WO2012090562A1 - 耐発錆性および熱伝導性に優れた金型用鋼およびその製造方法 - Google Patents
耐発錆性および熱伝導性に優れた金型用鋼およびその製造方法 Download PDFInfo
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- WO2012090562A1 WO2012090562A1 PCT/JP2011/072317 JP2011072317W WO2012090562A1 WO 2012090562 A1 WO2012090562 A1 WO 2012090562A1 JP 2011072317 W JP2011072317 W JP 2011072317W WO 2012090562 A1 WO2012090562 A1 WO 2012090562A1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
Definitions
- the present invention relates to a steel for molds that has both excellent rust resistance and thermal conductivity and is most suitable for plastic molding applications, and a method for producing the same.
- improvement in rust resistance and thermal conductivity is an important requirement for recent mold steels.
- rust is generated on the mold surface due to condensation when the mold is not used, such as during production or maintenance.
- a process of removing rust is essential when starting to use again, which causes a decrease in productivity. Therefore, many improvement of rust resistance is calculated
- the improvement of the thermal conductivity of the mold steel is an important improvement characteristic for shortening the thermal cycle and increasing the productivity in plastic molding that repeats heating and cooling.
- the steel for mold of Patent Document 1 containing 2 to 5% Cr is excellent in rust resistance.
- the thermal conductivity is low, there is a concern that the thermal cycle time increases depending on the molding conditions and the productivity is lowered.
- the steel for molds of Patent Document 2 in which Cr is 2.5% or less has high thermal conductivity and can shorten the heat cycle time.
- there is room for improvement in rust resistance compared with the steel for molds of Patent Document 1, there is room for improvement in rust resistance.
- heat conductivity and rust resistance are contradictory properties, it has been desired to provide steel for molds having these properties at a high level.
- An object of the present invention is to provide a mold steel having both excellent thermal conductivity and rust resistance and a preferable manufacturing method for obtaining the mold steel.
- the present inventor has reviewed the component composition of steel for molds. As a result, it was confirmed that even many element types constituting the conventional steel for molds interacted with each other in a complicated manner with respect to rust resistance and thermal conductivity. And for the purpose of combining both of the above characteristics, we extracted factors that have a particularly large influence among many elemental species, and found that there is an optimal relationship between these contents. The present invention has been reached.
- the present invention in mass%, C: 0.07 to 0.15%, Si: more than 0 to less than 0.8%, Mn: more than 0 to less than 1.5%, P: less than 0.05% , S: less than 0.06%, Ni: more than 0 to less than 0.9%, Cr: 2.9 to 4.9%, Mo and W alone or in combination (Mo + 1 / 2W): more than 0 to 0. Less than 8%, V: more than 0 to less than 0.15%, Cu: 0.25 to 1.8%, with the balance being steel composed of Fe and inevitable impurities, with a hardness of 30 to It is steel for metal mold
- the present invention by mass, C: 0.07 to 0.15%, Si: more than 0 to less than 0.8%, Mn: more than 0 to less than 1.5%, P: less than 0.05% , S: less than 0.06%, Ni: more than 0 to less than 0.9%, Cr: 2.9 to 4.9%, Mo and W alone or in combination (Mo + 1 / 2W): more than 0 to 0. Less than 8%, V: more than 0 to less than 0.15%, Cu: 0.25 to 1.8%, the balance is composed of Fe and inevitable impurities.
- the feature of the present invention resides in that an element species having a great influence on rust resistance and thermal conductivity can be specified as a constituent element of steel for molds. That is, C, S, Ni, Cr, Mo, and W have a great influence on rust resistance, and C, Si, Mn, Ni, Cr, Mo, W, and Cu have a great influence on thermal conductivity. It is.
- C, S, Ni, Cr, Mo, and W have a great influence on rust resistance
- C, Si, Mn, Ni, Cr, Mo, W, and Cu have a great influence on thermal conductivity. It is.
- heat conduction can be achieved by reviewing the amounts of C, Si, Mn, Ni, Cr, Mo, W, and Cu. Improvement in performance can be achieved.
- Patent Document 2 having excellent thermal conductivity by improving the content of C, S, Ni, Cr, Mo, W, rust resistance can be improved. Can be achieved.
