JP2000234149A - Metal mold for casting, excellent in erosion resistance - Google Patents
Metal mold for casting, excellent in erosion resistanceInfo
- Publication number
- JP2000234149A JP2000234149A JP3279999A JP3279999A JP2000234149A JP 2000234149 A JP2000234149 A JP 2000234149A JP 3279999 A JP3279999 A JP 3279999A JP 3279999 A JP3279999 A JP 3279999A JP 2000234149 A JP2000234149 A JP 2000234149A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- content
- erosion resistance
- erosion
- resistance
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Molds, Cores, And Manufacturing Methods Thereof (AREA)
- Paper (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、例えば溶融金属の
鋳造鋳型や、スリーブ、ピン等を製造する際の溶湯に接
する金型類において、耐溶損性を改良した鋳造用金型に
関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a casting mold having improved erosion resistance, for example, in a mold which comes into contact with a molten metal when manufacturing a casting mold of molten metal, a sleeve, a pin, and the like. .
【０００２】[0002]
【従来の技術】例えばアルミニウム合金、マグネシウム
合金、銅合金等の溶融金属の金型鋳造（ダイカスト、グ
ラビティ）に用いる金型類には、従来、熱間工具鋼、マ
ルエージング鋼などの、鋼や鋳鉄が用いられている。こ
の中で最も多く使用されているのは、アルミニウム合金
のダイカスト鋳造であるが、この金型類の寿命は必ずし
も満足できるものではなかった。2. Description of the Related Art Molds used for die casting (die casting, gravity) of molten metals such as aluminum alloys, magnesium alloys, and copper alloys include, for example, steels such as hot tool steels and maraging steels. Cast iron is used. Among them, die casting of an aluminum alloy is most frequently used, but the life of the molds has not always been satisfactory.
【０００３】[0003]
【発明が解決しようとする課題】上記した金型類におい
て、寿命を支配するのは主として熱亀裂、溶損である
が、この鋳造用金型の耐溶損性を改善するため、例えば
特開平４−５６７４９号には、窒化処理を施すことが開
示されている。しかし、窒化処理を施した場合であって
も、その金型寿命はまだユーザーのニーズにまでは至っ
ていないのが実状である。In the above-mentioned molds, heat cracks and erosion mainly govern the service life. However, in order to improve the erosion resistance of the casting mold, for example, Japanese Patent Application Laid-Open No. No. 56749 discloses performing a nitriding treatment. However, even in the case where nitriding is performed, the life of the mold has not yet reached the needs of the user.
【０００４】本発明は、上記した実状に鑑みてなされた
ものであり、熱亀裂、大割れに影響する基本的な性能
（高温強度、延性、靱性）は従来の金型類に劣ることな
く、耐溶損性を向上させた鋳造用金型を提供することを
目的としている。[0004] The present invention has been made in view of the above-described circumstances, and the basic performance (high-temperature strength, ductility, toughness) affecting thermal cracks and large cracks is not inferior to conventional molds. An object of the present invention is to provide a casting mold with improved erosion resistance.
【０００５】[0005]
【課題を解決するための手段】上記した目的を達成する
ために、本発明の耐溶損性に優れた鋳造用金型は、高Ｃ
ｒ鋼の表面に１〜３０μｍ厚さの酸化皮膜を形成させる
こととしている。そして、このようにすることで、溶湯
アルミニウム合金との反応が抑制され、溶損を軽減させ
ることができる。In order to achieve the above-mentioned object, a casting mold excellent in erosion resistance according to the present invention has a high C content.
An oxide film having a thickness of 1 to 30 μm is formed on the surface of the r steel. By doing so, the reaction with the molten aluminum alloy is suppressed, and erosion can be reduced.
【０００６】[0006]
【発明の実施の形態】本発明者らは、種々研究、実験を
行った結果、Ｃｒ含有量が８重量％以上の高Ｃｒ鋼に酸
化皮膜を形成させると、溶湯アルミニウム合金との反応
が抑制され、溶損が軽減されることを知見した。BEST MODE FOR CARRYING OUT THE INVENTION As a result of various studies and experiments, the present inventors have found that when an oxide film is formed on a high Cr steel having a Cr content of 8% by weight or more, the reaction with the molten aluminum alloy is suppressed. And found that erosion was reduced.
