JP5641298B2 - Manufacturing method of steel for plastic molding dies - Google Patents

Description

  The present invention relates to a method for producing pre-hardened steel for plastic molding dies used for plastic molded products.

  Conventionally, pre-hardened steel is known as a mold material used for a plastic mold. Pre-hardened steel is tempered to a predetermined hardness and can be processed and used by mold users without heat treatment. Therefore, the productivity of die machining can be increased accordingly.

  Therefore, for example, in Patent Document 1, a plastic mold material having a predetermined component composition is quenched (970 ° C.) and tempered (600 to 610 ° C.) so as to have a hardness of 30 to 32 HRC. Good results have been obtained with respect to sex.

  Patent Document 2 discloses that a steel having a predetermined composition is heated at 970 ° C. for 30 minutes, and then cooled to 600 ° C. at a cooling rate of 2.5 ° C./min. Quenching conditions are disclosed. This quenching condition simulates the cooling condition in order to study the amount of C, Cr and Mn from the viewpoint of hardenability.

JP 2002-88442 A JP-A-3-177536

By the way, in recent years, there has been an increasing opportunity for plastic molded articles to become larger, such as automotive headlamp lenses that are becoming more modular and integrated. As plastic moldings become larger, the molds that mold them inevitably become larger. For this reason, when heat treatment conditions that have been conventionally performed are applied particularly to large dies, warping and twisting occur after cutting and electric discharge machining, and the dimensional accuracy of the dies cannot be maintained.

  In addition, the above-mentioned plastic mold material for lenses of relatively large automobiles and the like is required to have particularly excellent specularity without pinholes or fine pits.

This invention is made | formed in view of the above problems, and the subject which this invention tends to solve is improving the mirror surface property of a metal mold | die, maintaining the dimensional accuracy of the metal mold | die after heat processing.

As a result of intensive studies, the present inventors have found that this problem can be solved. The specific means is as follows. First, the first invention is mass%,
C: 0.20% to 0.30%,
Si: 0.25% to 0.35%,
Mn: 1.00% to 2.00%
P: 0.015% or less,
Cu: 0.25% or less,
Ni: 0.25% or less,
Cr: 2.00% to 2.50%,
Mo: 0.25% to 0.45%,
V: 0.05% to 0.20%,
Al: 0.030% or less,
O: 0.0100% or less, and
N: 0.02% or less,
Containing the steel material, the balance being Fe and inevitable impurities, at a quenching temperature above the austenite transformation point,
A first quenching step for cooling from the quenching temperature to 500 ° C at a cooling rate of 1.0 to 5 ° C / min, and a second quenching for cooling from 500 ° C to 200 ° C at a cooling rate of 2.5 to 10 ° C / min. A step and a tempering step of tempering the steel material at 500 to 600 ° C.,
The cooling rate of the second quenching step is higher than the cooling rate of the first quenching step, and Rzmax when polished to # 5000 abrasive grains is 0.0550 μm or less (based on JIS B 0633) This is a manufacturing method of pre-hardened steel for plastic molds.

Next, the second invention is a method for producing the pre-hardened steel for plastic molding dies according to the first invention described above, in mass%,
S: 0.001% to 0.20%,
Se: 0.001% to 0.3%,
Te: 0.001% to 0.3%,
Ca: 0.0002% to 0.10%,
Pb: 0.001% to 0.20%, and
Bi: One or more selected from 0.001% to 0.30% are contained.

Next, the third invention is a method for producing the pre-hardened steel for plastic molding dies according to the first invention or the second invention described above, in mass%,
Ta: 0.001% to 0.30%,
Ti: 0.20% or less, and
Zr: One type or two or more types selected from 0.001% to 0.30% are contained.

