularly a tensile strength of 780 MPa class or higher (hereinafter also referred to as “TS”).

  On the other hand, as shown in Patent Document 1, in a forming method called a hot press method in which a heated steel plate is press-formed, the steel plate is soft and highly ductile at high temperatures during press forming, and thus has a complicated shape. However, it is possible to mold with dimensional accuracy. Furthermore, by increasing the strength of the steel sheet by martensitic transformation, the steel sheet is heated in the austenite region and rapidly cooled (quenched) in the press die.

  Patent Document 2 discloses a pre-press quench method that simultaneously achieves high strength and formability of a steel sheet by forming into a predetermined shape at room temperature and then heating to an austenite region and quenching in a mold. The invention which concerns is disclosed.

Such a hot press method and a pre-press quench method are excellent molding methods that can simultaneously ensure high strength and excellent moldability of the molded member.
By the way, the member manufactured in this way is often subjected to shearing or punching such as trim or piercing. However, when the tensile strength of the member is increased to 1.2 GPa or more, a large residual stress remains on the end surface formed by the shearing process or the punching process, so that the risk of occurrence of delayed fracture increases.

In order to solve such a problem, Patent Document 3 discloses an invention in which a delayed fracture susceptibility is lowered by applying a compressive stress to the end face subjected to the shearing process by a coining process.
British Patent Publication No. 1490535 Japanese Patent Laid-Open No. 10-96031 JP 2006-82099 A

  In the invention disclosed in Patent Document 3, it is necessary to process an end face formed by shearing or punching with high accuracy, and the shape of the end face is complicated or the area of the processed end face is large. Then, since it involves a significant increase in the number of steps, it is difficult to say that this is an efficient method.

  The present invention has been made in view of the problems of such a conventional technique, and is formed by shearing or punching such as trim or piercing performed after hot pressing, and is resistant to end face cracks on a processed end face. It aims at providing the manufacturing method of the hot press member excellent in property.

  As a result of intensive studies to improve the delayed fracture resistance of the end face, the present inventors have significantly improved the delayed fracture resistance of the end face by applying an appropriate heat treatment to a steel sheet having an appropriate chemical composition. It was newly discovered that it will be. The present invention completed based on the new knowledge is as follows.

The present invention contains C: 0.15% or more and 0.45% or less (in this specification, “%” relating to composition means “mass%” unless otherwise specified), and contains Mn . Mn + Cr: containing 0.5% to 3.0% or less, further P: 0.05% or less, S: 0.03% or less, Si: 0.5% or less, Ni: 2% or less, Cu: 1 % or less, V: 1% or less and Al: P is selected from the group consisting of 1% or less, an amount that satisfies S, Si, and contains more than four or five containing Al, further the following equation (1) A steel plate having a chemical composition consisting of the remaining Ti and the balance Fe and impurities is held in a temperature range of Ac ₃ points or more (Ac ₃ points + 100 ° C.) for 5 minutes or less, and then hot pressed, Quenching treatment to cool to Mf point at a cooling rate higher than the critical cooling rate Then, after the tensile strength is set to 1.2 GPa or more, a shearing process or punching process is performed, and a processing end surface formed by the shearing process or the punching process has a temperature range of 300 ° C. to 400 ° C. for 10 minutes or less. A method for producing a hot press member, characterized by performing a heat treatment to be held.
3.42N + 0.001 ≦ Ti ≦ 3.42N + 0.5 (1)
Here, Ti and N in the formula (1) indicate the content (unit: mass%) of each element in the steel.

In the method for producing a hot-pressed member according to the present invention, the chemical composition is replaced with a part of Fe,
(A) B: 0.01% or less,
(B) Nb: 1.0% or less and / or Mo: 1.0% or less , and
(C ) Ca: One or more of 0.005% or less may be contained .

  According to the present invention, it becomes possible to manufacture a hot press member that is formed by shearing or punching such as trim or piercing performed after hot pressing and excellent in end face crack resistance on the processed end face. Therefore, it is possible to reliably provide machine structural parts such as automobile body structural parts and underbody parts.