【０００７】すなわち、金型製作後、酸化処理を行え
ば、鋼中にＣｒを多量に含有している場合、酸化皮膜は
スピネル型の鉄−クロムの酸化物となる。この酸化皮膜
が、溶融アルミニウム合金との反応を抑制するので、溶
損が軽減するのである。[0007] That is, if oxidation treatment is performed after the mold is manufactured, if the steel contains a large amount of Cr, the oxide film becomes a spinel-type iron-chromium oxide. This oxide film suppresses the reaction with the molten aluminum alloy, so that the erosion is reduced.
【０００８】酸化処理としては、例えば５００〜７００
℃の温度範囲で、水蒸気、若しくは、水蒸気＋空気、或
いは、水蒸気＋窒素ガス雰囲気で１〜１０時間加熱す
る。こうすることにより、表面に酸化皮膜を形成させる
ことができる。[0008] As the oxidation treatment, for example, 500 to 700
In a temperature range of ° C., heating is performed for 1 to 10 hours in an atmosphere of steam, steam + air, or steam + nitrogen gas. By doing so, an oxide film can be formed on the surface.
【０００９】また、金型表面は使用中に約６００℃まで
昇温するために、表面に酸化皮膜が形成されるが、鋼中
にＣｒを多量に含有している場合、酸化処理と同様な鉄
−クロム複合酸化物が形成されるので、溶損が軽減す
る。この酸化皮膜の厚みは１μｍ未満では溶損に対して
効果が見られず、３０μｍを超えると酸化皮膜が基地よ
り剥離しやすくなり、やはり、溶損に対しての効果が低
下する。従って、本発明では、酸化皮膜の厚みは１〜３
０μｍとする。In addition, since the surface of the mold is heated up to about 600 ° C. during use, an oxide film is formed on the surface. However, when the steel contains a large amount of Cr, the same as in the oxidation treatment. Since an iron-chromium composite oxide is formed, erosion is reduced. When the thickness of the oxide film is less than 1 μm, no effect on erosion is observed, and when it exceeds 30 μm, the oxide film is easily peeled off from the base, and the effect on erosion is also reduced. Therefore, in the present invention, the thickness of the oxide film is 1 to 3
0 μm.
【００１０】一方、鋳造用金型は、溶損の他、耐熱亀裂
性と対溶損性を改善するため、高温強度及び延性、靱性
が要求される。しかし、Ｃｒ含有量が多くなると、高温
強度と靱性が低下するため、Ｃ、Ｃｒの最適な組合せに
ついて種々研究した結果、Ｃｒ量を増加させた場合には
Ｃ量を低減させることにより、また、Ｃｒ含有量が少な
い場合には、Ｃ量を多くすることにより、高温強度（耐
熱亀裂性）と靱性（破壊靱性値）の低下を抑制できるこ
とを知見した。On the other hand, a casting mold is required to have high-temperature strength, ductility, and toughness in order to improve heat crack resistance and erosion resistance in addition to erosion. However, when the Cr content increases, the high-temperature strength and the toughness decrease. Therefore, as a result of various studies on the optimal combination of C and Cr, when the Cr content is increased, the C content is reduced, It has been found that when the Cr content is small, a decrease in high-temperature strength (heat crack resistance) and toughness (fracture toughness) can be suppressed by increasing the C content.
【００１１】すなわち、耐熱亀裂性と靱性に対して、最
適なＣ、Ｃｒの組合せは図１に示されるように、 Ｃｒ＝１６±１−３０×〔Ｃ〕＋３０〔Ｃ〕2 但し、Ｃｒ：Ｃｒの重量％、 Ｃ：Ｃの重量％、 の範囲にあることを見出した。That is, the optimum combination of C and Cr for heat crack resistance and toughness is, as shown in FIG. 1, Cr = 16 ± 1-30 × [C] +30 [C] 2 where Cr: It was found that the weight percent of Cr was in the range of C: the weight percent of C.