  When the steel material having the composition according to the present invention is quenched and tempered, the dimensions of the mold processed after the heat treatment are subject to internal strain (residual stress) due to repeated shrinkage and expansion inside the steel material, and are likely to change. . The occurrence of residual stress is thought to be due to the non-uniform temperatures of the surface portion of the steel material having a high cooling rate and the central portion of the steel material having a low cooling rate. On the other hand, if the cooling rate is extremely slow in order to eliminate uneven temperature, the structure in the steel material is not quenched well (not martensite or bainite), which is necessary as a mold. Hardness cannot be obtained. Further, if the cooling rate is slow, it is not economically preferable. Therefore, in the present invention, in order to obtain the necessary hardness as a mold without causing a dimensional change of the mold processed after the heat treatment, the quenching process is divided into two steps, and the first quenching is performed first. In the process, the cooling rate is slowed so that the temperature difference between the surface portion and the central portion of the steel material does not become uneven. In the second quenching step to be performed next, the required hardness can be obtained by increasing the cooling rate, that is, faster than the cooling rate of the first quenching step. Thereby, in this invention, the mirror surface property of a metal mold | die can be improved, maintaining the dimensional accuracy of the metal mold | die processed after heat processing.

  Here, when one or more selected from the specific amounts of S, Se, Te, Ca, Pb, and Bi are contained, machinability is improved while suppressing a decrease in toughness. Can be made. Therefore, it can contribute to the improvement of mold workability.

  In addition, when one or more selected from the specific amounts of Ta, Ti, and Zr are contained, it becomes easier to form carbonitrides by combining with C and N, and the crystal grains are coarse. Is suppressed. In addition, machinability is hardly deteriorated. Therefore, it can contribute to improving the mirror surface property and workability of the mold.

It is a figure which shows the chemical composition of invention steel and comparative steel. It is a figure which shows the heat processing conditions of invention steel and comparative steel. It is a figure which shows the test result of invention steel and a comparison steel.

  Below, the manufacturing method of the prehardened steel for plastic molding dies (henceforth "this prehardened steel") which concerns on one Embodiment of this invention is demonstrated in detail. Applications of this pre-hardened steel include daily miscellaneous goods, exterior / interior / parts for home appliances, exterior / interior / parts for OA equipment, exteriors for mobile phones, interior and exterior parts for automobiles and motorcycles, and structural members thereof. Can be mentioned. In the present invention, it is preferable to apply to a large mold (practically a mold of 40 kg or more) when molding a lens for a headlamp of a large automobile or the like.

The pre-hardened steel according to the present invention contains the following elements. The kind of additive element, its component range, and the reason for limitation are as follows. In addition, the unit of a component ratio is the mass%.

C: 0.20% to 0.30%
C is an element necessary for ensuring strength and wear resistance. C combines with carbide-forming elements such as Cr, Mo, W, and V to form carbides. C is also necessary for securing hardness by forming a martensite structure by solid solution in the matrix during quenching. In order to obtain the effect, the lower limit of the C content is 0.20%. The lower limit of the C content is preferably 0.23%. When the C content is excessive, the carbide forming element and C are combined to form coarse carbides, and the impact value is lowered. Therefore, the upper limit of the C content is set to 0.30%.

Si: 0.25% to 0.35%
Si is mainly added as a deoxidizer or an element that improves the machinability at the time of mold production. In order to obtain the effect, the lower limit of the Si content is 0.25%. On the other hand, the thermal conductivity decreases due to the addition of Si. Further, the hardness of the quenched and tempered steel is determined by the secondary hardening by the hardness after quenching and the distribution of precipitated carbides. Therefore, it is necessary to obtain sufficient hardness after quenching. When the Si content becomes excessive, Si dissolves in the matrix, and precipitation of other carbides is promoted, the position of the pearlite nose in the CCT diagram moves to the short time side, and the start temperature of the bainite transformation increases. In particular, the hardness of the center of a large mold that slows down cooling is reduced. From these viewpoints, the upper limit of the Si content is 0.35%.

Mn: 1.00% to 2.00%
Mn is added to improve hardenability and stabilize austenite. In order to obtain the effect, the lower limit of the Mn content is 1.00%. When the Mn content is excessive, hot workability is reduced. Therefore, the upper limit of the Mn content is 2.00%.

P: 0.015% or less P is inevitably contained in steel. P segregates at the grain boundaries and causes toughness to decrease. Therefore, the upper limit of the P content is 0.015%.

Cu: 0.25% or less Cu is an element that stabilizes austenite. However, when Cu content becomes excessive, hot workability will fall. From the viewpoint of preventing this, the upper limit of the Cu content is set to 0.25%.

Ni: 0.25% or less Ni is an element that stabilizes austenite. However, when the Ni content is excessive, the annealing property is lowered and it is difficult to adjust the hardness. Therefore, the upper limit of Ni content is 0.25%.