Next, the best mode for carrying out the present invention will be described.
The reason for limiting the chemical composition and production conditions in the present invention will be described.
(I) Chemical composition In this invention, the chemical composition of the steel plate provided to a hot press is prescribed | regulated as follows.
C: 0.15% or more and 0.45% or less C is a very important element that enhances the hardenability of the steel sheet and mainly determines the strength after quenching. If the C content is less than 0.15%, it is difficult to ensure a TS of 1.2 GPa or more in strength after quenching. Therefore, the C content is 0.15% or more. Preferably it is 0.20% or more. On the other hand, if the C content exceeds 0.45%, the strength after quenching becomes too high, and the deterioration of toughness becomes remarkable. Therefore, the C content is set to 0.45% or less. Preferably it is 0.33% or less.
Mn + Cr: 0.5% or more and 3.0% or less Mn and Cr are elements that are very effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching. However, if the total content of Mn and Cr (hereinafter also referred to as “(Mn + Cr) content”) is less than 0.5%, this effect is not sufficient, while the (Mn + Cr) content is 3.0%. If it exceeds, the effect will be saturated, and it will be difficult to secure a stable strength. Therefore, the (Mn + Cr) content is 0.5% or more and 3.0% or less. Preferably, the (Mn + Cr) content is 0.8% or more and 2.0% or less.
P: 0.05% or less, S: 0.03% or less, Si: 0.5% or less, Ni: 2% or less, Cu: 1% or less, V: 1% or less, and Al: 1% or less Or these 2 or more types of elements are elements which are effective in improving the hardenability of a steel plate and ensuring the intensity | strength after quenching stably. However, since the effect is small even if it contains more than an upper limit, and it causes a cost increase unnecessarily, the content of each element is set to the above-described range.

Furthermore, in the present invention, the steel sheet to be subjected to hot pressing contains Ti and may contain B, Nb, Mo , and Ca as optional additional elements, and these will also be described.
B: 0.01% or less B is effective for enhancing the hardenability of the steel sheet and further enhancing the effect of stably securing the strength after quenching. It is also an important element in that it segregates at grain boundaries to increase grain boundary strength and improve toughness. Furthermore, the effect of suppressing the grain growth of austenite at the time of heating at the time of subjecting to hot pressing is also high, and it has the effect of improving toughness due to this. Therefore, in the present invention, it is preferable to contain B as an optional additive element. However, if the B content exceeds 0.01%, the above effect is saturated, leading to an increase in cost. Therefore, when it contains B, the content shall be 0.01% or less.

Preferably it is 0.0030% or less. In order to obtain the above effect more reliably, the B content is preferably 0.0001% or more, and more preferably 0.0010% or more.
Nb: 1.0% or less, Mo: 1.0% or less Both Nb and Mo form fine carbides, and when the steel sheet used for hot pressing is heated to Ac ₃ points or more, the austenite grains are coarse It has the effect of greatly improving toughness in order to keep it fine. Furthermore, since Nb has a strong action of suppressing recrystallization, the above effect is even greater. Therefore, in the present invention, it is preferable to contain Nb and / or Mo as optional additional elements. However, when the content of any element exceeds 1.0%, the effect is saturated, and the cost is unnecessarily increased. Therefore, when Nb and / or Mo are contained, each content is made 1.0% or less.

The Nb content is preferably 0.15% or less, and more preferably 0.10% or less. The Mo content is preferably 0.20% or less, and more preferably 0.15% or less. In order to obtain the above effect more reliably, the Nb content is preferably 0.02% or more, and more preferably 0.04% or more. Further, the Mo content is preferably 0.01% or more, and more preferably 0.04% or more.
3.42N + 0.001 ≦ Ti ≦ 3.42N + 0.5
Since Ti forms fine carbides and suppresses recrystallization, it suppresses the coarsening of austenite grains and keeps them fine when heating a steel sheet to be subjected to hot pressing to Ac ₃ points or more. Has the effect of greatly improving Therefore, containing T i in the present invention.

In order to reliably obtain such an effect, the Ti content is preferably set to (3.42N + 0.001) or more. On the other hand, when the Ti content exceeds (3.42N + 0.5), the effect is saturated and the cost is unnecessarily increased. A more desirable Ti content is 3.42N + 0.02 ≦ Ti ≦ 3.42N + 0.08.
Ca: 0.005% or less Ca has an effect of making inclusions in steel finer and improving toughness after quenching. Therefore, in the present invention, it is preferable to contain Ca as an optional additive element.