- a further feature of the present invention is that the degree of influence of the identified element species on rust resistance and thermal conductivity can be quantified. By quantifying the degree of influence, the optimum component composition of the mold steel to be adjusted is clarified, and further improvement in rust resistance and thermal conductivity can be achieved. Hereinafter, each component requirement will be described.
- ⁇ C 0.07 to 0.15% C is an element that enhances hardenability and brings about structural strengthening by precipitation of Cr, Mo (W), and V carbides in tempering, and maintains the quenching and tempering hardness of 30 to 42 HRC described later.
- said tempering temperature can be made high. Therefore, in the steel of the present invention, for example, it is important to add a sufficient amount of C that can stably achieve a hardness of 30 HRC or higher even when tempering at 530 ° C. or higher.
- the rust resistance decreases, so in the present invention, it is 0.15% or less.
- solid solution Cr is a major factor for lowering the thermal conductivity of the mold steel, if the amount of C forming the Cr carbide is too small, the thermal conductivity of the mold steel is deteriorated. And since necessary hardness cannot be obtained, it is made 0.07% or more. Preferably, it is 0.08% or more and / or 0.13% or less. More preferably, it is 0.1% or more and / or 0.12% or less. 0.1% or less is more preferable.
- Si more than 0 to less than 0.8% Si is an element that enhances the corrosion resistance against the atmosphere when using a mold, such as a gas generated from a molding material during plastic molding.
- a mold such as a gas generated from a molding material during plastic molding.
- Si when the amount is too large, the thermal conductivity of the mold steel is remarkably lowered, and the thermal conductivity is deteriorated.
- Si when Si is reduced, the anisotropy of mechanical properties is reduced, stripe segregation is also reduced, and excellent mirror surface workability is obtained. Therefore, it is less than 0.8% in the present invention.
- it is 0.1% or more and / or 0.6% or less. More preferably, it is 0.15% or more and / or 0.5% or less. More preferably, it is 0.2% or more. 0.25% or more is particularly preferable.
- Mn more than 0 to less than 1.5%
- Mn is an element that increases hardenability, suppresses the formation of ferrite, and imparts appropriate quenching and tempering hardness.
- the amount is too large, not only the thermal conductivity is remarkably impaired, but also non-metallic inclusion MnS is formed by combining with S described later, which also causes rust and pinholes.
- the content is made less than 1.5%.
- it is 0.1% or more and / or 1.0% or less. More preferably, it is 0.2% or more and / or 0.8% or less. 0.3% or more is more preferable.
- P is an element that reduces hot workability and toughness when it is too much. Therefore, in the present invention, it is less than 0.05%. Preferably, it is 0.03% or less.
- S has a great effect in improving machinability by being present as MnS of non-metallic inclusions.
- MnS has a great effect in improving machinability by being present as MnS of non-metallic inclusions.
- the presence of a large amount of MnS becomes a factor that degrades the performance of the mold itself, such as promoting mechanical properties, particularly toughness anisotropy.
- MnS also becomes a starting point of rust and pinhole generation, which greatly deteriorates rust resistance and polishing finish, which are important characteristics for the steel of the present invention. Therefore, even if S is added, it is limited to less than 0.06%. 0.035% or less is preferable. A preferred lower limit is 0.005% or more.
- Ni more than 0 to less than 0.9% Ni also enhances the hardenability of the steel of the present invention and suppresses the formation of ferrite. And it is an element which improves the rust resistance of this invention steel. However, if the amount is too large, not only the thermal conductivity is lowered, but also the viscosity of the base is raised to reduce the machinability. Therefore, Ni is less than 0.9%. Preferably, it is 0.1% or more and / or 0.6% or less. More preferably, it is 0.15% or more, More preferably, it is 0.2% or more.
- ⁇ Cr 2.9 to 4.9% Cr is an element that precipitates and agglomerates fine carbides by tempering to increase the strength of the steel of the present invention. On the other hand, it is an element that improves the rust resistance of the steel of the present invention by dissolving in the base. Further, when nitriding is performed, there is an effect of increasing the hardness of the nitrided layer. However, if the amount is too large, the amount of the solid solution Cr increases, not only significantly reducing the thermal conductivity, but also reducing the softening resistance. Therefore, the Cr of the present invention is 2.9 to 4.9%. Preferably, it is 3.5% or more and / or 4.8% or less. 3.8% or more is more preferable.
