JP2016172918A - Hypoeutectic spheroidal graphite cast iron - Google Patents
Hypoeutectic spheroidal graphite cast iron Download PDFInfo
- Publication number
- JP2016172918A JP2016172918A JP2015054631A JP2015054631A JP2016172918A JP 2016172918 A JP2016172918 A JP 2016172918A JP 2015054631 A JP2015054631 A JP 2015054631A JP 2015054631 A JP2015054631 A JP 2015054631A JP 2016172918 A JP2016172918 A JP 2016172918A
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- spheroidal graphite
- graphite
- graphite cast
- hypoeutectic
- 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
Abstract
Description
本発明は亜共晶球状黒鉛鋳鉄に関する。 The present invention relates to hypoeutectic spheroidal graphite cast iron.
一般に球状黒鉛鋳鉄は強度、靱性に寄与しない黒鉛を面積率で１０〜１３％程度含むため、鋼より機械的特性が劣る。ヤング率は鋼では２００〜２１０ＧＰａ、球状黒鉛鋳鉄では１４０〜１７０ＧＰａ程度である。
一方、炭素含有量を減らした亜共晶組成の球状黒鉛鋳鉄では、冷却時にデンドライトが先行して生じ易い。デンドライトが先行することで、残部液相にＭｎ等の炭化物安定化元素が濃化し、共晶セメンタイトができ易くなる。即ち、亜共晶組成の球状黒鉛鋳鉄は白鋳鉄化し易い傾向にある。このため従来は、鋳込み後に熱処理を行うことによって、組織中のセメンタイトを分解、黒鉛化して、組織を改善し、機械的特性を出すようにするのが一般的であった。
In general, spheroidal graphite cast iron contains about 10 to 13% by area of graphite that does not contribute to strength and toughness, and therefore is inferior in mechanical properties to steel. The Young's modulus is about 200 to 210 GPa for steel and about 140 to 170 GPa for spheroidal graphite cast iron.
On the other hand, in spheroidal graphite cast iron having a hypoeutectic composition with a reduced carbon content, dendrites are likely to occur prior to cooling. By leading the dendrite, a carbide stabilizing element such as Mn is concentrated in the remaining liquid phase, and eutectic cementite is easily formed. That is, spheroidal graphite cast iron having a hypoeutectic composition tends to be easily converted into white cast iron. For this reason, conventionally, heat treatment is performed after casting, so that cementite in the structure is decomposed and graphitized to improve the structure and exhibit mechanical properties.
上記特許文献１の発明は高剛性球状黒鉛鋳鉄及びその製造方法に関し、組織中の黒鉛量を減少させ、靱性、高ヤング率、０．２％耐力の向上の面で有利な、特に低温における靱性の向上に有利なものが開示されている。しかしながら、この発明は黒鉛化促進のために、ＢｉやＢａを添加している。Ｂｉ、Ｂａは少量で黒鉛の球状化を阻害する傾向をもたらす。
上記特許文献２の発明は高剛性球状黒鉛鋳鉄に関し、引け巣及びチルの発生を防止しながらヤング率の向上を図るものが開示されている。しかしながら、この発明では依然としてＣＥ値が高く、組織中の黒鉛量が多くなり、機械的特性が不十分となる問題が生じ得る。
上記特許文献３の発明は亜共晶球状黒鉛鋳鉄に関し、鋳放しのままでも強度、靱性および剛性に優れたものが開示されている。しかしながら特許文献１の発明では、高コストのＲＥＭ（希土類元素）、ＢＮ（窒化ホウ素）を黒鉛化促進、球状化促進に用いており、コストを重視する産業的生産には適さないという問題がある。
上記特許文献４の発明は高剛性球状黒鉛鋳鉄に関し、炭素当量（ＣＥ値）を低下させて、黒鉛晶出量を抑制し、ヤング率を高め、高剛性化を図るものが開示されている。しかしながら、この発明では、ＣＥ値が３．６〜４．２％の高い範囲では黒鉛の晶出量がかなり多くなり、機械的特性が期待できない。一方、ＣＥ値が２．８〜３．２％の低い範囲では、含有成分的からして、鋳放し状態で遊離セメンタイトを晶出させないのは難しく、そのままでは実製品に適用し難いという問題が残る。
The invention of Patent Document 1 relates to a high-rigid spheroidal graphite cast iron and a method for producing the same, which reduces the amount of graphite in the structure and is advantageous in terms of toughness, high Young's modulus, and 0.2% yield strength improvement, particularly toughness at low temperatures. What is advantageous to the improvement of is disclosed. However, in the present invention, Bi or Ba is added to promote graphitization. Bi and Ba tend to inhibit the spheroidization of graphite in a small amount.
The invention of Patent Document 2 relates to a high-rigid spheroidal graphite cast iron, which discloses an improvement in Young's modulus while preventing the formation of shrinkage cavities and chills. However, in the present invention, there is still a problem that the CE value is high, the amount of graphite in the structure increases, and the mechanical properties become insufficient.
The invention of Patent Document 3 relates to hypoeutectic spheroidal graphite cast iron, which is disclosed as having excellent strength, toughness and rigidity even when left as cast. However, in the invention of Patent Document 1, high-cost REM (rare earth element) and BN (boron nitride) are used for promoting graphitization and spheroidization, which is not suitable for industrial production with an emphasis on cost. .
The invention of Patent Document 4 relates to high-rigid spheroidal graphite cast iron, which discloses a technique for reducing the carbon equivalent (CE value), suppressing the amount of graphite crystallization, increasing the Young's modulus, and increasing the rigidity. However, in the present invention, when the CE value is in a high range of 3.6 to 4.2%, the amount of graphite crystallized becomes considerably large, and mechanical properties cannot be expected. On the other hand, in the range where the CE value is as low as 2.8 to 3.2%, it is difficult to crystallize free cementite in an as-cast state because of the content of components, and it is difficult to apply it to actual products as it is. Remains.
そこで本発明は上記従来の問題点を解消し、鋳放しのままで、遊離セメンタイトが晶出することなく、しかも晶出する黒鉛の面積率が小さく、黒鉛球状化率が高い、高ヤング率を有する亜共晶球状黒鉛鋳鉄の提供を課題とする。 Therefore, the present invention solves the above-mentioned conventional problems, and as it is as cast, free cementite does not crystallize, and the area ratio of the crystallized graphite is small, the graphite spheroidization ratio is high, and the high Young's modulus is high. An object is to provide hypoeutectic spheroidal graphite cast iron.