【００１２】本発明の耐溶損性に優れた鋳造用金型は、
上記知見に加え、その他の元素の影響を調査した結果に
基づいて成されたものであり、重量％で、Ｃ：０．１〜
０．４％、Ｓｉ：０．１〜０．７％、Ｍｎ：０．１〜
１．５％、Ｃｒ：８．０〜１３．０％、Ａｌ：０．０１
〜３．０％、を含有し、残部はＦｅ及び不可避的不純物
からなる鋼、或いは、Ｃ：０．１〜０．４％、Ｓｉ：
０．１〜０．７％、Ｍｎ：０．１〜１．５％、Ｃｒ：
８．０〜１３．０％、Ａｌ：０．０１〜３．０％、Ｍ
ｏ：０．０１〜１．２％、Ｗ：０．１〜３．５％、Ｖ：
０．０５〜０．５％、Ｎｂ：０．００５〜０．２％、
Ｂ：０．０００１〜０．０２％、を含有し、残部はＦｅ
及び不可避的不純物からなる鋼の表面に１〜３０μｍ厚
さの鉄−クロムの酸化物層を形成させたことを要旨とす
るものであり、ＣｒとＣの含有量は、 Ｃｒ＝１６±１−３０×〔Ｃ〕＋３０〔Ｃ〕2 但し、Ｃｒ：Ｃｒの重量％、 Ｃ：Ｃの重量％、 とすることが望ましい。The casting mold excellent in erosion resistance of the present invention comprises:
In addition to the above findings, it was made based on the result of investigating the influence of other elements.
0.4%, Si: 0.1 to 0.7%, Mn: 0.1 to
1.5%, Cr: 8.0 to 13.0%, Al: 0.01
-3.0%, the balance being steel consisting of Fe and unavoidable impurities, or C: 0.1-0.4%, Si:
0.1-0.7%, Mn: 0.1-1.5%, Cr:
8.0-13.0%, Al: 0.01-3.0%, M
o: 0.01 to 1.2%, W: 0.1 to 3.5%, V:
0.05-0.5%, Nb: 0.005-0.2%,
B: 0.0001 to 0.02%, with the balance being Fe
And an iron-chromium oxide layer having a thickness of 1 to 30 μm is formed on the surface of steel consisting of unavoidable impurities. The content of Cr and C is as follows: Cr = 16 ± 1 30 × [C] +30 [C] 2 However, it is desirable that Cr: Cr weight% and C: C weight%.
【００１３】以下に、本発明の耐溶損性に優れた鋳造用
金型における成分組成を限定する理由について説明す
る。 Ｃ：Ｃはオーステナイト化安定元素であり、δフェライ
トの析出を抑制すると共に鋼の焼入性を向上し、Ｆｅ、
Ｃｒ、Ｍｏ、Ｖ、Ｎｂと炭化物を形成して、耐摩耗性、
焼戻し軟化抵抗、高温強度を向上させる。これらの作用
効果を確保するためには、０．１％以上添加することが
必要である。しかし、その含有量が０．４０％を超える
と、炭化物が過剰に析出して、高温強度、靱性を低下さ
せ、熱亀裂性を低下させる。そこで、本発明ではその含
有量を０．１〜０．４％とした。本発明者らの知見で
は、後述するＣｒ量に対する最適なＣ量は、Ｃｒ＝１６
±１−３０×〔Ｃ〕＋３０〔Ｃ〕2 の範囲である。The reason for limiting the component composition in the casting mold of the present invention having excellent erosion resistance will be described below. C: C is an austenitizing stable element that suppresses precipitation of δ ferrite and improves the hardenability of steel,
Form carbide with Cr, Mo, V, Nb, wear resistance,
Improves tempering softening resistance and high-temperature strength. In order to ensure these effects, it is necessary to add 0.1% or more. However, when the content exceeds 0.40%, carbides precipitate excessively, lowering high-temperature strength and toughness, and lowering thermal cracking properties. Therefore, in the present invention, the content is set to 0.1 to 0.4%. According to the findings of the present inventors, the optimum C amount with respect to the Cr amount described below is Cr = 16.
The range is ± 1−30 × [C] +30 [C] 2 .