- Mo and W are singly or in combination (Mo + 1 / 2W): more than 0 to less than 0.8% Mo and W precipitate and agglomerate fine carbides during tempering to improve the strength of the steel of the present invention.
- the resistance to softening during tempering is increased.
- Cr since it is an element which improves the rust resistance of the steel of the present invention by dissolving in the matrix, it is an element contained alone or in combination.
- a part of Mo and W is partly dissolved in the oxide film on the mold surface, thereby improving the corrosion resistance against corrosive gas generated from, for example, plastic during use of the mold. Also have. However, if too much, the machinability is reduced.
- Mo and W are less than 0.8% in a single or composite amount defined by the relational expression of (Mo + 1 / 2W). Preferably, it is 0.1% or more and / or 0.6% or less. More preferably, it is 0.3% or more and / or 0.5% or less.
- V more than 0 to less than 0.15% V increases temper softening resistance and suppresses coarsening of crystal grains, thereby contributing to improvement of toughness. In addition, there is an effect of improving the wear resistance by forming hard carbide finely. However, if the amount is too large, the machinability deteriorates, so the content was made less than 0.15%. Preferably, it is 0.03% or more and / or 0.10% or less. More preferably, it is 0.05% or more, More preferably, it is 0.07% or more.
- Cu 0.25 to 1.8%
- Cu is an element that improves the strength of the steel of the present invention by precipitating and aggregating a Fe—Cu solid solution during tempering.
- Cu of the present invention is made 0.25 to 1.8%.
- it is 0.4% or more and / or 1.5% or less. More preferably, it is 0.7% or more, More preferably, it is 1.0% or more.
- Al of the present invention is preferably regulated to less than 0.1%. More preferably, it is less than 0.05%.
- N nitrogen: less than 0.06% N, an inevitable impurity, is an element that forms nitrides in steel. If the nitride is excessively formed, the toughness, machinability and polishability of the mold are significantly deteriorated. Therefore, it is preferable to regulate N in steel low. Therefore, in this invention, it is preferable to prescribe
- O oxygen
- O oxygen
- the upper limit of O of the present invention is preferably regulated to 0.005%. More preferably, it is less than 0.003%.
- the values according to the following formulas 1 and 2 satisfy 100 or more ([] in parentheses indicate the content (mass%) of each element).
- Formula 1 85-60.1 ⁇ [C%] ⁇ 115 ⁇ [S%] + 0.1 ⁇ [Ni%] + 7.17 ⁇ [Cr%] + 2.44 ⁇ [(Mo + 1 / 2W)%]
- Formula 2 140 + 30.9 ⁇ [C%] ⁇ 17.8 ⁇ [Si%] ⁇ 10.5 ⁇ [Mn%] ⁇ 12.4 ⁇ [Ni%] ⁇ 3.68 ⁇ [Cr%] ⁇ 1.
- the degree of influence on the rust resistance and thermal conductivity of each of the constituent elements of the steel of the present invention was investigated.
- the improvement effect is large in the order of Cr, Mo, W, and Ni.
- S and C have been found to decrease the characteristics in this order.
- thermal conductivity the improvement effect due to the inclusion of C is large, and it was found that Si, Ni, Mn, Cr, Cu, Mo, and W deteriorate the characteristics in this order. Then, by performing a multiple regression analysis using the contents of these elements as variables, it was possible to express the degree of influence as an accurate mutual coefficient.
- the degree of influence of the constituent elements on the rust resistance of the steel of the present invention can be mutually expressed by the following formula 1.
- the coefficient of the element for improving the characteristic is expressed as positive, and the coefficient of the element for decreasing the characteristic is expressed as negative.
- it is preferable for the further improvement of rust resistance that the value of Formula 1 is 100 or more. More preferably, the value is 105 or more.
- Formula 1 85-60.1 ⁇ [C%] ⁇ 115 ⁇ [S%] + 0.1 ⁇ [Ni%] + 7.17 ⁇ [Cr%] + 2.44 ⁇ [(Mo + 1 / 2W)%]
- the influence degree of the constituent element concerning the thermal conductivity of the steel of the present invention can be mutually expressed by the following formula 2.
- the coefficient of the element that works to improve the characteristic is expressed as plus, and the coefficient of the element that works down the characteristic is expressed as minus.
- the value of Formula 2 is 100 or more. More preferably, the value is 105 or more.