上記課題を解決する本発明の亜共晶球状黒鉛鋳鉄は、質量パーセントで、Ｃ：１．５〜２．７％、Ｓｉ：１．０〜３．０％、炭素当量：２．２〜３．４％、Ａｌ：０．０１〜０．２％、Ｍｇ：０．０１５〜０．０６０％を含有し、残部がＦｅからなる成分組成を有し、
基地中における黒鉛球状化率が８０％以上、黒鉛面積率が９％以下、ヤング率が１８０ＧＰａ以上であることを第１の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第１の特徴に加えて、質量パーセントで、Ｃ：１．５〜２．７％、Ｓｉ：１．０〜３．０％、炭素当量：２．２〜３．４％、Ａｌ：０．０１〜０．２％、Ｃｕ＋Ｎｉ：０．０１〜２．０％、Ｍｇ：０．０１５〜０．０６０％を含有し、残部がＦｅからなる成分組成を有することを第２の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第２の特徴に加えて、質量パーセントで、Ｃ：１．５〜２．７％、Ｓｉ：１．０〜３．０％、炭素当量：２．２〜３．４％、Ａｌ：０．０１〜０．２％、Ｎｉ：０．０１〜２．０％、Ｃｕ＋Ｎｉ：０．０１〜２．０％、Ｍｇ：０．０１５〜０．０６０％を含有し、残部がＦｅからなる成分組成を有することを第３の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第３の特徴に加えて、質量パーセントで、Ｃ：１．５〜２．７％、Ｓｉ：１．０〜３．０％、炭素当量：２．２〜３．４％、Ａｌ：０．０１〜０．２％、Ｎｉ：０．０５〜１．６％、Ｃｕ：０．０５〜１．６％、Ｃｕ＋Ｎｉ：０．１〜２．０％、Ｍｇ：０．０１５〜０．０６０％を含有し、残部がＦｅからなる成分組成を有することを第４の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第４の特徴に加えて、質量パーセントで、Ｃ：１．５〜２．７％、Ｓｉ：１．０〜３．０％、炭素当量：２．２〜３．４％、Ａｌ：０．０１〜０．２％、Ｎｉ：０．１〜１．２％、Ｃｕ：０．１〜１．２％、Ｃｕ＋Ｎｉ：０．２〜１．６％、Ｍｇ：０．０１５〜０．０６０％を含有し、残部がＦｅからなる成分組成を有することを第５の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第１〜第５の何れかの特徴に加えて、質量パーセントで、Ｃ：１．７〜２．５％、Ｓｉ：１．４〜２．６％、炭素当量：２．３〜３．０％とすることを第６の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第６の特徴に加えて、質量パーセントで、Ｃ：１．８〜２．３％、Ｓｉ：１．６〜２．４％、炭素当量：２．４〜２．７％とすることを第７の特徴としている。
また本発明の亜共晶球状黒鉛鋳鉄は、上記第１〜第７の何れかの特徴に加えて、質量パーセントで、Ｍｎ：１．０％未満とすることを第８の特徴としている。
The hypoeutectic spheroidal graphite cast iron of the present invention that solves the above problems is, by mass percent, C: 1.5-2.7%, Si: 1.0-3.0%, carbon equivalent: 2.2-3 .4%, Al: 0.01 to 0.2%, Mg: 0.015 to 0.060%, with the balance being composed of Fe,
The first feature is that the graphite spheroidization ratio in the base is 80% or more, the graphite area ratio is 9% or less, and the Young's modulus is 180 GPa or more.
Further, the hypoeutectic spheroidal graphite cast iron of the present invention has, in addition to the first feature, C: 1.5 to 2.7%, Si: 1.0 to 3.0%, and carbon equivalent: Contains 2.2 to 3.4%, Al: 0.01 to 0.2%, Cu + Ni: 0.01 to 2.0%, Mg: 0.015 to 0.060%, with the balance being Fe It has the 2nd characteristic to have a component composition.
Further, the hypoeutectic spheroidal graphite cast iron of the present invention has, in addition to the second feature, C: 1.5 to 2.7%, Si: 1.0 to 3.0%, and carbon equivalent: 2.2-3.4%, Al: 0.01-0.2%, Ni: 0.01-2.0%, Cu + Ni: 0.01-2.0%, Mg: 0.015-0. The third feature is that it has a component composition containing 060% and the balance being Fe.
The hypoeutectic spheroidal graphite cast iron of the present invention has, in addition to the third feature, C: 1.5 to 2.7%, Si: 1.0 to 3.0%, and carbon equivalent: 2.2-3.4%, Al: 0.01-0.2%, Ni: 0.05-1.6%, Cu: 0.05-1.6%, Cu + Ni: 0.1-2. The fourth feature is that it contains 0%, Mg: 0.015 to 0.060%, and the balance is composed of Fe.
Further, the hypoeutectic spheroidal graphite cast iron of the present invention has, in addition to the fourth feature, C: 1.5 to 2.7%, Si: 1.0 to 3.0%, and carbon equivalent: 2.2 to 3.4%, Al: 0.01 to 0.2%, Ni: 0.1 to 1.2%, Cu: 0.1 to 1.2%, Cu + Ni: 0.2 to 1. The fifth feature is that it contains 6%, Mg: 0.015 to 0.060%, and the balance is composed of Fe.
The hypoeutectic spheroidal graphite cast iron of the present invention has, in addition to any of the above first to fifth features, C: 1.7 to 2.5%, Si: 1.4 to 2.2. The sixth feature is that the carbon equivalent is 6% and 2.3 to 3.0%.
Further, the hypoeutectic spheroidal graphite cast iron of the present invention, in addition to the sixth feature, C: 1.8 to 2.3%, Si: 1.6 to 2.4%, carbon equivalent: The seventh feature is that the content is 2.4 to 2.7%.
Further, the hypoeutectic spheroidal graphite cast iron of the present invention is characterized in that, in addition to any one of the first to seventh features, the Mn is less than 1.0% by mass percent.