【００１４】Ｓｉ：Ｓｉは耐酸化性を改善するが、多す
ぎると靱性を低下させるため、０．７％以下とする。し
かし、その含有量が０．１０％未満では添加効果に乏し
い。そこで、本発明ではその含有量を０．１〜０．７％
とした。Si: Although Si improves the oxidation resistance, if it is too much, the toughness is reduced. However, if the content is less than 0.10%, the effect of addition is poor. Therefore, in the present invention, the content is 0.1 to 0.7%
And
【００１５】Ｃｒ：Ｃｒは焼入性の向上、耐摩耗性の向
上に有効な元素である。しかし、金型表面に安定な酸化
皮膜を形成させるためには、８．０％以上の添加が必要
である。但し、１３．０％を越えるとδフェライトの生
成、高温強度の低下、靭性の低下をもたらし、耐熱亀裂
性が低下する。そこで、本発明ではその含有量を８．０
〜１３．０％とした。なお、ＣｒとＣの最適な組み合わ
せは先に説明した通りである。Cr: Cr is an element effective for improving hardenability and abrasion resistance. However, in order to form a stable oxide film on the mold surface, it is necessary to add 8.0% or more. However, if it exceeds 13.0%, the formation of δ ferrite, a decrease in high-temperature strength and a decrease in toughness are caused, and the heat crack resistance is reduced. Therefore, in the present invention, the content is set to 8.0.
１３13.0%. The optimum combination of Cr and C is as described above.
【００１６】Ａｌ：Ａｌは鋼の脱酸元素として作用する
と共に、安定な酸化皮膜の形成、オーステナイトの安定
化に寄与する。そして、これらの効果を得るためには、
０．０１％以上の添加が必要である。しかし、３．０％
を超えると、高温強度や靱性を低下させる。そのため、
本発明ではその含有量を０．０１〜３．０％とした。Al: Al acts as a deoxidizing element for steel and contributes to formation of a stable oxide film and stabilization of austenite. And to get these effects,
It is necessary to add 0.01% or more. However, 3.0%
If it exceeds, the high-temperature strength and toughness are reduced. for that reason,
In the present invention, the content is set to 0.01 to 3.0%.
【００１７】Ｍｏ：Ｍｏは高温強度、焼戻し軟化抵抗、
及び、耐摩耗性を向上させる作用を有する。しかし、そ
の含有量が０．０１％未満では添加効果が得られない。
一方、１．２％を超えるとδフェライトが生成して靱性
を低下させる。従って、本発明ではその含有量を０．０
１〜１．２％とした。Mo: Mo is high temperature strength, temper softening resistance,
And it has the effect of improving wear resistance. However, if the content is less than 0.01%, the effect of addition cannot be obtained.
On the other hand, if it exceeds 1.2%, δ ferrite is formed and the toughness is reduced. Therefore, in the present invention, the content is 0.0
1 to 1.2%.
【００１８】Ｗ：ＷはＭｏと同様に高温強度、焼戻し軟
化抵抗、及び、耐摩耗性を向上させる作用を有する。そ
して、前記作用はＭｏと複合添加した場合に、その効果
は著しい。しかし、０．１％未満ではＭｏと複合添加し
ても効果が小さい。一方、３．５％を超えるとδフェラ
イトが生成して靭性を低下させる。従って、本発明では
その含有量を０．１〜３．５％とした。望ましい下限は
０．８％である。W: Like Mo, W has the function of improving high-temperature strength, tempering softening resistance, and abrasion resistance. The effect is remarkable when Mo is added in combination with Mo. However, if it is less than 0.1%, the effect is small even if it is added in combination with Mo. On the other hand, when the content exceeds 3.5%, δ ferrite is formed and the toughness is reduced. Therefore, in the present invention, the content is set to 0.1 to 3.5%. A desirable lower limit is 0.8%.