- the hardness of the mold steel is 30-42 HRC. If the hardness of the material is too low, the mirror surface workability at the time of mold production is reduced. And the abrasion resistance as a mold product also falls. On the other hand, if the hardness of the material is too high, the machinability at the time of mold production is reduced. And the toughness as a mold product also falls. Therefore, the hardness of the mold steel of the present invention is 30 to 42 HRC. Preferably, it is 35 HRC or more and / or 40 HRC or less.
- the mold steel of the present invention can be used as so-called pre-hardened steel that is tempered to the hardness by quenching and tempering heat treatment and then cut into a mold shape.
- the steel of the present invention can stably achieve the above hardness of 30 HRC or more, and further 35 HRC or more even by tempering at a high temperature of 530 ° C. or more. Even tempering at 540 ° C. or higher can be achieved.
- tempering at a high temperature that can reduce the residual stress in the steel is advantageous in order to suppress the processing strain that occurs during cutting.
- the mold steel of the present invention is adjusted to an optimum component composition that combines the above-described tempering characteristics with excellent rust resistance and thermal conductivity. In this case, no special setting is required for the quenching temperature. For example, quenching from a temperature of 900 ° C. or higher can be applied.
- Table 1 also shows the values of Formulas 1 and 2 according to the present invention.
- Conventional steels 1 and 2 correspond to Patent Documents 1 and 2, respectively.
- these steel ingots were forged at 1150 ° C. to obtain a steel material having a thickness of 30 mm ⁇ width of 30 mm, which was annealed at 860 ° C. And from each annealing treatment material, for the hardness evaluation of 10 mm ⁇ 10 mm ⁇ 10 mm, for rust resistance evaluation of 5 mm ⁇ 8 mm ⁇ 15 mm, and for the thermal conductivity evaluation of diameter 10 mm ⁇ thickness 1 mm Dimensionally shaped steel pieces were processed. And the following tests were implemented about what performed predetermined hardening tempering processing to these steel pieces.
- the steel of the present invention achieved a hardness of 30 HRC or higher even at 550 ° C., and preferably a hardness of 35 HRC or higher.
- steels 1 to 6 of the present invention in which the component composition is optimally adjusted, achieves both excellent rust resistance and thermal conductivity compared to conventional steels 1 and 2.
- the steels 3 to 6 of the present invention having a value of Formula 1 of 100 or more, no occurrence of rust was confirmed.
- the comparative steel 1 having a high Si and the comparative steel 3 having a high Ni have greatly reduced thermal conductivity.
- Even comparative steel 2 having a component composition close to that of the present invention steel has high Ni and low thermal conductivity.
- the comparative steel 3 with low Cr also has low rust resistance.
- Example 4 A 10 kg steel ingot was melted in the same manner as in Example 1 except that the component composition was changed.
- Table 4 shows the component composition.
- Table 4 as in Table 1, the values of Formulas 1 and 2 according to the present invention are also shown.
- these steel ingots were forged under the same conditions as in Example 1 and annealed. And from each annealing treatment material, for the hardness evaluation of 10 mm ⁇ 10 mm ⁇ 10 mm, for rust resistance evaluation of 5 mm ⁇ 8 mm ⁇ 15 mm, and for the thermal conductivity evaluation of diameter 10 mm ⁇ thickness 1 mm Dimensionally shaped steel pieces were processed. And the following tests were implemented about what performed predetermined hardening tempering processing to these steel pieces.
- the inventive steels 7 to 22 have excellent rust resistance and thermal conductivity, and achieve both of these.
- the steel 10 of the present invention has a high amount of C, but the value of the formula 1 is high and the rust resistance is good.
- the comparative steels 5 and 6 with high Si have low thermal conductivity.
- the comparative steel 7 with low Cr has a large amount of decrease in mass due to the occurrence of rust, and the rust resistance is reduced.
- the steel of the present invention also satisfies the basic characteristics for molds, in addition to molds for plastic molding, molds for rubber molding, hot working for small lot production, die casting, etc. It can also be applied to molds.