請求項１に記載の亜共晶球状黒鉛鋳鉄によれば、そこに示された成分組成により、現に、鋳放しのままで、遊離セメンタイトが晶出することなく、しかも晶出する黒鉛の面積率が小さく、黒鉛球状化率が高い、高ヤング率を有する実用に適した亜共晶球状黒鉛鋳鉄を提供することが可能となる。より具体的には、基地中における黒鉛球状化率が８０％以上で、黒鉛面積率が９％以下、ヤング率が１８０ＧＰａ以上の亜共晶球状黒鉛鋳鉄を鋳放し状態で得ることが可能となる。また鋳放し状態で引張り強さが６９０Ｎ／ｍｍ２以上とすることが可能となる。 According to the hypoeutectic spheroidal graphite cast iron according to claim 1, due to the component composition shown therein, the area ratio of the graphite that is actually crystallized without crystallization of free cementite as it is as cast. Thus, it is possible to provide hypoeutectic spheroidal graphite cast iron suitable for practical use having a small graphite, a high graphite spheroidization ratio, and a high Young's modulus. More specifically, hypoeutectic spheroidal graphite cast iron having a graphite spheroidization ratio in the base of 80% or more, a graphite area ratio of 9% or less, and a Young's modulus of 180 GPa or more can be obtained in an as-cast state. . Moreover, it becomes possible to make tensile strength into 690 N / mm < 2 > or more in the as-cast state.
また請求項２に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項１に記載の構成による作用効果に加えて、ＣｕとＮｉの何れか１つ若しくは両方を総量で０．０１〜２．０質量％含有させることにより、より黒鉛化の促進を図ることができ、容易に黒鉛の面積率が小さく黒鉛球状化率が高い、高ヤング率の亜共晶球状黒鉛鋳鉄を鋳放し状態で得ることが可能となる。
また請求項３に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項２に記載の構成による作用効果に加えて、Ｎｉを０．０１〜２．０質量％、ＣｕとＮｉの総量を０．０１〜２．０質量％とすることにより、より一層、黒鉛化の促進を図ることができ、確実に黒鉛面積率が小さく黒鉛球状化率が高い、高ヤング率の亜共晶球状黒鉛鋳鉄を鋳放し状態で得ることが可能となる。
また請求項４に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項３に記載の構成による作用効果に加えて、Ｎｉを０．０５〜１．６質量％、Ｃｕを０．０５〜１．６質量％、ＣｕとＮｉの総量を０．１〜２．０質量％とすることにより、更に一層、黒鉛化の促進を図ることができ、より確実に黒鉛面積率が低く黒鉛球状化率が高い、高ヤング率の亜共晶球状黒鉛鋳鉄を鋳放し状態で得ることが可能となる。
また請求項５に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項４に記載の構成による作用効果に加えて、Ｎｉを０．１〜１．２質量％、Ｃｕを０．１〜１．２質量％、ＣｕとＮｉの総量を０．２〜１．６質量％とすることにより、更により一層、黒鉛化の促進を図ることができ、更により確実に黒鉛面積率が小さく黒鉛球状化率が高い、高ヤング率の亜共晶球状黒鉛鋳鉄を鋳放し状態で得ることが可能となる。
Moreover, according to the hypoeutectic spheroidal graphite cast iron according to claim 2, in addition to the function and effect of the structure according to claim 1, 0.01 or 2 in total of any one or both of Cu and Ni is added. By containing 0.0% by mass, graphitization can be further promoted, and a hypoeutectic spheroidal graphite cast iron having a high Young's modulus and a high graphite spheroidization ratio can be easily obtained in an as-cast state. Can be obtained.
Moreover, according to the hypoeutectic spheroidal graphite cast iron according to claim 3, in addition to the function and effect of the configuration according to claim 2, Ni is 0.01 to 2.0 mass%, and the total amount of Cu and Ni is By setting the content to 0.01 to 2.0% by mass, graphitization can be further promoted, and the high eutectic spheroidal graphite having a small graphite area ratio and a high graphite spheroidization ratio is ensured. It becomes possible to obtain cast iron in an as-cast state.
According to the hypoeutectic spheroidal graphite cast iron according to claim 4, in addition to the operational effects of the configuration according to claim 3, 0.05 to 1.6 mass% of Ni and 0.05 to By making the total amount of 1.6% by mass and Cu and Ni 0.1 to 2.0% by mass, the graphitization can be further promoted, and the graphite area ratio is more reliably reduced and the graphite spheroidized. It is possible to obtain hypoeutectic spheroidal graphite cast iron having a high rate and high Young's modulus in an as-cast state.
Moreover, according to the hypoeutectic spheroidal graphite cast iron according to claim 5, in addition to the operational effect of the configuration according to claim 4, 0.1 to 1.2 mass% of Ni and 0.1 to Cu of 0.1 to By making the total amount of 1.2% by mass and Cu and Ni 0.2 to 1.6% by mass, the graphitization can be further promoted, and the graphite area ratio is further reliably reduced. It becomes possible to obtain hypoeutectic spheroidal graphite cast iron having a high spheroidization rate and a high Young's modulus in an as-cast state.
また請求項６に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項１〜５の何れかに記載の構成による作用効果に加えて、Ｃを１．７〜２．５質量％、Ｓｉを１．４〜２．６質量％、炭素当量を２．３〜３．０質量％とすることで、基地中の黒鉛面積率が低く、黒鉛球状化率の高い、より高ヤング率の亜共晶球状黒鉛鋳鉄を、より確実に鋳放し状態で得ることが可能となる。
また請求項７に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項６に記載の構成による作用効果に加えて、Ｃを１．８〜２．３質量％、Ｓｉを１．６〜２．４質量％、炭素当量を２．４〜２．７質量％とすることで、基地中の黒鉛面積率が低く、黒鉛球状化率の高い、より高ヤング率の高い亜共晶球状黒鉛鋳鉄を、更により確実に鋳放し状態で得ることが可能となる。
また請求項８に記載の亜共晶球状黒鉛鋳鉄によれば、上記請求項１〜７に何れかに記載の構成による作用効果に加えて、Ｍｎを１．０質量％未満とすることで、共晶セメンタイトの晶出を抑制することができ、鋳放し状態での黒鉛化を促進することができる。
Moreover, according to the hypoeutectic spheroidal graphite cast iron according to claim 6, in addition to the function and effect of the structure according to any one of claims 1 to 5, C is 1.7 to 2.5 mass%, Si Is 1.4 to 2.6 mass% and the carbon equivalent is 2.3 to 3.0 mass%, so that the graphite area ratio in the base is low, the graphite spheroidization ratio is high, and the higher Young's modulus It becomes possible to obtain eutectic spheroidal graphite cast iron more reliably in an as-cast state.
