KR100960088B1 - Plastic die steels with superior uniformity hardness distribution and machinability - Google Patents
Plastic die steels with superior uniformity hardness distribution and machinability Download PDFInfo
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract
The present invention is a plastic mold steel excellent in uniform hardness and workability, the weight% of C: 0.25 to 0.35%, Si: 0.10 to 0.35%, Mn: 0.65 to 0.84%, Cu: 0.30% or less, Ni: 0.20 to 0.50% , Cr: 1.00 ~ 1.50%, Mo: 0.20 ~ 0.45%, V: 0.03 ~ 0.12%, Al: 0.020 ~ 0.050%, B: 0.0008 ~ 0.0050%, Zr: 0.0050 ~ 0.0500%, P: 0.020% or less, S : 0.020% or less, N: 0.0100% or less, O: 0.0020% or less and H: 0.00020% or less, the balance includes Fe and impurities inevitably mixed during steelmaking, and temper softening resistance during quenching tempering heat treatment Any relation T SR =
Description
BACKGROUND OF THE
The metal mold | die used at the time of manufacturing the product which has a special shape is an indispensable processing tool in shape | molding materials, such as a metal and plastics. In general, plastic mold steel used for molding plastics was initially used as a simple mold for producing general-purpose sundries or cosmetic containers using mainly carbon steel. Plastic products are molded by injection molding which presses the heated resin into the mold. Recently, in accordance with the advancement of the industrial economy, plastic products are used not only for automobiles and home appliances, but also for optical devices such as office equipment and lenses requiring beautiful gloss and high gloss. Until now, it is used for manufacture of the high precision product which has a comparatively complicated shape.
For this reason, the following characteristics are calculated | required by the plastic mold steel used for it. First of all, it should have less porosity, have a clean and homogeneous structure, and the characteristics required for manufacturing molds include welding repairability for sticking due to variation in processing, and streaks caused by spray or film corrosion during corrosion processing. It should be excellent in specular processability, etc., and resins and plastics sprayed in the molten state have high temperature stability (at room temperature / high temperature) as they are required for injection that can withstand the repeated stress generated by repeated heating and cooling while contacting the mold material. Strength characteristics, impact resistance, wear resistance, etc.) should be excellent.
Conventional plastic mold steels include medium carbon SCMs such as JIS SCM440 and AISI P20. Mn, Cr, Ni, Mo, etc. are added to meet the properties required for resin and plastic injection. In order to improve the workability and improve the processability, Ca, Te, Ti, Zr, Ce, Nb, V, La, Pb, Bi, Se and the like are added to spheroidize or complex compound non-metallic inclusions such as oxides and sulfides, In order to improve the machinability, mirror surface workability and corrosion processability by reducing the cutting resistance, the patent related technologies disclosed in JIS SUM system and US Patents 3973950, 4115111, and Korean Patents 36172, 79360 and the like.
In addition, Korean Patent 10-0263426 adds a small amount of boron (B), nitrogen (N) and a small amount of aluminum (Al) to existing steel grades and secures the grain boundary segregation boron by buffering three elements to improve the hardenability. There is a patented technology that can reduce the internal and external hardness deviation due to the mass effect, which is a problem of large mold materials, as well as allow homogenization of the tissue, thereby reducing the economic loss that is repaired and discarded during the final mold production.
However, the above conventional technology alone cannot satisfy the characteristics required for mold production. It is necessary to control the shape of the sulfide-based (MnS) non-metallic inclusion formed by S, which is inevitably added to improve workability as well as to have a uniform hardness. Therefore, there is a need for a mold steel suitable for a large mold material that can be secured at the same time to secure uniform hardness and improve workability through optimal alloy design.
In order to solve the problems of the prior art as described above, the present invention is to secure the internal and external uniform hardness to meet the requirements of the mold steel used for office automation equipment, radiator grill, TV housing and automobile bumper, and improve the workability Provide plastic mold steel that can be made.
More specifically, by designing an alloy by optimally combining the composition of Mn content and the relationship between B, N and Al in the alloy component of the conventionally developed steel grade, internal and external uniform hardness can be ensured, and sulfide-based nonmetals Zr is added for the purpose of inclusion distribution and shape control to form Zr-based oxides and nitrides, which are effective for improving workability, to provide nucleation sites for MnS inclusions, and to provide fine and even distribution to improve workability. It is an object of the present invention to provide an optimization technique capable of satisfying the characteristics required for mold making such as optimum alloy design, hot deformation and heat treatment.