【００１９】Ｖ：ＶはＣ、Ｎと微細な炭窒化物を析出さ
せ、高温強度と耐摩耗性を向上させると共に、結晶粒の
微細化に寄与する。しかし、その含有量が０．０５％未
満であるとその効果が乏しく、０．５％を超えると炭窒
化物が過剰に析出し、延性や靱性を低下させる。そこ
で、本発明ではその含有量を０．０５〜０．５％とし
た。望ましくは０．１〜０．３％である。V: V precipitates C and N and fine carbonitrides, improves high-temperature strength and wear resistance, and contributes to refinement of crystal grains. However, if the content is less than 0.05%, the effect is poor, and if it exceeds 0.5%, carbonitrides are excessively precipitated, and ductility and toughness are reduced. Therefore, in the present invention, the content is set to 0.05 to 0.5%. Desirably, it is 0.1 to 0.3%.
【００２０】Ｎｂ：ＮｂはＶと同様にＣ、Ｎと微細な炭
窒化物を析出させ、高温強度と耐摩耗性を向上させると
共に、結晶粒の微細化に寄与する。しかし、その含有量
が０．００５％未満であるとその効果が乏しく、０．２
％を超えると炭窒化物が過剰に析出し、延性や靭性を低
下させる。そこで、本発明ではその含有量を０．００５
〜０．２％とした。望ましくは０．０１〜０．２％であ
る。Nb: Like N, Nb precipitates C, N and fine carbonitrides, improves high-temperature strength and wear resistance, and contributes to refinement of crystal grains. However, if the content is less than 0.005%, the effect is poor, and 0.2%
%, Carbonitride precipitates excessively, and reduces ductility and toughness. Therefore, in the present invention, the content is 0.005.
０．２0.2%. Desirably, it is 0.01 to 0.2%.
【００２１】Ｂ：Ｂは微量の添加で炭化物を微細に分散
させ、かつ、その高温安定性を高めて高温強度を向上さ
せる。しかし、０．０００１％未満ではその効果が得ら
れない。一方、過剰に添加すると延性や靱性の低下をも
たらすので、本発明では、上限は０．０２％、望ましく
は０．００８％にする。B: B adds a small amount of carbide to finely disperse the carbide and enhances the high-temperature stability to improve the high-temperature strength. However, if less than 0.0001%, the effect cannot be obtained. On the other hand, if added in excess, the ductility and toughness are reduced, so in the present invention, the upper limit is made 0.02%, preferably 0.008%.
【００２２】本発明の鋳造用金型では、上記の成分のほ
か、残部はＦｅと不可避的な不純物である。この不純物
の含有量は特に規制しないが、不純物のうち、Ｐは０．
０２％以下、Ｓは０．００３％以下、Ｎは０．１％以下
とすることが望ましい。In the casting mold of the present invention, in addition to the above components, the balance is Fe and inevitable impurities. Although the content of this impurity is not particularly limited, among the impurities, P is set to 0.1.
It is preferable that the content of S is not more than 02%, the content of S is not more than 0.003%, and the content of N is not more than 0.1%.
【００２３】[0023]
【実施例】本発明の鋳造用金型の効果を実施例に基づい
て説明する。下記表１及び表２に示す成分組成の工具鋼
を高周波炉で溶解した後、鋳塊を据え込み及び鍛伸して
所定の寸法に鍛造した。鍛造温度はδフェライトが析出
しない１２００℃以下で加熱した。EXAMPLES The effects of the casting mold of the present invention will be described based on examples. After the tool steels having the component compositions shown in Tables 1 and 2 below were melted in a high-frequency furnace, the ingot was upset and forged to forge to predetermined dimensions. The forging temperature was heated to 1200 ° C. or less at which δ ferrite was not precipitated.
【００２４】表１（鋼種１から４２）は本発明の鋳造用
金型に採用する鋼、表２の鋼種６２、６３は従来から広
く用いられているＳＫＤ６１、表２の鋼種４３〜６３は
＊印を付した成分が本発明で規定する範囲から外れる比
較鋼である。これらの鍛造材を熱処理した後、所定の試
験片に機械加工した。Table 1 (steel types 1 to 42) shows steels used in the casting mold of the present invention, steel types 62 and 63 in Table 2 show SKD61 which has been widely used conventionally, and steel types 43 to 63 in Table 2 show *. This is a comparative steel in which the components marked out of the range specified in the present invention. After heat treatment of these forgings, they were machined into predetermined test pieces.