Moreover, according to the hypoeutectic spheroidal graphite cast iron according to claim 7, in addition to the operational effect of the structure according to claim 6, C is 1.8 to 2.3 mass%, Si is 1.6 to Hypoeutectic spheroidal graphite having a low graphite area ratio in the matrix, a high graphite spheroidization ratio, and a higher high Young's modulus by making 2.4 mass% and carbon equivalent 2.4 to 2.7 mass%. It becomes possible to obtain cast iron in an as-cast state even more reliably.
Moreover, according to the hypoeutectic spheroidal graphite cast iron according to claim 8, in addition to the function and effect by the configuration according to any one of claims 1 to 7, by making Mn less than 1.0 mass%, Crystallization of eutectic cementite can be suppressed, and graphitization in an as-cast state can be promoted.
本発明の亜共晶球状黒鉛鋳鉄について、使用する鋳鉄材料の成分組成における各成分元素の含有範囲について、以下に説明する。なお、以下において各成分の含有量は質量％で記載する。 About the hypoeutectic spheroidal graphite cast iron of this invention, the containing range of each component element in the component composition of the cast iron material to be used is demonstrated below. In addition, below, content of each component is described in the mass%.
Ｃの含有量は、１．５〜２．７％とする。
亜共晶鋳鉄としては、Ｃの含有量は前提として４．３％未満ということになるが、Ｃの含有量が多くなりすぎると、黒鉛面積率が増加して、機械的特性が劣る。このためＣの含有量は２．７％以下とする。
Ｃの含有量が２．７％を超えると、基地中の黒鉛の量が多く、黒鉛面積率が９％を超え易く、機械的特性としてヤング率が１８０ＧＰａ未満、引張り強さが６００Ｎ／ｍｍ２未満となり易い。Ｃの含有量が１．５％未満では、黒鉛が晶出し難くなり、初析セメンタイトが生成する。
Ｃの含有量は、得られる亜共晶球状黒鉛鋳鉄が黒鉛球状化率８０％以上、黒鉛面積率が９％以下、引張り強さが６９０Ｎ／ｍｍ２以上、ヤング率が１８０ＧＰａ以上となることを考慮して、１．７〜２．５％が好ましく、更に好ましくは１．８〜２．３％とするのがよい。
The content of C is 1.5 to 2.7%.
As hypoeutectic cast iron, the C content is supposed to be less than 4.3%, but if the C content is too large, the graphite area ratio increases and the mechanical properties are inferior. Therefore, the C content is 2.7% or less.
When the content of C exceeds 2.7%, the amount of graphite in the base is large, the graphite area ratio tends to exceed 9%, Young's modulus is less than 180 GPa as mechanical properties, and tensile strength is 600 N / mm 2. It tends to be less than. If the C content is less than 1.5%, graphite is difficult to crystallize and proeutectoid cementite is generated.
The content of C indicates that the obtained hypoeutectic spheroidal graphite cast iron has a graphite spheroidization rate of 80% or more, a graphite area ratio of 9% or less, a tensile strength of 690 N / mm 2 or more, and a Young's modulus of 180 GPa or more. Considering it, 1.7 to 2.5% is preferable, and 1.8 to 2.3% is more preferable.
Ｓｉの含有量は、１．０〜３．０％とする。
Ｓｉは強い黒鉛化作用があり、Ｃの１／３程度の割合で状態図を低Ｃ側に動かす。１．０％未満では黒鉛化作用が十分発揮しない。３．０％を超えると、フェライト基地に固溶し、靱性を下げる。
Ｓｉの含有量は、Ｃの黒鉛化促進と基地への固溶（靱性の低下）を考慮して、１．４〜２．６％が好ましく、更に好ましくは１．６〜２．４％とするのがよい。
The Si content is set to 1.0 to 3.0%.
Si has a strong graphitizing action, and moves the phase diagram to the low C side at a rate of about 1/3 of C. If it is less than 1.0%, the graphitization effect is not sufficiently exhibited. If it exceeds 3.0%, it will dissolve in the ferrite matrix and lower the toughness.
The content of Si is preferably 1.4 to 2.6%, more preferably 1.6 to 2.4% in consideration of C graphitization promotion and solid solution in the base (decrease in toughness). It is good to do.
炭素当量（ＣＥ値）は、２．２〜３．４％とする。
炭素当量は、これが高いと黒鉛の晶出量が多くなり、機械的特性が低下する。一方、少ないと遊離セメンタイトが晶出し易く、白鋳鉄化する。２．２％未満では鋳放しで白鋳鉄化し、実用に供せない。３．４％を超えると、黒鉛の晶出量が多く、ヤング率を１８０ＧＰａにするのが難しくなる。また引張り強さが６９０Ｎ／ｍｍ２を超えるのが難しくなる。
炭素当量は、得られる亜共晶球状黒鉛鋳鉄が黒鉛球状化率８０％以上、黒鉛面積率が９％以下、引張り強さが６９０Ｎ／ｍｍ２以上、ヤング率が１８０ＧＰａ以上となることを考慮して、２．３〜３．０％が好ましく、更に好ましくは２．４〜２．７％とするのがよい。
なお炭素当量（ＣＥ値）は、例えばＣＥ＝Ｃ％＋（１／３）・Ｓｉ％として、簡易演算することができる。本発明では、原則としてＣＥ＝Ｃ％＋（１／３）・Ｓｉ％として演算している。
勿論、前記Ｃ、Ｓｉ以外の成分元素、不純物元素が含まれる場合には、それら成分元素、不純物元素についての炭素当量を加算、減算して総炭素当量を演算し、これを炭素当量としてもよい。
The carbon equivalent (CE value) is 2.2 to 3.4%.
If the carbon equivalent is high, the amount of graphite crystallized increases, and the mechanical properties deteriorate. On the other hand, when the amount is small, free cementite is easily crystallized and white cast iron is formed. If it is less than 2.2%, it is cast as white cast iron and cannot be put to practical use. If it exceeds 3.4%, the amount of crystallization of graphite is large, and it becomes difficult to make the Young's modulus 180 GPa. Moreover, it becomes difficult for the tensile strength to exceed 690 N / mm 2 .