In addition, the present invention, in the manufacture of plastic mold steel, by establishing a specific relationship relating to tempering softening resistance during quenching tempering heat treatment, the tempering softening resistance and high temperature stability of the mold during plastic molding (at room temperature / high temperature strength, impact resistance, wear resistance) It is another object of the present invention to provide a plastic mold steel that can secure the.
The object of the present invention as described above is by weight% C: 0.25 to 0.35%, Si: 0.10 to 0.35%, Mn: 0.65 to 0.84%, Cu: 0.30% or less, Ni: 0.20 to 0.50%, Cr: 1.00 to 1.50 %, Mo: 0.20 ~ 0.45%, V: 0.03 ~ 0.12%, Al: 0.020 ~ 0.050%, B: 0.0008 ~ 0.0050%, Zr: 0.0050 ~ 0.0500%, P: 0.020% or less, S: 0.020% or less, N : 0.0100% or less, O: 0.0020% or less, H: 0.00020% or less, and the balance includes Fe and impurities which are inevitably mixed during steelmaking It is achieved by plastic mold steel with excellent uniform hardness and workability.
Preferably, the plastic mold steel is T SR =
Still another object of the present invention is to melt the plastic mold steel and then cast an ingot through a refining and vacuum degassing process; First upsetting the cast ingot by heating at 1200 ° C. to 1250 ° C .; Reheating the first upset ingot at 1200 ° C. to 1250 ° C. for second upsetting; And free forging the second upset ingot.
Preferably, the step of performing a hydrogen diffusion heat treatment at 550 ℃ ~ 650 ℃ after the free forging step; Hardening heat treatment at 850 ° C to 950 ° C; And it is characterized in that it further comprises the step of heat treatment at 550 ℃ ~ 650 ℃.
According to the plastic mold steel of the present invention, the steel of the present invention, by adjusting the Mn content and alloy design by optimally combining B, N and Al, it is possible to increase the precision to have a uniform hardness inside and outside the mold, sulfide-based non-metallic inclusions Zr is added for the purpose of distribution and shape control to form Zr-based oxides and nitrides, which are effective for improving workability, to provide nucleation sites of MnS inclusions, and to have fine and even distribution, thereby improving workability and machinability. The optimum alloy design of the steel can be achieved to achieve the same effect.
In addition, in the method of manufacturing the plastic mold steel of the present invention, the tempering softening resistance and the high temperature stability (normal temperature / high temperature strength, impact resistance) of the mold during plastic molding by satisfying the specific relation of the present invention related to tempering softening resistance during quenching tempering heat treatment. , Wear resistance) can be obtained.
The present invention is a method of manufacturing a plastic mold steel having excellent uniformity and workability, in weight% C: 0.25-0.35%, Si: 0.10-0.35%, Mn: 0.65-0.84%, P: 0.020% or less, S: 0.020% Cu: 0.30% or less, Ni: 0.20 to 0.50%, Cr: 1.00 to 1.50%, Mo: 0.20 to 0.45%, V: 0.03 to 0.12%, Al: 0.020 to 0.050%, B: 0.0008 to 0.0050%, Zr: 0.0050 ~ 0.0500%, N: 0.0100% or less, O: 0.0020% or less, H: 0.00020% or less, consisting of the remaining Fe and impurities inevitable in steelmaking, and at the same time related to tempering softening resistance during quenching tempering heat treatment Any relation T SR =
The present invention by the above configuration was performed to the optimum alloy design by adding Ni, Cr, Mo, and a small amount of B, V in order to lower the content of Mn and improve the hardenability of the steel compared to the steels used in the prior art Zr was added to improve the processability by controlling the shape of nonmetallic inclusions.
Hereinafter, the reason for the addition of the alloying component and the limit of the component range of the present invention will be described.
C: 0.25% to 0.35% by weight
C is an austenite stabilizing element and is an important element which is dissolved in a matrix at the time of hardening to increase strength and hardness. In the present invention, as an element that increases hardness and abrasion resistance, the curing ability decreases sharply at less than 0.25%, and the strength decreases. When the content exceeds 0.35%, the effect of improving the hardenability due to the addition of B is reduced. Therefore, the content of C is limited to the range of 0.25% by weight to 0.35% by weight.