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Abstract
Description
(1)鏡面仕上げ性が良く、ピンホールやその他微細ピットの発生傾向が小さいこと、
(2)シボ加工性が良いこと、
(3)強度、耐摩耗性、靭性が良いこと、
(4)被切削性が良いこと、
(5)耐食性、耐発錆性が良いこと、
(6)熱伝導性が良いこと、
などが要求される。
また、C:0.10~0.25%、Si:1.00%以下、Mn:2.00%以下、Ni:0.60~1.50%、Cr:1.00超~2.50%、MoとWは単独または複合で(Mo+1/2W):1.00%以下、V:0.03~0.15%、Cu:0.50~2.00%、S:0.05%以下を含有し、Alは0.10%以下、Nは0.06%以下、Oは0.005%以下に規制され、残部はFeおよび不可避的不純物の組成でなる金型用鋼が提案されている(特許文献2)。
式1:85-60.1×[C%]-115×[S%]+0.1×[Ni%]+7.17×[Cr%]+2.44×[(Mo+1/2W)%]
式2:140+30.9×[C%]-17.8×[Si%]-10.5×[Mn%]-12.4×[Ni%]-3.68×[Cr%]-1.26×[(Mo+1/2W)%]-3.68[Cu%]
ここで、[]括弧内は各元素の含有量(質量%)を示す。
Cは、焼入性を高め、かつ焼戻しにおいては、Cr、Mo(W)、V炭化物の析出による組織強化をもたらす元素であって、後述する30~42HRCの焼入れ焼戻し硬さを維持するために必要な、基本的添加元素である。そして、切削加工時などに発生する加工歪を抑制するためには、鋼中の残留応力を低減しておくことが望ましく、このためには上記の焼戻し温度は高くできることが必要である。そこで、本発明鋼では、例えば530℃以上の焼戻しでも30HRC以上の硬さを安定して達成できるだけの、十分なC量を添加することが重要である。
Siは、例えばプラスチック成形時の被成形材から発生するガス等、金型使用時の雰囲気に対する耐食性を高める元素である。しかし、多すぎると金型用鋼の有する熱伝導率が著しく低下し、熱伝導性が劣化する。また、Siを低減すると機械的特性の異方性が軽減され、縞状偏析も低減されて、優れた鏡面加工性が得られる。よって、本発明では0.8%未満とする。好ましくは、0.1%以上および/または0.6%以下である。より好ましくは、0.15%以上および/または0.5%以下である。更に好ましくは、0.2%以上である。0.25%以上が、特に好ましい。
Mnは、焼入性を高め、またフェライトの生成を抑制し、適度の焼入れ焼戻し硬さを付与する元素である。しかし、多すぎると熱伝導性を著しく損なうだけでなく、後述のSと結合して非金属介在物MnSを生成して、錆やピンホール発生の要因ともなる。また基地の粘さを上げて被切削性を低下させるので、1.5%未満とする。好ましくは、0.1%以上および/または1.0%以下である。より好ましくは、0.2%以上および/または0.8%以下である。0.3%以上が、更に好ましい。
Pは、多すぎると熱間加工性や靭性を低下させる元素である。よって、本発明では、0.05%未満とする。好ましくは、0.03%以下である。
Sは、非金属介在物のMnSとして存在させることで、被切削性の向上に大きな効果がある。しかし、多量のMnSの存在は、機械的特性、特に靭性の異方性を助長するなど、金型自体の性能を低下させる要因となる。そして、MnSは錆やピンホール発生の起点ともなり、これは本発明鋼にとっての重要な特性である耐発錆性や研磨仕上性を大きく劣化させる。よって、Sは添加する場合であっても、0.06%未満に限定する。0.035%以下が好ましい。なお、好ましい下限は0.005%以上である。
Niも、本発明鋼の焼入れ性を高め、またフェライトの生成を抑制する。そして、本発明鋼の耐発錆性を向上する元素である。しかし、多すぎると熱伝導率を低下するだけでなく、基地の粘さを上げて被切削性も低下させる。よって、Niは0.9%未満とする。好ましくは、0.1%以上および/または0.6%以下である。より好ましくは0.15%以上であり、更に好ましくは0.2%以上である。
Crは、焼戻し処理によって微細炭化物を析出、凝集させ、本発明鋼の強度を高める元素である。そして一方では、基地に固溶することで、本発明鋼の耐発錆性を高める元素である。更に窒化処理を行う場合には、窒化層の硬さを高める効果も有する。しかし、多すぎると、上記の固溶Cr量が増加して、熱伝導率を著しく低下させるだけでなく,軟化抵抗も低下させる。よって、本発明のCrは2.9~4.9%とする。好ましくは、3.5%以上および/または4.8%以下である。3.8%以上が、更に好ましい。
Mo、Wは、焼戻し処理時に微細炭化物を析出、凝集させて、本発明鋼の強度を向上する。また、焼戻し時の軟化抵抗を大きくする。そしてCrと同様に、基地に固溶することで、本発明鋼の耐発錆性を高める元素であることから、単独または複合で含有する元素である。更に、MoやWの一部は、金型表面の酸化皮膜中に一部固溶することで、金型使用中の、例えばプラスチックから発生する腐食性ガスに対しての耐食性を向上する作用効果も有する。しかし多すぎると、被切削性の低下を招く。そして、上記の固溶量が増加すると、熱伝導率を著しく低下させる。よって、本発明では、MoとWは(Mo+1/2W)の関係式で定義される単独または複合量で0.8%未満とした。好ましくは、0.1%以上および/または0.6%以下である。更に好ましくは、0.3%以上および/または0.5%以下である。
Vは、焼戻し軟化抵抗を高めるとともに、結晶粒の粗大化を抑制して、靭性の向上に寄与する。また、硬質の炭化物を微細に形成して、耐摩耗性を向上させる効果がある。しかし、多すぎると被切削性の低下を招くので0.15%未満とした。好ましくは、0.03%以上および/または0.10%以下である。より好ましくは、0.05%以上であり、更に好ましくは、0.07%以上である。
Cuは、焼戻し処理時にFe-Cu固溶体を析出、凝集させ、本発明鋼の強度を向上する元素である。しかし多すぎると、著しく熱間加工性を低下させる。そして、熱伝導率も低下して、本発明鋼の熱伝導性が劣化する。よって、本発明のCuは0.25~1.8%とする。好ましくは、0.4%以上および/または1.5%以下である。より好ましくは、0.7%以上であり、更に好ましくは、1.0%以上である。
不可避的不純物であるAlは、通常、溶製時の脱酸元素として用いられる。そして、硬さを調質後の状態にある本発明鋼においては、その鋼中にAl2O3が多く存在すると鏡面加工性が劣化する。よって、本発明のAlは0.1%未満に規制することが好ましい。より好ましくは0.05%未満である。
不可避的不純物であるNは、鋼中に窒化物を形成する元素である。窒化物は過多に形成されると、金型の靭性、被削性および磨き性を著しく劣化する。したがって、鋼中のNは低く規制することが好ましい。よって本発明では、Nを0.06%未満に規定することが好ましい。より好ましくは0.03%未満である。
不可避的不純物であるOは、鋼中に酸化物を形成する元素である。過多の酸化物は、冷間での塑性加工性および磨き性を著しく劣化させる要因となる。そして本発明では、特に上記のAl2O3の形成を抑えることが重要である。よって、本発明のOは、上限を0.005%に規制することが好ましい。より好ましくは、0.003%未満である。
式1:85-60.1×[C%]-115×[S%]+0.1×[Ni%]+7.17×[Cr%]+2.44×[(Mo+1/2W)%]
式2:140+30.9×[C%]-17.8×[Si%]-10.5×[Mn%]-12.4×[Ni%]-3.68×[Cr%]-1.26×[(Mo+1/2W)%]-3.68[Cu%]
強度や軟化抵抗、被削性等の基本特性を満足した上で、さらに本発明の特徴である優れた耐発錆性および熱伝導性を達成するためには、本発明鋼を構成する多くの元素種の含有量を上記の成分範囲内に調整する必要がある。しかし、耐発錆性および熱伝導性に及ぼす影響の度合いは、これら個々の元素で異なる。したがって、基本特性を維持して、さらに優れた耐発錆性と熱伝導性を両立させるには、構成元素種の含有量を相互的に管理することが有効である。
式1:85-60.1×[C%]-115×[S%]+0.1×[Ni%]+7.17×[Cr%]+2.44×[(Mo+1/2W)%]
式2:140+30.9×[C%]-17.8×[Si%]-10.5×[Mn%]-12.4×[Ni%]-3.68×[Cr%]-1.26×[(Mo+1/2W)%]-3.68[Cu%]
素材の硬さが低すぎると、金型作製時の鏡面加工性が低下する。そして、金型製品としての耐摩耗性も低下する。一方、素材の硬さが高すぎると、金型作製時の被切削性が低下する。そして、金型製品としての靭性も低下する。よって、本発明の金型用鋼の硬さは30~42HRCとする。好ましくは、35HRC以上および/または40HRC以下である。本発明の金型用鋼は、焼入れ焼戻し熱処理によって該硬さに調質された後、金型形状に切削加工される、いわゆるプリハードン鋼としての使用が可能である。