The carbon equivalent is considered considering that the obtained hypoeutectic spheroidal graphite cast iron has a graphite spheroidization ratio of 80% or more, a graphite area ratio of 9% or less, a tensile strength of 690 N / mm 2 or more, and a Young's modulus of 180 GPa or more. 2.3 to 3.0% is preferable, and 2.4 to 2.7% is more preferable.
The carbon equivalent (CE value) can be simply calculated as, for example, CE = C% + (1/3) · Si%. In the present invention, in principle, the calculation is performed as CE = C% + (1/3) · Si%.
Of course, when component elements other than C and Si and impurity elements are included, the carbon equivalents of these component elements and impurity elements are added and subtracted to calculate the total carbon equivalent, which may be used as the carbon equivalent. .
Ａｌの含有量は、０．０１〜０．２％とする。
本発明では、Ａｌを添加、含有させるのが１つの特徴である。
ＡｌはＳｉと同様に、強い黒鉛化促進作用がある。また溶湯中の窒素濃度を下げ、セメンタイトの発生を抑制する作用がある。しかし０．２％以上添加すると、湯流れが悪くなる。また０．０１％未満では効果が薄い。
The Al content is set to 0.01 to 0.2%.
In the present invention, one feature is that Al is added and contained.
Al, like Si, has a strong graphitization promoting effect. It also has the effect of reducing the nitrogen concentration in the molten metal and suppressing the generation of cementite. However, if 0.2% or more is added, the hot water flow becomes worse. If the content is less than 0.01%, the effect is weak.
Ｎｉは黒鉛化促進作用がある。またフェライトに固溶して、基地を強化する作用がある。よって必須ではないが、含有させるのがよい。
Ｎｉを含有させる場合は、０．０１〜２．０％とする。２．０％を超えるとフェライト基地の脆化につながる。０．０１％未満では効果が薄い。
Ｎｉの含有量は、黒鉛化促進作用、基地強化作用、フェライト基地の脆化作用を考慮して、０．０５〜１．６％がより好ましく、更には０．１〜１．２％が最も好ましい。
Ni has a graphitization promoting action. It also has the effect of strengthening the base by dissolving in ferrite. Therefore, although it is not essential, it is good to contain.
When Ni is contained, the content is set to 0.01 to 2.0%. If it exceeds 2.0%, it will lead to embrittlement of the ferrite base. Less than 0.01% is less effective.
The Ni content is more preferably 0.05 to 1.6%, and most preferably 0.1 to 1.2% in consideration of the graphitization promoting effect, the matrix strengthening effect, and the brittleness effect of the ferrite matrix. preferable.
Ｃｕは黒鉛化促進作用がある。またパーライトのラメラ間隔を密にして、耐力を向上させる。よって必須ではないが、含有させるのがよい。
Ｃｕを含有させる場合は、０．０１〜２．０％とする。２．０％を超えるとパーライト基地を脆化し、靱性が低下し、また黒鉛球状化を阻害する。０．０１％未満では効果が薄い。
Ｃｕの含有量は、黒鉛化促進作用、耐力向上作用、パーライト基地の脆化作用、黒鉛球状化阻害作用を考慮して、０．０５〜１．６％がより好ましく、更には０．１〜１．２％が最も好ましい。
Cu has a graphitization promoting action. In addition, the pearlite lamella spacing is increased to improve the yield strength. Therefore, although it is not essential, it is good to contain.
When Cu is contained, the content is 0.01 to 2.0%. If it exceeds 2.0%, the pearlite matrix becomes brittle, the toughness is lowered, and graphite spheroidization is inhibited. Less than 0.01% is less effective.
The content of Cu is more preferably 0.05 to 1.6% in consideration of the graphitization promoting effect, the yield strength improving effect, the embrittlement effect of the pearlite base, and the graphite spheroidization inhibiting effect, and further 0.1 to 0.1%. 1.2% is most preferred.
なおＮｉとＣｕは何れも黒鉛化促進作用がある点で共通する。その合計、即ちＮｉ＋Ｃｕの合計としての含有は必須ではないが、上記ＮｉやＣｕの含有に伴って、Ｎｉ＋Ｃｕの合計量としても含有させることになる。但し、Ｎｉ＋Ｃｕの合計量としては、０．０１〜２．０％とする。０．０１％未満では黒鉛化促進効果が薄い。また２．０％を超えると基地の脆化につながる。
Ｎｉ＋Ｃｕの合計含有量は、黒鉛化促進作用、耐力向上作用、基地の強化と脆化の作用、黒鉛球状化阻害作用を考慮して、０．１〜２．０％がより好ましく、更には０．２〜１．６％が最も好ましい。
Both Ni and Cu are common in that they have a graphitization promoting action. Although the total content, that is, the total content of Ni + Cu is not essential, the total content of Ni + Cu is included with the content of Ni and Cu. However, the total amount of Ni + Cu is 0.01 to 2.0%. If it is less than 0.01%, the graphitization promoting effect is small. If it exceeds 2.0%, the base will become brittle.
The total content of Ni + Cu is more preferably 0.1 to 2.0% in consideration of graphitization promoting action, yield strength improving action, base strengthening and embrittlement action, and graphite spheroidization inhibiting action, and further 0 .2 to 1.6% is most preferable.
Ｍｇは黒鉛の球状化に用いる。
Ｍｇの含有量は０．０１５〜０．０６０％とする。
Ｍｇは溶湯中で気化し、その気泡中にＣが拡散して、球状黒鉛が生成されるため必須である。０．０６０％を超えると、Ｍｇによる炭化物促進作用が働き、好ましくない。０．０１５％未満では、黒鉛が自由に成長して片状になり易いので、好ましくない。
Mg is used for spheroidizing graphite.
The Mg content is 0.015 to 0.060%.
Mg is essential because it vaporizes in the molten metal and C diffuses into the bubbles to produce spherical graphite. If it exceeds 0.060%, the carbide promoting action by Mg works, which is not preferable. If it is less than 0.015%, the graphite tends to grow freely into a piece, which is not preferable.