【００２５】焼入は１０００〜１０５０℃から油焼入を
施し、焼戻しは５２０〜５８０℃の空冷を２回繰り返し
た。各鋼種は硬さＨＲＣ４３に調整した。試験片を加工
後、５５０℃の水蒸気雰囲気中で１時間加熱し、酸化皮
膜を形成させた。なお、鋼種１６〜２１、鋼種３７〜３
９、鋼種５９及び６１は、前記した酸化処理を行わず
に、加工のままで試験に供した。Oil quenching was performed from 1000 to 1050 ° C., and air cooling at 520 to 580 ° C. was repeated twice for tempering. Each steel grade was adjusted to hardness HRC43. After processing the test piece, it was heated in a steam atmosphere at 550 ° C. for 1 hour to form an oxide film. In addition, steel type 16-21, steel type 37-3
9, steel types 59 and 61 were subjected to the test as they were, without performing the above-mentioned oxidation treatment.
【００２６】試験は溶融アルミニウム合金（材質ＡＤＣ
１０）による溶損試験、破壊靱性試験およびヒートチェ
ック試験を実施した。このうち、溶損試験は、７００℃
の溶湯温度の前記アルミニウム合金中に、２０×２０×
１００（ｍｍ）のサイズの試験片を浸漬し、上下動を５
時間繰り返すことにより耐溶損性を調査した。なお、耐
溶損性評価には次式で求めた値を用いた。求めた耐溶損
性は、値が小さいほど耐溶損性に優れることを意味して
いる。 耐溶損性（％／ｈ）＝（試験前の重量−試験後の重量）
／浸漬部の重量／試験時間The test was conducted on molten aluminum alloy (material ADC)
The erosion test, fracture toughness test and heat check test according to 10) were performed. Among them, the melting test was performed at 700 ° C.
20 × 20 ×
A test piece of 100 (mm) size was immersed,
The erosion resistance was investigated by repeating for a time. In addition, the value calculated | required by the following formula was used for evaluation of erosion resistance. The smaller the value of the obtained erosion resistance, the better the erosion resistance. Melting resistance (% / h) = (weight before test−weight after test)
/ Weight of immersion part / test time
【００２７】また、破壊靱性試験は、ＡＳＴＭ Ｅ３９
９−８３に準じて測定し、耐大割れ性の指標とした。求
めた破壊靱性値は大きいほど、耐大割れ性に優れること
を示す。The fracture toughness test was performed according to ASTM E39.
Measured according to 9-83, and used as an index for large crack resistance. The larger the obtained fracture toughness value, the better the large crack resistance.
【００２８】また、ヒートチェック試験は、直径が３５
ｍｍの試験片の表層部を誘導加熱して試験片の表面を６
００℃に加熱した後、直ちに常温まで水冷する操作（１
サイクル１５秒）を１０００回繰り返した。その後、試
験片を切断して断面を顕微鏡観察し、外周部に発生した
亀裂の最大深さを測定した。In the heat check test, the diameter was 35
Induction heating of the surface layer of the test piece of
After heating to 00 ° C, immediately water-cool to room temperature (1
(Cycle 15 seconds) was repeated 1000 times. Thereafter, the test piece was cut, the cross section was observed under a microscope, and the maximum depth of a crack generated in the outer peripheral portion was measured.
【００２９】表３及び表４に耐溶損性、耐熱亀裂性（最
大亀裂長さ）、耐大割れ性（破壊靱性値）を示す。表３
及び表４より明らかなように、本発明の鋳造用金型に採
用する鋼の耐熱亀裂性、耐大割れ性は従来鋼と同等であ
るが、耐溶損性は従来鋼及び比較鋼よりも著しく優れて
いる。従って、本発明の鋳造用金型に採用する鋼を実際
にダイカスト金型として使用した場合には、従来鋼およ
び比較鋼を採用した場合よりも長寿命となることが判
る。Tables 3 and 4 show erosion resistance, heat crack resistance (maximum crack length), and large crack resistance (fracture toughness). Table 3
As is clear from Table 4 and Table 4, the steel used in the casting mold of the present invention has the same heat crack resistance and large crack resistance as the conventional steel, but has a significantly higher erosion resistance than the conventional steel and the comparative steel. Are better. Therefore, it can be seen that when the steel employed in the casting mold of the present invention is actually used as a die casting mold, the life is longer than when the conventional steel and the comparative steel are employed.