10mm×10mm×10mmの鋼片を用いて、これに950℃からのガス冷却による焼入れ処理を行った。そして、焼戻し処理は、鋼中の残留応力を低減するのに有利な高温焼戻しとして、550℃で2時間の条件とした。硬さの結果を表2に示す。本発明鋼は、550℃の焼戻しでも30HRC以上の硬さを達成し、好ましいものでは35HRC以上の硬さを達成した。
5mm×8mm×15mmの鋼片を用いて、これに上記と同様の焼入れ処理を行った。焼戻し処理は、硬さが34~36HRC(狙い硬さ35HRC)になるように、540℃から580℃の適正温度で2時間の条件とした。そして、この焼戻し処理後の試験片に、温度80℃、湿度90%の雰囲気で24時間の曝露試験を行い、8mm×15mmの表面に発生した錆の面積率(100×錆発生面積(mm2)/試験片の表面積(mm2))を算出した。結果を表3に示す。
直径10mm×厚さ1mmの鋼片を用いて、これに上記と同様の焼入れ処理を行った。焼戻し処理は、上記と同様の、硬さが34~36HRC(狙い硬さ35HRC)になるように、540℃から580℃の適正温度で2時間の条件とし、耐発錆性の評価用試験片とともに処理した。そして、焼戻し処理後の試験片に対し、レーザーフラッシュ法により熱伝導率を測定した。結果を表3に示す。
10mm×10mm×10mmの鋼片を用いて、これに実施例1と同じ条件の焼入れ処理を行った。そして、焼戻し処理は、実施例1の550℃で2時間の条件と、580℃で2時間の条件の、2条件を実施した。硬さの結果を表5に示す。なお、表5には、実施例1で評価した本発明鋼2、3、5、6と、比較鋼1~3、従来鋼1、2の結果も併せて示す。本発明鋼は、550℃の焼戻しに加えて、580℃の焼戻しでも30HRC以上の硬さを達成し、好ましいものでは35HRC以上の硬さを達成した。なお、Vが低めの本発明鋼22は、580℃の焼戻しで硬さが30HRCを下回った。一方、C量の少ない比較鋼4は、550℃、580℃の両方の焼戻しで30HRCを達成しなかった。
5mm×8mm×15mmの鋼片を用いて、これに実施例1の耐発錆性の評価時と同じ条件の焼入れおよび焼戻し処理と、曝露試験を行った。そして、試験前の試験片の質量と、試験後の錆を落とした試験片の質量とを測定して、質量の減少率(100×試験片の減少量(g)/試験前の試験片の質量(g))を算出した。結果を表6に示す。なお、表6には、実施例1で評価した従来鋼2の結果も併記しておく。
直径10mm×厚さ1mmの鋼片を用いて、これに実施例1の熱伝導性の評価時と同じ条件の焼入れおよび焼戻し処理と、熱伝導率の測定をした。結果を表6に示す。なお、表6には、実施例1で評価した従来鋼2の結果も併記しておく。
Claims (6)
- 質量%で、C:0.07~0.15%、Si:0超~0.8%未満、Mn:0超~1.5%未満、P:0.05%未満、S:0.06%未満、Ni:0超~0.9%未満、Cr:2.9~4.9%、MoとWは単独または複合で(Mo+1/2W):0超~0.8%未満、V:0超~0.15%未満、Cu:0.25~1.8%を含有し、残部はFeおよび不可避的不純物からなる組成の鋼であって、硬さが30~42HRCであることを特徴とする耐発錆性および熱伝導性に優れた金型用鋼。
- 鋼の組成は、質量%による下記の式1および式2による値がそれぞれ100以上を満たすことを特徴とする請求項1に記載の耐発錆性および熱伝導性に優れた金型用鋼。
式1:85-60.1×[C%]-115×[S%]+0.1×[Ni%]+7.17×[Cr%]+2.44×[(Mo+1/2W)%]
式2:140+30.9×[C%]-17.8×[Si%]-10.5×[Mn%]-12.4×[Ni%]-3.68×[Cr%]-1.26×[(Mo+1/2W)%]-3.68[Cu%]
ここで、[]括弧内は各元素の含有量(質量%)を示す。 - 不可避的不純物であるAlは0.1%未満、Nは0.06%未満、Oは0.005%未満に規制することを特徴とする請求項1または2に記載の耐発錆性および熱伝導性に優れた金型用鋼。
- 質量%で、C:0.07~0.15%、Si:0超~0.8%未満、Mn:0超~1.5%未満、P:0.05%未満、S:0.06%未満、Ni:0超~0.9%未満、Cr:2.9~4.9%、MoとWは単独または複合で(Mo+1/2W):0超~0.8%未満、V:0超~0.15%未満、Cu:0.25~1.8%を含有し、残部はFeおよび不可避的不純物からなる組成の鋼を、焼入れと、530℃以上の温度による焼戻しによって、硬さを30~42HRCに調整することを特徴とする耐発錆性および熱伝導性に優れた金型用鋼の製造方法。