Si : 0.10 wt% ~ 0.35 wt%
Si is used as an effective deoxidizer in steelmaking and is an element added to secure the strength by ferrite strengthening at the base. If the content is lower than 0.10% by weight, the deoxidation is insufficient, and if it is added higher than 0.35% by weight. It promotes ferrite formation, embrittles, and decreases forging. Therefore, the content of Si is limited to 0.10% to 0.35% by weight.
Mn : 0.65 wt% ~ 0.84 wt%
Mn is also used as a deoxidizer, and it is added to improve the hardenability and strength, and is added to prevent the harmfulness of S present in the steel to form MnS. It is set in%, and when used in excess of 0.84% by weight, the micro segregation and hydrogen crack sensitivity are increased. Therefore, the content of Mn is limited to the range of 0.65% by weight to 0.84% by weight.
Ni : 0.20 wt% ~ 0.50 wt%
Ni is an element that increases toughness and promotes graphitization, and when added in less than 0.20% by weight, Ni has a large decrease in toughness, and when added in excess of 0.50% by weight, Ni is economical and generates residual austenite, causing embrittlement. Therefore, the content of Ni is limited to 0.20% by weight to 0.50% by weight.
Cr : 1.00 wt% ~ 1.50 wt%
Cr is an element that increases the hardenability and makes the carbide to increase the impact resistance. The lower limit is set to 1.00% by weight in order to compensate for the hardenability due to the reduction of Mn content and to increase the tempering resistance by forming complex compounds with Mo, V and the like. In consideration of corrosion resistance and economical efficiency, the upper limit is limited to 1.50% by weight.
Mo : 0.20 wt% ~ 0.45 wt%
Mo combines with C to form carbides (Mo 2 C) to give high temperature hardness and strength, and Mo contained in Mo 2 C combines with grains of phosphorus (P) to relieve tempering brittleness by P and to temper secondary As an element which improves sclerosis | hardenability, the effect is insignificant in less than 0.20 weight%, and when it exceeds 0.45 weight%, since there is no economic effect by an increase in manufacturing cost, the content range of Mo is limited to 0.20 weight%-0.45 weight%.
V: 0.03 wt% ~ 0.12 wt%
V refines grains by fine carbonitride formation to improve strength and toughness. If the added amount is less than 0.03% by weight, the effect of increasing strength is small, and if it is added more than 0.12% by weight, the strength is increased, but toughness is lowered, which is not preferable because there is no economic effect due to the increase in manufacturing cost. Therefore, the V content is limited to 0.03% by weight to 0.12% by weight.
Al : 0.020 wt% ~ 0.050 wt%
Al is at the same time acting as a strong deoxidizer, in combination with N sikina refine the crystal grains is less than 0.020% by weight of deoxidation and is not preferred because the small grain refinement effect, 0.050% by weight in excess over by addition rather than Al 2 O 3 The same nonmetallic inclusions can have a rather detrimental effect. Therefore, the appropriate content range of Al is limited to 0.020 ~ 0.050% by weight.
B: 0.0005% by weight to 0.0050% by weight
With the addition of trace amounts, B hardly improves the hardenability due to grain boundary segregation, while B has an effect of increasing the hardenability of the basic components of steel such as Mn, Cr, Mo, etc. It tends to decrease with a small increase. When B impregnated around a less than 5 ppm, because the boron mouth gyepyeon seats difficult hardenability improving effect is sharply reduced was set as the lower limit, 50 ppm is exceeded, the dispersoids of BN and Fe 23 of boron at the grain boundaries (C, B) 6 Was formed, and hot brittleness caused the red brittleness, which adversely affects the product characteristics, so it was set as the upper limit.
Zr : 0.0050% to 0.0500% by weight
When excessively added as an element added for the purpose of improving the workability by spheroidizing non-metallic inclusions, it is limited to 0.0050% by weight to 0.0500% by weight, depending on the sulfur (S) and oxygen (O) content, because it reduces the machinability.
On the other hand, phosphorus (P), sulfur (S), oxygen (O), nitrogen (N), hydrogen (H), etc. are basically impurities in the steelmaking process during the manufacturing process. In the case of S, the hot workability is lowered, and in combination with Mn or Mo, the workability is increased, but if too much, the toughness is reduced, so it is added at 0.020% by weight or less.
Oxygen, nitrogen, hydrogen, etc. also form oxides, nitrides, hydrides, and molecular hydrogen, making the material brittle. Therefore, these elements were set to O: 0.0020% or less, N: 0.0100% or less, and H: 0.00020% or less so that they can be easily managed in the steelmaking process.
In addition to satisfying the composition range as described above, the plastic mold steel according to the present invention must satisfy the following relational expression related to tempering softening resistance.
T SR =
Equation T SR is an arbitrary relation related to tempering softening resistance, and in the case of plastic mold steel to which the present invention is applied, quenching and nitriding for securing high temperature stability (normal temperature / high temperature strength, impact resistance, and abrasion resistance) after mold processing of tempered steel The treatment can be performed further.
In general, nitriding is a heat treatment method for obtaining a hard surface by a surface hardening method by introducing nitrogen into a metal surface by contacting with a nitriding gas (usually ammonia) while maintaining the metal at an appropriate temperature (below A C1 ). The nitriding temperature is between 495 and 565 ° C for all steels. At this time, if the tempering softening resistance is not excellent, it is difficult to use the plastic mold. Therefore, an optimal alloy design is needed to satisfy both economical and steel characteristics of the relation T SR range related to tempering softening resistance.
T SR presented above If the value is lower than 3, the tempering softening resistance is low, and the high temperature stability (normal temperature / high temperature strength, impact resistance, and abrasion resistance) of the mold during plastic molding is lowered, thereby reducing the mold life. Also T SR If the value is higher than 4, the economic effect of increasing the amount of addition of Cr, Mo, and V components is lost.
Hereinafter, the present invention will be described in more detail with reference to Examples.
Example 1: Composition and manufacturing method of plastic mold steel
Table 1 shows the chemical components of the inventive steel and the comparative steel having the composition of the present invention. Inventive steels A to C represent chemical compositions for steel grades manufactured using vacuum induction melting (VIM) in various alloy designs set up for development. Invented steel D shows the chemical composition of the mass-produced products designed to the optimum conditions through the evaluation of the A-C of the VIM material produced by the alloy design.
Invented steels A to D and
For reference, the upsetting process refers to a process of extruding the material in the vertical direction to reduce the height and widen the cross section. The reason for performing the first and second upsetting in the present invention is to minimize ingot dendritic structure and prevent internal defects. will be. In addition, after free forging in order to prevent defects caused by hydrogen, hydrogen diffusion heat treatment was performed at 550 ° C to 650 ° C. Thereafter, quenching at 850 ° C. to 950 ° C. and heat treatment at 550 ° C. to 650 ° C. were performed to produce the final plastic mold steel. Hardness comparison results for the inventive steels and the comparative steels are shown in FIGS. 1A and 1B.
TABLE 1 (% by weight)
In general, the hardenability of steel is affected by alloy composition, heating temperature, grain size of austenite, homogeneity of alloy components, etc., but is most particularly affected by alloy composition. According to FIGS. 1A and 1B, the inventive steels A to D appear to have a lower hardness value than the
Comparative steel 3 (Korean Patent 10-0263426) developed by adding B to reduce C content and ensure uniform hardness to the inside for excellent welding repair among the required characteristics of mold steel, prehardened steel equivalent to SCM440 Jominy curves for Comparative Steel 4 and Invented Steel D are shown in FIG. 1 (b). In the case of the inventive steel D, even if the Mn content is adjusted to the lower limit than the comparative steel 3, it is judged that the addition of an appropriate amount of element B for the purpose of securing quenchability is effective to have uniform hardness from the surface to the center.
2 and 3 show the cross-sectional hardness distribution and tensile strength values for forgings of inventive steel D and comparative steels 3 and 4. Invented steel D has a hardness distribution higher than that of comparative steel 3 and lower than that of comparative steel 4. In the case of the tensile strength, the invention steel D showed the same level as the comparative steel 3 and lower than the comparative steel 4.
Example 2: workability evaluation test
Table 2 shows the test conditions for the evaluation of workability for the forged steel of the invention steel 4 and Comparative steel 4 prepared as in Example 1. As shown in the test conditions in Table 2, the number of holes until tool breakage was evaluated by tool life (drilling processability for invention steel and comparative steel) while drilling was carried out 15mm deep in the cross-sectional direction using φ9mm carbide tools. And the result is shown in FIG. According to FIG. 4, the inventive steel D shows excellent drilling workability results compared to the comparative steels 3 and 4, which is considered to be due to controlling the distribution of MnS inclusions by Zr addition. The MnS inclusion distribution results for this are shown in FIG. 5. 5 is a diagram showing the degree of stretching of Mns inclusions in Comparative Steel 3 and Inventive Steel 4. FIG.
According to FIG. 5, in Comparative Steel 3, it can be seen that MnS inclusions are elongated. However, in the inventive steel 4, Zr-based oxides and nitrides are preferentially formed by Zr addition, and even distribution of Zr-based oxides and Zr-based nitrides is achieved. Provided nucleation sites of MnS, induced a fine and even distribution, and it can be seen that Zr oxide has the effect of preventing the stretching of MnS.
TABLE 2
1A and 1B are diagrams showing the results of quenchability comparison between the inventive steel and the comparative steel according to the alloying components in the examples of the present invention.
2 is a view showing the cross-sectional hardness comparison results after the QT heat treatment of the forged steel according to the invention steel and comparative steel in the embodiment of the present invention.
Figure 3 is a view showing the tensile strength comparison results after the QT heat treatment of the forged steel according to the invention steel and comparative steel in the embodiment of the present invention.
4 is a view showing the drilling workability evaluation after the QT heat treatment of the forgings according to the invention steel and comparative steel in the embodiment of the present invention.
5 is a view showing the shape of the non-metallic inclusions of the forged product according to the invention steel and comparative steel in the embodiment of the present invention.
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Cited By (8)
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| KR101302693B1 (en) * | 2012-10-17 | 2013-09-03 | 주식회사 세아베스틸 | Plastic mold steel with uniform hardness and workability by reducing segregation |
| CN104674132A (en) * | 2013-11-27 | 2015-06-03 | 斗山重工业株式会社 | Hybrid mold steel and manufacturing method thereof |
| US20170226605A1 (en) * | 2016-02-05 | 2017-08-10 | A. FinkI & Sons Co | Plastic injection mold tooling and a method of manufacture thereof |
| EP3385049A1 (en) * | 2017-04-07 | 2018-10-10 | A. Finkl & Sons Co. | Plastic injection mold tooling and a method of manufacture thereof |
| US10260122B2 (en) | 2016-02-05 | 2019-04-16 | A. Finkl & Sons Co. | Plastic injection mold tooling and a method of manufacture thereof |
| RU2703630C1 (en) * | 2018-06-26 | 2019-10-21 | А. Финкл энд Сонс Ко. | Equipment for plastic injection molding and method of its manufacturing |
| CN112322965A (en) * | 2020-09-15 | 2021-02-05 | 舞阳钢铁有限责任公司 | Corrosion-resistant die steel plate and production method thereof |
| WO2023272873A1 (en) * | 2021-06-30 | 2023-01-05 | 江苏省沙钢钢铁研究院有限公司 | Plastic mold steel plate and production method therefor |
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| KR101302693B1 (en) * | 2012-10-17 | 2013-09-03 | 주식회사 세아베스틸 | Plastic mold steel with uniform hardness and workability by reducing segregation |
| CN104674132A (en) * | 2013-11-27 | 2015-06-03 | 斗山重工业株式会社 | Hybrid mold steel and manufacturing method thereof |
| US20170226605A1 (en) * | 2016-02-05 | 2017-08-10 | A. FinkI & Sons Co | Plastic injection mold tooling and a method of manufacture thereof |
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| KR20200001460A (en) * | 2018-06-26 | 2020-01-06 | 에이.핀클 앤드 선스 컴퍼니 | Plastic injection mold tooling and a method of manufacture thereof |
| KR102329951B1 (en) | 2018-06-26 | 2021-11-23 | 에이.핀클 앤드 선스 컴퍼니 | Plastic injection mold tooling and a method of manufacture thereof |
| CN112322965A (en) * | 2020-09-15 | 2021-02-05 | 舞阳钢铁有限责任公司 | Corrosion-resistant die steel plate and production method thereof |
| WO2023272873A1 (en) * | 2021-06-30 | 2023-01-05 | 江苏省沙钢钢铁研究院有限公司 | Plastic mold steel plate and production method therefor |
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