【００３０】[0030]
【表１】 [Table 1]
【００３１】[0031]
【表２】 [Table 2]
【００３２】[0032]
【表３】 [Table 3]
【００３３】[0033]
【表４】 [Table 4]
【００３４】[0034]
【発明の効果】以上説明したように、本発明の鋳造用金
型は、溶融アルミニウム合金に対して優れた耐溶損性を
備えているので、耐溶損性が向上しその金型寿命を延ば
すことが可能である。As described above, since the casting mold of the present invention has excellent erosion resistance to a molten aluminum alloy, the erosion resistance is improved and the life of the mold is extended. Is possible.
【図１】耐熱亀裂性、靱性におよぼすＣｒ、Ｃ量の関係
を示した図である。FIG. 1 is a graph showing the relationship between Cr and C contents on heat crack resistance and toughness.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 近藤 邦夫 大阪府大阪市中央区北浜４丁目５番33号 住友金属工業株式会社内 Ｆターム(参考） 4E093 NB08 NB09 ────────────────────────────────────────────────── ─── Continued on the front page (72) Kunio Kondo, Inventor Sumitomo Metal Industries Co., Ltd. F-term (reference) 4-5-33 Kitahama, Chuo-ku, Osaka-shi, Osaka 4E093 NB08 NB09
Claims (3)
ｉ：０．１〜０．７％、Ｍｎ：０．１〜１．５％、Ｃ
ｒ：８．０〜１３．０％、Ａｌ：０．０１〜３．０％、
を含有し、残部はＦｅ及び不可避的不純物からなる鋼の
表面に１〜３０μｍ厚さの鉄−クロムの酸化物層を形成
させたことを特徴とする耐溶損性に優れた鋳造用金型。C .: 0.1 to 0.4% by weight, S
i: 0.1 to 0.7%, Mn: 0.1 to 1.5%, C
r: 8.0 to 13.0%, Al: 0.01 to 3.0%,
A casting mold excellent in erosion resistance, characterized in that an iron-chromium oxide layer having a thickness of 1 to 30 [mu] m is formed on the surface of steel consisting of Fe and unavoidable impurities.
ｉ：０．１〜０．７％、Ｍｎ：０．１〜１．５％、Ｃ
ｒ：８．０〜１３．０％、Ａｌ：０．０１〜３．０％、
Ｍｏ：０．０１〜１．２％、Ｗ：０．１〜３．５％、
Ｖ：０．０５〜０．５％、Ｎｂ：０．００５〜０．２
％、Ｂ：０．０００１〜０．０２％、を含有し、残部は
Ｆｅ及び不可避的不純物からなる鋼の表面に１〜３０μ
ｍ厚さの鉄−クロムの酸化物層を形成させたことを特徴
とする耐溶損性に優れた鋳造用金型。2. C: 0.1 to 0.4% by weight, S
i: 0.1 to 0.7%, Mn: 0.1 to 1.5%, C
r: 8.0 to 13.0%, Al: 0.01 to 3.0%,
Mo: 0.01 to 1.2%, W: 0.1 to 3.5%,
V: 0.05-0.5%, Nb: 0.005-0.2
%, B: 0.0001 to 0.02%, with the balance being 1 to 30 μm on the surface of steel consisting of Fe and unavoidable impurities.
A casting mold excellent in erosion resistance, wherein an iron-chromium oxide layer having a thickness of m is formed.