- 鋼の組成は、質量%による下記の式1および式2による値がそれぞれ100以上を満たすことを特徴とする請求項4に記載の耐発錆性および熱伝導性に優れた金型用鋼の製造方法。
式1:85-60.1×[C%]-115×[S%]+0.1×[Ni%]+7.17×[Cr%]+2.44×[(Mo+1/2W)%]
式2:140+30.9×[C%]-17.8×[Si%]-10.5×[Mn%]-12.4×[Ni%]-3.68×[Cr%]-1.26×[(Mo+1/2W)%]-3.68[Cu%]
ここで、[]括弧内は各元素の含有量(質量%)を示す。 - 不可避的不純物であるAlは0.1%未満、Nは0.06%未満、Oは0.005%未満に規制することを特徴とする請求項4または5に記載の耐発錆性および熱伝導性に優れた金型用鋼の製造方法。
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CN103774047A (zh) * | 2012-10-20 | 2014-05-07 | 大同特殊钢株式会社 | 具有优异的热导性、镜面抛光性和韧性的成型模具用钢 |
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EP2963137A4 (en) * | 2013-02-28 | 2016-11-02 | Hitachi Metals Ltd | DIE STEEL AND PROCESS FOR PRODUCING SAME |
WO2014132868A1 (ja) | 2013-02-28 | 2014-09-04 | 日立金属株式会社 | 金型用鋼およびその製造方法 |
CN105026595A (zh) * | 2013-02-28 | 2015-11-04 | 日立金属株式会社 | 模具用钢及其制造方法 |
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CN108624826A (zh) * | 2013-02-28 | 2018-10-09 | 日立金属株式会社 | 模具用钢及其制造方法 |
KR20150110716A (ko) | 2013-02-28 | 2015-10-02 | 히타치 긴조쿠 가부시키가이샤 | 금형용 강 및 그 제조 방법 |
JP2016145407A (ja) * | 2015-01-28 | 2016-08-12 | 大同特殊鋼株式会社 | 鋼の粉末及びこれを用いた金型 |
US10975460B2 (en) | 2015-01-28 | 2021-04-13 | Daido Steel Co., Ltd. | Steel powder and mold using the same |
JP2017024053A (ja) * | 2015-07-24 | 2017-02-02 | 大同特殊鋼株式会社 | 金型補修溶接材料 |
EP3348660A4 (en) * | 2015-09-11 | 2019-03-27 | Daido Steel Co.,Ltd. | STEEL FOR SHAPES AND MOLDING TOOL |
US11141778B2 (en) | 2015-09-11 | 2021-10-12 | Daido Steel Co., Ltd. | Steel for molds and molding tool |
CN112708816A (zh) * | 2021-01-28 | 2021-04-27 | 南通成科精密铸件有限公司 | 一种压铸件及其表面处理方法 |
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KR20130091351A (ko) | 2013-08-16 |
KR101545417B1 (ko) | 2015-08-18 |
CN103282530A (zh) | 2013-09-04 |
JPWO2012090562A1 (ja) | 2014-06-05 |
EP2660348A1 (en) | 2013-11-06 |
EP2660348A4 (en) | 2014-09-03 |
CN103282530B (zh) | 2015-05-13 |
JP5534482B2 (ja) | 2014-07-02 |
EP2660348B1 (en) | 2017-11-15 |
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