Ｍｎは炭化物を安定化するので好ましくなく、含有させないのが原則である。ただし原料の鉄屑から混入する。混入量を１．０％未満にするのが好ましい。より好ましくは０．５％未満とするのが良い。
またＰやＳは、実際の製品では不純物として含有され得るが、本発明ではそれらの不純物は含有させる対象ではない。
Since Mn stabilizes the carbide, Mn is not preferable, and in principle, Mn is not included. However, it is mixed from raw iron scrap. The mixing amount is preferably less than 1.0%. More preferably, it is less than 0.5%.
Further, P and S can be contained as impurities in an actual product, but these impurities are not included in the present invention.
Ｆｅの含有量は、１００％から各含有元素の含有量（％）を差し引いた残部となる。 The content of Fe is the balance obtained by subtracting the content (%) of each contained element from 100%.
なお黒鉛化促進のため、Ｚｒ、Ｃａ、Ｂａ等を含有する接種剤を溶湯に添加するようにしてもよい。 In order to accelerate graphitization, an inoculum containing Zr, Ca, Ba or the like may be added to the molten metal.
本発明の亜共晶球状黒鉛鋳鉄は、例えば、原料となる各材料を亜共晶組成となるようにして、溶解炉に入れ、１３５０〜１５５０℃で溶解し、その後１５５０℃で取鍋に移して球状化処理を行い、１４５０℃で鋳型に鋳込むことで製造することができる。Ａｌは溶解後に溶湯に添加する。また必要に応じて、Ｚｒ、Ｃａ、Ｂａ等を含有する接種剤を鋳込み直前に添加することができる。
上記によって、鋳放し状態で亜共晶球状黒鉛鋳鉄を現に製造することができる。
The hypoeutectic spheroidal graphite cast iron of the present invention is, for example, placed in a melting furnace so that each raw material has a hypoeutectic composition, melted at 1350 to 1550 ° C., and then transferred to a ladle at 1550 ° C. Can be produced by spheroidizing and casting into a mold at 1450 ° C. Al is added to the molten metal after melting. If necessary, an inoculum containing Zr, Ca, Ba or the like can be added immediately before casting.
By the above, hypoeutectic spheroidal graphite cast iron can actually be produced in an as-cast state.
原則として、後処理としての熱処理は不要であるが、更に良好な組織、機械的特性を得るために、熱処理を後処理として施すことも可能である。
後処理としての熱処理は、例えば６００〜９００℃で一定時間保持し、その後徐冷する、いわゆるフェライト化焼鈍を行うことができる。このフェライト化焼鈍をすることで、パーライトを分解し、例えば後述の実施例２に示したように、伸びを例えば７％以上とする等、伸びを適当に増加させ、一方、引張り強度を適当に減少させる等の、引張り強度と伸びのバランス調整を行うことができる。ただし、そのようなフェライト化焼鈍処理を施しても、ヤング率は低下することがない。
In principle, a heat treatment as a post-treatment is not necessary, but a heat treatment can be applied as a post-treatment in order to obtain better structure and mechanical properties.
The heat treatment as the post-treatment can be performed, for example, so-called ferrite annealing, which is held at 600 to 900 ° C. for a certain time and then gradually cooled. By this ferritic annealing, the pearlite is decomposed and, for example, as shown in Example 2 described later, the elongation is appropriately increased, for example, the elongation is set to 7% or more, while the tensile strength is appropriately adjusted. It is possible to adjust the balance between the tensile strength and the elongation, for example, by reducing it. However, the Young's modulus does not decrease even when such a ferritic annealing treatment is performed.
実施例１〜６、比較例１の各鋳鉄材料を、電気炉で１３５０〜１５５０℃で約１時間溶融し、これを約１５５０℃で取鍋に移した後、約１４５０℃で、鋳型に鋳造した。得られた鋳放し鋳鉄の成分組成と炭素当量（ＣＥ値：Ｃ＋１／３・Ｓｉ）を表１に示す。
なお実施例２においては、鋳造後、９００℃で１時間、焼なましを行った。
また比較例２として、特開２０１３−１７３９６９号公報に開示された実施例８の成分組成を表１に併せて示す。比較例２はＡｌを含有していない点で、本発明と本質的に異なる。
更に実施例１〜６、比較例１〜２について、黒鉛面積率（％）、球状化率（％）、黒鉛粒数（個／ｍｍ２）、０．２％耐力（Ｎ／ｍｍ２）、引張り強さ（Ｎ／ｍｍ２）、伸び（％）、ヤング率（ＧＰａ）を測定した。結果を表１に示す。
The cast iron materials of Examples 1 to 6 and Comparative Example 1 were melted in an electric furnace at 1350 to 1550 ° C for about 1 hour, transferred to a ladle at about 1550 ° C, and then cast into a mold at about 1450 ° C. did. Table 1 shows the component composition and carbon equivalent (CE value: C + 1/3 · Si) of the as-cast iron obtained.
In Example 2, after casting, annealing was performed at 900 ° C. for 1 hour.
In addition, as Comparative Example 2, the component composition of Example 8 disclosed in JP2013-173969A is also shown in Table 1. Comparative Example 2 is essentially different from the present invention in that it does not contain Al.
Further, for Examples 1 to 6 and Comparative Examples 1 and 2, the graphite area ratio (%), the spheroidization ratio (%), the number of graphite particles (pieces / mm 2 ), the 0.2% proof stress (N / mm 2 ), Tensile strength (N / mm 2 ), elongation (%), and Young's modulus (GPa) were measured. The results are shown in Table 1.
表１より明らかなように、鋳放し状態の実施例１、３〜６において、黒鉛面積率３．９５〜７．０４％、球状化率８８．７〜９０．４％、０．２％耐力３７５．４〜５０６．４Ｎ／ｍｍ２、引張り強さ６９８．８〜８４８．１Ｎ／ｍｍ２、ヤング率１８３．４〜１９８．１ＧＰａであった。
これに対して比較例１では、Ｃの含有量、炭素当量（ＣＥ値）が過剰であり、また黒鉛面積率が９．２６％と過剰で、球状化率が８５．６％、０．２％耐力が３３４．０Ｎ／ｍｍ２、引張り強さが５５２．６Ｎ／ｍｍ２、ヤング率が１７８．０ＧＰａで何れも低調であった。
また比較例２では、黒鉛面積率、球状化率、０．２％耐力は不明である。一方、引張り強さが６８４．８Ｎ／ｍｍ２と本発明に比べてかなり低い。またヤング率は１８３．０ＧＰａで、１８０ＧＰａを超えるが、本発明と比べて低いと言える。
また実施例２では、鋳造後に焼きなましを行うことで、ヤング率が大きいまま、引張り強度を若干低下させるも、７００Ｎ／ｍｍ２以上を保持しつつ、伸びを７．０％以上（７．６８％）にすることができた。またヤング率は高いまま保持することができた。
As apparent from Table 1, in Examples 1 and 3 to 6 in the as-cast state, the graphite area ratio was 3.95 to 7.04%, the spheroidization ratio was 88.7 to 90.4%, and 0.2% proof stress. They were 375.4-506.4N / mm < 2 >, tensile strength 698.8-848.1N / mm < 2 >, and Young's modulus 183.4-198.1GPa.