に優れた鋳造用金型。3. The content of Cr and C is as follows: Cr = 16 ± 1-30 × [C] +30 [C] 2 where Cr: wt% of Cr, C: wt% of C The casting mold having excellent erosion resistance according to claim 1 or 2.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03279999A JP4099888B2 (en) | 1999-02-10 | 1999-02-10 | Casting mold with excellent melt resistance |
| TW89116397A TW491904B (en) | 1999-02-10 | 2000-08-11 | A method of non-ferrous casting using a tool steel and casting components made from the tool steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03279999A JP4099888B2 (en) | 1999-02-10 | 1999-02-10 | Casting mold with excellent melt resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000234149A true JP2000234149A (en) | 2000-08-29 |
| JP4099888B2 JP4099888B2 (en) | 2008-06-11 |
Family
ID=12368905
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03279999A Expired - Fee Related JP4099888B2 (en) | 1999-02-10 | 1999-02-10 | Casting mold with excellent melt resistance |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JP4099888B2 (en) |
| TW (1) | TW491904B (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2015168859A (en) * | 2014-03-07 | 2015-09-28 | 大同特殊鋼株式会社 | Steel for mold |
| JP2019147179A (en) * | 2018-02-28 | 2019-09-05 | 株式会社デンソー | Mold device |
-
1999
- 1999-02-10 JP JP03279999A patent/JP4099888B2/en not_active Expired - Fee Related
-
2000
- 2000-08-11 TW TW89116397A patent/TW491904B/en not_active IP Right Cessation
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2015168859A (en) * | 2014-03-07 | 2015-09-28 | 大同特殊鋼株式会社 | Steel for mold |
| JP2019147179A (en) * | 2018-02-28 | 2019-09-05 | 株式会社デンソー | Mold device |
| WO2019167692A1 (en) * | 2018-02-28 | 2019-09-06 | 株式会社デンソー | Mold device |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4099888B2 (en) | 2008-06-11 |
| TW491904B (en) | 2002-06-21 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP6432070B2 (en) | Hot die steel for long-life die casting excellent in high-temperature thermal conductivity and method for producing the same | |
| JP5143531B2 (en) | Cold mold steel and molds | |
| JP7335680B2 (en) | Steel, products made from the steel, and methods for making the same | |
| JP4267260B2 (en) | Steel with excellent machinability | |
| JP5929963B2 (en) | Hardening method of steel | |
| JP5093010B2 (en) | Hot working mold | |
| JP5226083B2 (en) | High alloy cold die steel | |
| WO2007123164A1 (en) | Piston ring material for internal combustion engine | |
| JP3535112B2 (en) | Hot tool steel excellent in erosion resistance and high temperature strength and high temperature member made of the hot tool steel | |
| JP2020026567A (en) | Hot stamp die steel, hot stamp die and method for producing the same | |
| JP2000144334A (en) | Steel for aluminum diecasting die excellent in erosion resistance | |
| JP5061455B2 (en) | Hot die tool steel for aluminum die casting with reduced cracking from water-cooled holes | |
| JP2000226635A (en) | Hot tool steel excellent in high temperature strength and toughness | |
| JP3581028B2 (en) | Hot work tool steel and high temperature members made of the hot work tool steel | |
| JP4605695B2 (en) | Pre-hardened steel for die casting molds | |
| JP2001089826A (en) | Hot working tool steel excellent in wear resistance | |
| JP2001158937A (en) | Tool steel for hot working, method for producing same and method for producing tool for hot working | |
| JP3468126B2 (en) | Martensitic heat-resistant steel with excellent cold workability | |
| JP4099888B2 (en) | Casting mold with excellent melt resistance | |
| JP3238908B2 (en) | Die-cast steel with high ductility, cleanness and no formation of micro-band, and method for producing the same | |
| JP6359241B2 (en) | Corrosion-resistant plastic molding steel with excellent specularity | |
| JP2000297351A (en) | Steel for diecasting die and diecasting die | |
| JP2002060907A (en) | Steel and cast steel for hot press anvil | |
| JP4745017B2 (en) | Alloy steel for cold forging and wear resistance and method for producing the same | |
| JP4811637B2 (en) | Steel for die casting mold and die casting mold |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20050819 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20071004 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20080226 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20080310 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110328 Year of fee payment: 3 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120328 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130328 Year of fee payment: 5 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130328 Year of fee payment: 5 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130328 Year of fee payment: 5 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140328 Year of fee payment: 6 |
|
| LAPS | Cancellation because of no payment of annual fees |