Cr: 2.00% to 2.50%
Cr is an element that improves the corrosion resistance. In order to obtain the effect, the lower limit of the Cr content is 2.00%. When the Cr content is excessive, the thermal conductivity is greatly reduced. From the viewpoint of preventing this, the upper limit of the Cr content is 2.50%.

Mo: 0.25% to 0.45%
Mo is an element that shifts the pearlite nose in the CCT diagram to the long time side. In order to obtain the effect, the lower limit of the Mo content is set to 0.25%. However, the Mo addition effect is gradually saturated. Therefore, the upper limit of the Mo content is 0.45%.

V: 0.05% to 0.20%
V combines with C to form a carbide. This carbide contributes to suppression of coarsening of the crystal grain size. In order to obtain the effect, the lower limit of the V content is set to 0.05%. When the V content is excessive, V carbide crystallizes and grows, so that the carbide particle size increases and the specularity decreases. From the viewpoint of preventing this, the upper limit of the V content is 0.20%.

Al: 0.030% or less Al is an element added as a deoxidizer. However, when the Al content is excessive, it combines with O to form a coarse oxide, and the specularity deteriorates. Therefore, the upper limit of the Al content is 0.030%.

O: 0.0100% or less O is an element inevitably contained in molten steel. However, when O becomes excessive, it combines with Si and Al to produce a coarse oxide, which becomes inclusions, and deteriorates toughness and specularity. From the viewpoint of preventing this, the upper limit of the O content is 0.0100%.

N: 0.02% or less N is an interstitial element and contributes to an increase in the hardness of the martensite structure. Γ stabilization ability is stronger than carbon of the same interstitial element. However, if the N content is excessive, the nitrogen gas ejection limit is exceeded due to the concentration of nitrogen during solidification, and voids are likely to occur in the ingot. Therefore, the upper limit of the N content is 0.02%.

The present prehardened steel may optionally contain one or more elements selected from the following elements in addition to the essential elements described above. The component ratio of each element, reasons for limitation, etc. are as follows.

S: 0.001% to 0.20%, Se: 0.001% to 0.3%, Te: 0.001% to 0.3%, Ca: 0.0002% to 0.10%, Pb: 0.001% to 0.20%, Bi: 0.001% to 0.30%
S, Se, Te, Ca, Pb, and Bi can all be added to improve machinability. In order to obtain the effect, the lower limit of the S content is 0.001%. Similarly, the lower limit of the Se content is 0.001%. The lower limit of the Te content is 0.001%. The lower limit of the Ca content is 0.0002%. The lower limit of the Pb content is 0.001%. The lower limit of the Bi content is 0.001%.

When the contents of S, Se, Te, Ca, Pb, and Bi are excessive, the toughness is reduced. From the viewpoint of preventing this, the upper limit of the S content is 0.20%, more preferably 0.050%. Similarly, the upper limit of the Se content is set to 0.3%. The upper limit of the Te content is set to 0.3%. The upper limit of the Ca content is 0.10%. The upper limit of the Pb content is 0.20%. The upper limit of Bi content is 0.30%.

Ta: 0.001% to 0.30%, Ti: 0.20% or less, Zr: 0.001% to 0.30%
Ta, Ti, and Zr are elements that are effective for combining with C and N to form carbonitrides and suppressing the coarsening of crystal grains to improve the specularity. In order to obtain the effect, the lower limit of the Ta content is set to 0.001%. Similarly, the lower limit of the Zr content is 0.001%. In addition, the minimum of Ti content is not specifically limited.

When each content of Ta, Ti, and Zr is excessive, machinability is deteriorated. From the viewpoint of preventing this, the upper limit of the Ta content is set to 0.30%. Similarly, the upper limit of the Ti content is 0.20%. The upper limit of the Zr content is 0.30%.

Moreover, it is preferable that the hardness (Rockwell hardness) of this prehardened steel is tempered within the range of 36-42 HRC. This is because when the hardness is less than 36 HRC, the hardness is insufficient, the surface roughness increases, and the mirror polishability decreases. On the other hand, if the hardness exceeds 42 HRC, it becomes too hard, and mold workability such as drilling with a high-speed drill or the like deteriorates.

[First quenching process]
The first quenching step is a step of cooling the steel material having the above-described composition at a quenching temperature not lower than the austenite transformation point and then cooling from the quenching temperature to 500 ° C at 1 to 5 ° C / min. As the quenching temperature, an appropriate temperature is selected according to the composition of the steel material. Usually, it is austenite transformation point + 30-50 degreeC. Here, 1 to 5 ° C./min refers to the average cooling rate from the quenching temperature to 500 ° C. In general, the higher the cooling rate, the easier the martensitic transformation and bainite transformation proceed. For this reason, if the cooling rate after quenching is fast, the temperature distribution of the steel material becomes worse, particularly in the case of a large mold. That is, variation occurs between the surface temperature of the steel material and the center temperature. As a result, the transformation does not occur uniformly in the steel material, and the part that has been transformed later is constrained and distorted. Therefore, the cooling rate from the quenching temperature to 500 ° C. is set to 5 ° C./min or less. On the other hand, when the cooling rate is slow, a pearlite structure is formed, and a material having a uniform structure cannot be obtained. Therefore, the cooling rate from the quenching temperature to 500 ° C. is set to 1 ° C./min or more. Here, the reason why the temperature is set to 500 ° C. is that the temperature is just above the martensitic transformation and bainite transformation start temperature.

[Second quenching process]
The second quenching step is a step of cooling the steel material having the composition quenched in the first quenching step described above from 500 ° C. to 200 ° C. at 2.5 to 10 ° C./min. Here, 2.5 to 10 ° C./min refers to an average cooling rate from 500 ° C. to 200 ° C. Since the martensite structure contains a large amount of strain, it is preferable to obtain a bainite structure by avoiding rapid cooling in order to prevent distortion. Therefore, the cooling rate from 500 ° C. to 200 ° C. is set to 10 ° C./min or less. On the other hand, if the cooling rate is slow, the hardness after quenching decreases and sufficient hardness cannot be obtained. Therefore, the cooling rate from 500 ° C. to 200 ° C. is set to 2.5 ° C./min or more. Here, the reason why the temperature is up to 200 ° C. is that the martensite and bainite transformation is sufficiently completed.

In the present invention, the cooling rate of the second quenching step is larger than the cooling rate of the first quenching step. The reason for this is to make it possible to eliminate the uneven temperature in the steel material and to obtain a sufficient mold hardness by the quenched structure.

[Tempering process]
The generation of the residual stress may be caused by factors such as plastic working and temperature variation during transformation, but can be eliminated by maintaining at an appropriate tempering temperature. That is, when tempering at a low temperature of about 200 ° C. or 300 ° C., the amount of reduction in residual stress is reduced. On the other hand, when tempering at a high temperature of about 700 ° C. or 800 ° C., sufficient hardness cannot be obtained due to excessive dullness, or austenite transformation occurs and re-quenching occurs. Therefore, in this invention, a tempering process is performed at 500-600 degreeC.

Hereinafter, the contents of the present invention will be described more specifically using examples.
A steel having a chemical composition (mass%) shown in FIG. 1 was melted in a vacuum induction furnace, and then a 500 kg ingot was cast. The ingot after casting was hot forged to produce a bar having a cross section of 250 × 60 mm square. Test pieces according to various tests were cut out from the bar material, and after heat treatment, a hardness test, a specularity test, and a deformation test were performed. FIG. 2 shows the heat treatment conditions for the inventive steel and the comparative steel.

Under the heat treatment conditions, the cooling rate was measured by opening a hole to the center of a dummy test piece having the same size as the test piece used in the deformation test and inserting a thermocouple. Specifically, a thermocouple was inserted into the center of the test piece, and the temperature history in the quenching process was sampled.

[Hardness test]
A 15 mm × 15 mm × 15 mm dice test piece was cut out from the bar, polished to # 400 after heat treatment, and measured with a Rockwell hardness tester.

[Specularity test]
A plate of 50 mm × 45 mm × 12 mm was processed from the bar, and after heat treatment, it was polished to # 5000 abrasive grains by mechanical polishing to prepare a test piece. And about the grinding | polishing surface of the said test piece, surface roughness Rzmax was measured based on JISB0633 and it was set as mirror surface evaluation. In this test, it was determined that a test piece having an Rzmax of 0.0550 or less was excellent in specularity.