In contrast, in Comparative Example 1, the C content and carbon equivalent (CE value) are excessive, the graphite area ratio is excessive at 9.26%, and the spheroidization ratio is 85.6%, 0.2. The% yield strength was 334.0 N / mm 2 , the tensile strength was 552.6 N / mm 2 , and the Young's modulus was 178.0 GPa.
In Comparative Example 2, the graphite area ratio, spheroidization ratio, and 0.2% yield strength are unknown. On the other hand, the tensile strength is 684.8 N / mm 2 , which is considerably lower than that of the present invention. The Young's modulus is 183.0 GPa and exceeds 180 GPa, but it can be said to be lower than that of the present invention.
Also, in Example 2, annealing was performed after casting, and while the Young's modulus was large, the tensile strength was slightly reduced, but the elongation was 7.0% or more (7.68% while maintaining 700 N / mm 2 or more. ) Also, the Young's modulus could be kept high.
Claims (8)
Ｃ ：１．５〜２．７％
Ｓｉ ：１．０〜３．０％
炭素当量 ：２．２〜３．４％
Ａｌ ：０．０１〜０．２％
Ｍｇ ：０．０１５〜０．０６０％
を含有し、残部がＦｅからなる成分組成を有し、
基地中における黒鉛球状化率が８０％以上、黒鉛面積率が９％以下、ヤング率が１８０ＧＰａ以上であることを特徴とする亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.5 to 2.7%
Si: 1.0-3.0%
Carbon equivalent: 2.2-3.4%
Al: 0.01 to 0.2%
Mg: 0.015-0.060%
And the balance has a component composition consisting of Fe,
A hypoeutectic spheroidal graphite cast iron having a graphite spheroidization rate of 80% or more, a graphite area ratio of 9% or less, and a Young's modulus of 180 GPa or more.
Ｃ ：１．５〜２．７％
Ｓｉ ：１．０〜３．０％
炭素当量 ：２．２〜３．４％
Ａｌ ：０．０１〜０．２％
Ｃｕ＋Ｎｉ ：０．０１〜２．０％
Ｍｇ ：０．０１５〜０．０６０％
を含有し、残部がＦｅからなる成分組成を有することを特徴とする請求項１に記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.5 to 2.7%
Si: 1.0-3.0%
Carbon equivalent: 2.2-3.4%
Al: 0.01 to 0.2%
Cu + Ni: 0.01 to 2.0%
Mg: 0.015-0.060%
2. The hypoeutectic spheroidal graphite cast iron according to claim 1, having a component composition in which the balance is made of Fe.
Ｃ ：１．５〜２．７％
Ｓｉ ：１．０〜３．０％
炭素当量 ：２．２〜３．４％
Ａｌ ：０．０１〜０．２％
Ｎｉ ：０．０１〜２．０％
Ｃｕ＋Ｎｉ ：０．０１〜２．０％
Ｍｇ ：０．０１５〜０．０６０％
を含有し、残部がＦｅからなる成分組成を有することを特徴とする請求項２に記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.5 to 2.7%
Si: 1.0-3.0%
Carbon equivalent: 2.2-3.4%
Al: 0.01 to 0.2%
Ni: 0.01 to 2.0%
Cu + Ni: 0.01 to 2.0%
Mg: 0.015-0.060%
3. The hypoeutectic spheroidal graphite cast iron according to claim 2, which has a component composition in which the balance is made of Fe.
Ｃ ：１．５〜２．７％
Ｓｉ ：１．０〜３．０％
炭素当量 ：２．２〜３．４％
Ａｌ ：０．０１〜０．２％
Ｎｉ ：０．０５〜１．６％
Ｃｕ ：０．０５〜１．６％
Ｃｕ＋Ｎｉ ：０．１〜２．０％
Ｍｇ ：０．０１５〜０．０６０％
を含有し、残部がＦｅからなる成分組成を有することを特徴とする請求項３に記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.5 to 2.7%
Si: 1.0-3.0%
Carbon equivalent: 2.2-3.4%
Al: 0.01 to 0.2%
Ni: 0.05-1.6%
Cu: 0.05 to 1.6%
Cu + Ni: 0.1-2.0%
Mg: 0.015-0.060%
4. The hypoeutectic spheroidal graphite cast iron according to claim 3, wherein the hypoeutectic spheroidal graphite cast iron has a component composition in which the balance is Fe.
Ｃ ：１．５〜２．７％
Ｓｉ ：１．０〜３．０％
炭素当量 ：２．２〜３．４％
Ａｌ ：０．０１〜０．２％
Ｎｉ ：０．１〜１．２％
Ｃｕ ：０．１〜１．２％
Ｃｕ＋Ｎｉ ：０．２〜１．６％
Ｍｇ ：０．０１５〜０．０６０％
を含有し、残部がＦｅからなる成分組成を有することを特徴とする請求項４に記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.5 to 2.7%
Si: 1.0-3.0%
Carbon equivalent: 2.2-3.4%
Al: 0.01 to 0.2%
Ni: 0.1-1.2%
Cu: 0.1-1.2%
Cu + Ni: 0.2 to 1.6%
Mg: 0.015-0.060%
5. The hypoeutectic spheroidal graphite cast iron according to claim 4, wherein the iron eutectic has a component composition consisting of Fe and the balance being Fe.
Ｃ ：１．７〜２．５％
Ｓｉ ：１．４〜２．６％
炭素当量 ：２．３〜３．０％
とすることを特徴とする請求項１〜５の何れかに記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.7-2.5%
Si: 1.4-2.6%
Carbon equivalent: 2.3-3.0%
The hypoeutectic spheroidal graphite cast iron according to any one of claims 1 to 5.