  However, when the Ca content exceeds 0.005%, the effect is saturated and the cost is increased. Therefore, the Ca content is 0.005% or less. Preferably it is 0.004% or less. In order to reliably obtain the above effects, the Ca content is preferably 0.001% or more, and more preferably 0.002% or more.

The balance other than those described above is Fe and impurities.
(Ii) Manufacturing conditions (hot press)
The steel plate having the above-described chemical composition is held in a temperature range of Ac ₃ points or more (Ac ₃ points + 100 ° C.) for 5 minutes or less and then hot pressed.

When the holding temperature of the steel sheet to be subjected to hot pressing is less than Ac ₃ points, it does not become an austenite single phase, so that it is difficult to obtain a strength of 1.2 GPa or more even if a subsequent quenching treatment is performed. On the other hand, when the holding temperature of the steel sheet to be subjected to hot pressing exceeds (Ac ₃ points + 100 ° C.), the austenite grains become coarse and the toughness deteriorates remarkably or the scale loss increases remarkably. Therefore, the holding temperature of the steel sheet subjected to hot pressing is set to Ac ₃ points or higher (Ac ₃ points + 100 ° C.).

Further, the holding time of the steel sheet to be subjected to hot pressing in this temperature range is set to 5 minutes or less in order to prevent the cost required for heating from being increased unnecessarily. The lower limit of the holding time is not particularly required, but is preferably 1 minute or more from the viewpoint of homogenizing the structure before quenching and stabilizing the product characteristics.
(Quenching process)
The steel material subjected to hot pressing is subjected to a quenching process for cooling to the Mf point at a cooling rate equal to or higher than the upper critical cooling rate.

  If the cooling rate in the quenching process is lower than the upper coastal cooling rate or the cooling end temperature is higher than the Mf point, a substantial amount of phases and structures other than martensite exceeding the level of inevitably mixed are generated. , It may be difficult to ensure a strength of 1.2 GPa or more. Therefore, the quenching process is performed under the conditions described above.

In addition, about the steel plate of this invention, it is enough if the cooling rate in a hardening process shall be 60 degrees C / sec or more. Moreover, it is sufficient that the cooling end temperature in the quenching process is 100 ° C.
(Shearing and punching)
The hot-pressed member after quenching is subjected to a shearing process or a punching process, and the shearing process or the punching process may be performed by a conventional method and is not particularly limited.
(Heat treatment)
The hot press member on which the processed end face is formed by shearing or punching is subjected to heat treatment for holding the processed end face in a temperature range of 300 ° C. to 400 ° C. for 10 minutes or less. This heat treatment reduces the tensile residual stress existing on the processed end face and improves delayed fracture resistance.

  When the holding temperature in the heat treatment is less than 300 ° C., the effect of reducing the tensile residual stress existing on the processed end face may not be sufficiently obtained. On the other hand, when the temperature exceeds 400 ° C., the strength of the hot pressed member may be significantly reduced. Accordingly, the holding temperature in the heat treatment is set to be 300 ° C. or higher and 400 ° C. or lower. Preferably they are 300 degreeC or more and 350 degrees C or less.

  Furthermore, if the holding time in this heat treatment exceeds 10 minutes, the strength of the hot pressed member may be significantly reduced. Therefore, the holding time in the heat treatment is 10 minutes or less. Preferably it is 5 minutes or less. Since the reduction of the tensile residual stress existing on the processed end face proceeds rapidly by heat treatment, the lower limit of the holding time is not particularly limited, but is usually 10 seconds or more in actual work.

  In addition, the part which heat-processes may be the whole hot press member in which the process end surface by the shearing process or the punching process was formed, and may be only a process end surface. Any method may be used as the heating method for performing the heat treatment, but in the case of heating only the processing end face, for example, laser heating, high-frequency heating, or heating by a gas burner is exemplified. Moreover, in the case of heating the whole hot press member, for example, furnace heating, high-frequency heating, electric heating or the like is exemplified.

The steel plate according to the present invention is subjected to a hot press that is press-formed after being held at a temperature of Ac ₃ points or higher. Therefore, the mechanical properties at room temperature are not important, and there is no need to specify the metal structure before being subjected to hot pressing. Therefore, the steel plate according to the present invention may be either a hot-rolled steel plate or a cold-rolled steel plate, and the surface of the steel plate may be plated. Moreover, it is not necessary to specifically limit the manufacturing method.

  According to the present embodiment described above, it is possible to manufacture a hot press member having excellent end face crack resistance with respect to a processed end face formed by shearing or punching such as trim or piercing performed after hot pressing. Therefore, for example, it is possible to reliably provide machine structural parts such as automobile body structural parts and undercarriage parts.

Furthermore, the present invention will be described more specifically with reference to examples.
Steel type No. shown in Table 1 A steel plate (plate thickness: 1.6 mm) having a chemical composition of 1 to 7 was used as a test material.

  These steel plates were heated at 1250 ° C. for 30 minutes and then hot-rolled at 900 ° C. or higher to obtain a steel plate having a thickness of 4 mm. After hot rolling, after water spray cooling to 600 ° C., it was charged into a furnace, held at 600 ° C. for 30 minutes, and then gradually cooled to room temperature at 20 ° C./hour to simulate a hot rolling winding process. . The obtained hot-rolled sheet was removed from the scale by pickling, and then cold-rolled to a thickness of 1.6 mm.

The cold-rolled steel sheet manufactured in this way is cut into dimensions of 1.6 t × 50 w × 150 L (mm), heated in the atmospheric heating furnace under the conditions shown in Table 2, and taken out from the heating furnace. Immediately thereafter, hot pressing was performed using a flat steel mold. In addition, the “holding time” in Table 1 refers to the time from when the Ac ₃ point is reached after charging into the furnace to when it is removed from the furnace. Moreover, the cooling rate of the quenching treatment by hot pressing was 60 ° C./second or more, and the cooling end temperature was 100 ° C. or less.

  Then, after leaving for one week, shearing cutting | disconnection was performed to the dimension of 1.6tx50wx10L. The cut specimen was heat-treated under the conditions shown in Table 2, and then immersed in a hydrochloric acid aqueous solution having a pH of 1 and a temperature of 30 ° C. After 50 hours, the cut end face was examined to check for cracks.

  Example No. which is an example of the present invention. In Nos. 1 to 7, no cracks were present on the cut end face. On the other hand, Example No. which is a comparative example. 8 and Example No. In No. 9, since the heat treatment temperature and the heat treatment holding time specified in the present invention were not satisfied, a crack was generated on the cut end surface by shearing cutting.

Claims (4)

C: 0.15 to 0.45% in mass%, Mn, Mn + Cr: 0.5 to 3.0%, P: 0.05% or less, S: 0.0. P, S, Si, and Al selected from the group consisting of 03% or less, Si: 0.5% or less, Ni: 2% or less, Cu: 1% or less, V: 1% or less, and Al: 1% or less A steel sheet containing 4 or 5 or more kinds of Ti, further containing Ti in an amount satisfying the following formula (1), and having a chemical composition consisting of the remaining Fe and impurities is Ac ₃ points or more (Ac ₃ points + 100 ° C. ) After holding for 5 minutes or less in the following temperature range, perform hot pressing, and then quenching to Mf point at a cooling rate higher than the upper critical cooling rate to obtain a tensile strength of 1.2 GPa or higher Are subjected to shearing or punching, and the shearing or punching The processed end face formed by punching, the manufacturing method of hot pressing member, characterized in that a heat treatment of holding at a temperature region of 300 ° C. or higher 400 ° C. or less than 10 minutes.
3.42N + 0.001 ≦ Ti ≦ 3.42N + 0.5 (1)
Here, Ti and N in the formula (1) indicate the content (unit: mass%) of each element in the steel.   The method for producing a hot-pressed member according to claim 1, wherein the chemical composition contains B: 0.01% or less in mass% instead of part of Fe.   The chemical composition contains Nb: 1.0% or less and / or Mo: 1.0% or less in terms of mass% instead of a part of Fe. The manufacturing method of the hot press member of description. The hot press member according to any one of claims 1 to 3 , wherein the chemical composition contains Ca: 0.005% or less in mass% instead of part of Fe. Manufacturing method.