[Deformation test]
A 250 mm × 60 mm × 400 mm block (46.8 kg) was processed from the bar, and after heat treatment, a 5 × 60 × 15 mm rectangle was cut out by wire cutting, and the amount of deformation was measured. More specifically, FIG. 3 shows the amount of warpage (μm / 60 mm) of the surface in the longitudinal direction as the deformation amount. In this test, it was judged that the amount of deformation was small if it was 2.5 μm or less.

FIG. 3 shows the test results of the inventive steel and the comparative steel. Comparison of FIGS. 1 to 3 reveals the following.
That is, in the comparative steel 1, the Mo content is below the lower limit of the specified range of the present invention. For this reason, pearlite is expected to be generated, the hardness is low, and it is difficult to ensure specularity.

In the comparative steel 2, the Cr content is below the lower limit of the specified range of the present invention. For this reason, the hardness is low and it is difficult to ensure the specularity.

In comparative steel 3, the cooling rate in the first quenching step is below the lower limit of the specified range of the present invention. For this reason, pearlite is expected to be generated, the hardness is low, and it is difficult to ensure specularity.

In comparative steel 4, the cooling rate in the second quenching step is lower than the lower limit of the specified range of the present invention. Therefore, the hardness after quenching decreases and sufficient hardness cannot be obtained, and it is difficult to ensure the specularity.

In the comparative steel 5, the tempering temperature in the tempering step is lower than the lower limit of the specified range of the present invention. As a result, the amount of reduction in residual stress due to tempering is reduced, resulting in significant deformation after processing.

In the comparative steel 6, the cooling rate in the second quenching process is not greater than the cooling rate in the first quenching process. Therefore, it is impossible to achieve both the elimination of non-uniform temperature in the steel material and the obtaining of sufficient mold hardness by the martensite structure, and as a result, sufficient hardness cannot be obtained. The specularity was not good.

In contrast to these comparative steels, it can be seen that all of the inventive steels ensure the mirror surface property of the mold while maintaining the dimensional accuracy of the mold after the heat treatment.

From the above results, it is confirmed that according to the manufacturing method of the present invention, it is possible to obtain a plastic molding die that can be molded with high productivity even if it is a relatively large (40 kg or more) plastic molded product. did it.

Heretofore, the embodiments and examples of the present invention have been described. The present invention is not particularly limited to these embodiments and examples, and various modifications can be made.

Claims (3)

% By mass
C: 0.20% to 0.30%,
Si: 0.25% to 0.35%,
Mn: 1.00% to 2.00%
P: 0.015% or less,
Cu: 0.25% or less,
Ni: 0.25% or less,
Cr: 2.00% to 2.50%,
Mo: 0.25% to 0.45%,
V: 0.05% to 0.20%,
Al: 0.030% or less,
O: 0.0100% or less, and
N: 0.02% or less,
Containing the steel material, the balance being Fe and inevitable impurities, at a quenching temperature above the austenite transformation point,
A first quenching step for cooling from the quenching temperature to 500 ° C at a cooling rate of 1.0 to 5 ° C / min, and a second quenching for cooling from 500 ° C to 200 ° C at a cooling rate of 2.5 to 10 ° C / min. A step and a tempering step of tempering the steel material at 500 to 600 ° C.,
The cooling rate of the second quenching step is higher than the cooling rate of the first quenching step, and Rzmax when polished to # 5000 abrasive grains is 0.0550 μm or less (based on JIS B 0633) become manufacturing method for a plastic molding die for pre-hardened steel. % By mass
S: 0.001% to 0.20%,
Se: 0.001% to 0.3%,
Te: 0.001% to 0.3%,
Ca: 0.0002% to 0.10%,
Pb: 0.001% to 0.20%, and
Bi: One type or two or more types selected from 0.001% to 0.30% are contained, The manufacturing method of the prehardened steel for plastic molds of Claim 1 characterized by the above-mentioned. % By mass
Ta: 0.001% to 0.30%,
Ti: 0.20% or less, and
Zr: 1 type, or 2 or more types selected from 0.001%-0.30% are contained, The manufacturing method of the prehardened steel for plastic molding dies of Claim 1 or 2 characterized by the above-mentioned.

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