Ｃ ：１．８〜２．３％
Ｓｉ ：１．６〜２．４％
炭素当量 ：２．４〜２．７％
とすることを特徴とする請求項６に記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
C: 1.8 to 2.3%
Si: 1.6-2.4%
Carbon equivalent: 2.4-2.7%
The hypoeutectic spheroidal graphite cast iron according to claim 6.
Ｍｎ ：１．０％未満
とすることを特徴とする請求項１〜７の何れかに記載の亜共晶球状黒鉛鋳鉄。 In weight percent,
The hypoeutectic spheroidal graphite cast iron according to any one of claims 1 to 7, wherein Mn: less than 1.0%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015054631A JP6548924B2 (en) | 2015-03-18 | 2015-03-18 | Hypoeutectic spheroidal graphite cast iron |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015054631A JP6548924B2 (en) | 2015-03-18 | 2015-03-18 | Hypoeutectic spheroidal graphite cast iron |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2016172918A true JP2016172918A (en) | 2016-09-29 |
| JP6548924B2 JP6548924B2 (en) | 2019-07-24 |
Family
ID=57008826
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2015054631A Active JP6548924B2 (en) | 2015-03-18 | 2015-03-18 | Hypoeutectic spheroidal graphite cast iron |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP6548924B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6254655B1 (en) * | 2016-09-15 | 2017-12-27 | 虹技株式会社 | Method for producing hypoeutectic spheroidal graphite cast iron castings |
| JP6254656B1 (en) * | 2016-09-15 | 2017-12-27 | 虹技株式会社 | Method for producing hypoeutectic spheroidal graphite cast iron castings |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61174358A (en) * | 1985-01-30 | 1986-08-06 | Toyota Motor Corp | Spheroidal graphite cast steel of high strength |
| JPH01152240A (en) * | 1987-12-10 | 1989-06-14 | Toyota Motor Corp | High toughness cast steel |
| WO2011145194A1 (en) * | 2010-05-20 | 2011-11-24 | 虹技株式会社 | Heat-resistant cast iron type metallic short fiber, and process for production thereof |
| JP2013173969A (en) * | 2012-02-24 | 2013-09-05 | Riken Corp | High rigidity spherical graphite cast iron |
| JP2014028987A (en) * | 2012-07-31 | 2014-02-13 | Hinode Ltd | Ferro alloy for casting and manufacturing method thereof |
-
2015
- 2015-03-18 JP JP2015054631A patent/JP6548924B2/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61174358A (en) * | 1985-01-30 | 1986-08-06 | Toyota Motor Corp | Spheroidal graphite cast steel of high strength |
| JPH01152240A (en) * | 1987-12-10 | 1989-06-14 | Toyota Motor Corp | High toughness cast steel |
| WO2011145194A1 (en) * | 2010-05-20 | 2011-11-24 | 虹技株式会社 | Heat-resistant cast iron type metallic short fiber, and process for production thereof |
| JP2013173969A (en) * | 2012-02-24 | 2013-09-05 | Riken Corp | High rigidity spherical graphite cast iron |
| JP2014028987A (en) * | 2012-07-31 | 2014-02-13 | Hinode Ltd | Ferro alloy for casting and manufacturing method thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6254655B1 (en) * | 2016-09-15 | 2017-12-27 | 虹技株式会社 | Method for producing hypoeutectic spheroidal graphite cast iron castings |
| JP6254656B1 (en) * | 2016-09-15 | 2017-12-27 | 虹技株式会社 | Method for producing hypoeutectic spheroidal graphite cast iron castings |
| JP2018044217A (en) * | 2016-09-15 | 2018-03-22 | 虹技株式会社 | Manufacturing method of hypoeutectic spheroidal graphite cast iron cast |
| JP2018044216A (en) * | 2016-09-15 | 2018-03-22 | 虹技株式会社 | Manufacturing method of hypoeutectic spheroidal graphite cast iron cast |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6548924B2 (en) | 2019-07-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5012231B2 (en) | High-strength spheroidal graphite cast iron with excellent wear resistance | |
| JP4835424B2 (en) | High strength spheroidal graphite cast iron | |
| JP6728150B2 (en) | Cast iron molten metal treatment method | |
| JP5113104B2 (en) | Spheroidal graphite cast iron pipe and manufacturing method thereof | |
| JP5712560B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP2011144443A (en) | Aluminum alloy for semisolid casting | |
| JP6254656B1 (en) | Method for producing hypoeutectic spheroidal graphite cast iron castings | |
| CN108203786B (en) | Silicon solid solution high-strength plastic ferrite nodular cast iron, manufacturing method and railway locomotive part | |
| JP6548924B2 (en) | Hypoeutectic spheroidal graphite cast iron | |
| JP5618466B2 (en) | High rigidity high damping capacity cast iron | |
| JP5712525B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP5589646B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP5367041B2 (en) | Thin wall spheroidal graphite cast iron casting | |
| JP6763377B2 (en) | Black core malleable cast iron and its manufacturing method | |
| JP5282546B2 (en) | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance | |
| JP5282547B2 (en) | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance | |
| JP2014105342A (en) | Spheroidal graphite cast iron excellent in high temperature ductility and high temperature creep rupture life and production method thereof | |
| JP6254655B1 (en) | Method for producing hypoeutectic spheroidal graphite cast iron castings | |
| JP5952455B1 (en) | High rigidity spheroidal graphite cast iron | |
| JP6087402B2 (en) | Spheroidal graphite cast iron and method for producing the same | |
| JP2006316341A (en) | Castable aluminum alloy and aluminum alloy cast made therefrom | |
| JP2014214343A (en) | Iron cast and manufacturing method therefor | |
| JP5712531B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP2006057139A (en) | Spheroidal graphite cast iron having excellent machinability and mechanical property | |
| JP2022052437A (en) | Aluminum alloy casting and method of manufacturing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20171204 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20181106 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20181226 |
|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20190129 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20190418 |
|
| A911 | Transfer to examiner for re-examination before appeal (zenchi) |
Free format text: JAPANESE INTERMEDIATE CODE: A911 Effective date: 20190425 |
|
| 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: 20190528 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20190626 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 6548924 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |