JPH0418002B2 - - Google Patents
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- Publication number
- JPH0418002B2 JPH0418002B2 JP13454484A JP13454484A JPH0418002B2 JP H0418002 B2 JPH0418002 B2 JP H0418002B2 JP 13454484 A JP13454484 A JP 13454484A JP 13454484 A JP13454484 A JP 13454484A JP H0418002 B2 JPH0418002 B2 JP H0418002B2
- Authority
- JP
- Japan
- Prior art keywords
- molten metal
- sulfur
- cast iron
- rare earth
- spheroidal graphite
- 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.)
- Expired
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C1/00—Refining of pig-iron; Cast iron
- C21C1/10—Making spheroidal graphite cast-iron
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
Description
本発明は、薄肉球状黒鉛鋳鉄の製造方法に関す
るものである。
球状黒鉛鋳鉄、特に薄肉厚の製品（10℃／秒以
上）は、冷却速度が速く、鋳放しの状態で、加工
性の優れた材質をもたせるためには、基地組織が
フエライト／パーライトで、チルの存在しないも
のにする必要がある。
このための基本的対策として化学組成的にCE
値を高目に、或は炭化物を安定化させる元素を排
除したりして調整することは勿論であるが、球状
黒鉛鋳鉄中に存在する球状黒鉛粒数とチル発生量
との相関性について注目することは重要なことで
ある。
本発明にかかわる方法は、硫黄が0.025〜0.18
％含有する溶湯の処理により、鋳放しでチルの存
在しない健全な薄肉球状黒鉛鋳鉄を得ることにあ
る。
通常、球状黒鉛鋳鉄を製造する際、溶湯中に含
有される硫黄量は球状化阻害元素として、出来る
だけ少量である方が望ましく、0.02％以下である
ことが奨められているが、本発明では、この値よ
りも高い硫黄量を含有する溶湯処理について着目
したものである。本発明で硫黄含有量の下限を
0.025％に限定したのは、低硫黄量の場合に比べ
硫黄量が増加するにしたがい、健全な鋳物をつく
るための希土類元素の添加許容量の巾が広くなり
現場的に作業が容易になるらである。一方上限を
0.18％と定めたのは一般的な鋳物工場における溶
湯の硫黄含有量の上限が最大量0.18％程度であ
り、何等かの理由で特別に硫黄を加えないかぎ
り、これ以上の硫黄の含有された溶湯はないと考
えられているからである。
一般に高硫黄含有の溶湯は、球状化処理により
発生した主としてマグネシウム硫化物らのドロス
等非金属介在物により、或は球状化不良等により
鋳鉄の健全さが失われる。
しかし、この発明では希土類金属又は希土類元
素含有合金又は添加剤で溶湯処理することによ
り、この実験範囲内では、これらとの硫化物は鋳
鉄の健全性を何等そこなうことがない。
むしろ、実施例でも述べられている通り、本発
明でのRE処理をすることにより、黒鉛粒数の増
加の傾向は高硫黄（本発明に記述する硫黄含有
量）溶湯で顕著であることが明らかになつた。
以下実施例をもつて本発明の特色を説明する。
実施例 １
炭素：3.8％，硅素：2.2％，マンガン：0.4％，
Ｐ：0.03％で硫黄量の0.025％，0.05％及び０／13
％の３水準の溶湯に対して、夫々の硫黄量に対応
した希土類元素（以下REと略称す）を1530℃で
８％マグネシウム−鉄−硅素合金を処理する前に
添加した後、同合金1.6％にて球状化処理を行い、
鉄−硅素（75％）合金0.3％にて接種し、1400℃
で第１図に示される階段状試験片CO2型に鋳込み
3m／ｍ肉厚部のものについてチルの有無につい
て調べ、200倍の倍率で２mm2の視野の直径1μm以
上の黒鉛粒数を画像解析処理装置により測定し
た。
チルの有無、RE添加量及び黒鉛粒数との関係
を調べた結果を第２図に示した。第２図中、は
Ｓ：0.025％の溶湯、はＳ：0.05％の溶湯、
はＳ：0.130％の溶湯に夫々REを添加しFe−Si接
種の場合を示す。
なお第２図には本発明を構成するRE添加後、
８％マグネシウム−鉄−硅素カルシウム合金で上
記試験と同一溶湯に処理後、鉄−硅素（75％）合
金で接種処理して、1400℃で3m／ｍ肉厚のCO2
型（第１図参照）に注湯したもののRE添加量と
黒鉛粒数の関係をにて併記したが、カルシウム
を配合した合金（８％マグネシウム−鉄−硅素１
％カルシウム）を添加処理した場合、同一添加量
のマグネシウム−鉄−硅素合金処理のものにくら
べ黒鉛粒数も多いことがわかつた。
なお、第３図に硫黄量0.05％の溶湯にRE添加
量を変えた処理をした試験片の顕微鏡組織（100
倍）を示す。第３図中、はRE：0.08％添加の
もので黒鉛粒数487個／mm2，チル有、はRE：
0.10％添加のもので黒鉛粒数700個／mm2，チル無、
はRE：0.30％添加のもので黒鉛粒数689個／
mm2，チル無、はRE：0.40％添加のもので黒鉛
粒数510個／mm2，チル有を示す。RE添加量が適正
であれば黒鉛粒数も多く、かつチルの発生もな
い。
実施例 ２
炭素：3.8％，硅素：2.2％，マンガン：0.4％，
Ｐ：0.03％で硫黄量の0.004％，0.08％の２水準の
溶湯に対して、夫々の硫黄量に対応した希土類元
素を1530℃で８％マグネシウム−鉄−硅素合金と
同時に添加後、鉄−硅素（75％）合金にて接種
し、1400℃で実施例−１に示したと同一の階段状
試験片CO2型（第１図参照）の3m／ｍ肉厚のも
のから採取した試料について、チルの有無とRE
添加量と黒鉛粒数との関係を調べ第４図にその関
係を示した。第４図中、は硫黄量0.004％，
は硫黄量0.08％の溶湯の場合を示す。
この方法でも、実施例−１に示した結果同様、
含有硫黄量に応じたRE量の適正添加をした場合、
チルは皆無でかつ黒鉛粒数も多いことがわかつ
た。
実施例 ３
炭素：3.75％，硅素：2.38％，硫黄：0.14％の
溶湯に0.9％のREを球状化処理前、同時処理及び
処理後に添加し、鉄−硅素（75％）合金を0.3％
接種した後、1400℃で平均肉厚3m／ｍのCO2型
（第１図参照）に鋳込み、併せて、この肉厚の冷
却速度にほぼ相当する10m／mψの丸棒から試験
片を作成し、機械的性質と顕微鏡組織について調
べた結果を第１表に第５図に示した。第５図は
RE処理後球状化処理した場合、第５図はRE処
理と球状化処理を同時にした場合、第５図は球
状化処理後RE処理をした場合を示す（３％ナイ
タール×100）。
球状化処理後RE添加をしたものは黒鉛粒数が
低くチルの発生もあり、また機械的性質も著しく
低下しており効果が得られていない。
従つて本発明にかかわる球状化処理前或は球状
化処理と同時にREを添加することによつて良好
な結果が得られるといえる。
なお、上記処理溶湯と同一のものについて、
RE処理後球状化処理及び同時処理をしたものは
球状化処理後、鉄−硅素（75％）合金で接種処理
を行わない3m／ｍ肉厚のものについても組織観
察の結果、チルの発生はなく、黒鉛粒数は、各々
680個／mm2と671個／mm2で、接種したものとほぼ同
様の組織を示していた。
実施例 ４
炭素：3.80％、硅素：2.30％、硫黄量0.10％の
キユポラ溶湯について、REを0.7％添加処理した
ものと処理しないものについて、それぞれ1.6％
の８％マグネシウム−鉄−硅素合金或は８％のマ
グネシウム−鉄−硅素−４％カルシウム合金にて
球状化処理し、3m／ｍ肉厚のCO2型（第１図参
照）へ鋳込み、それらの顕微鏡組織の観察結果を
第２表に示した。
これらの結果から、RE処理後、球状化処理又
はREと球状化処理とを同時処理する本発明の効
果が顕著であることがわかり、加えてマグネシウ
ム−鉄−硅素合金にカルシウムの入つた合金は黒
鉛粒数の増加と無チル化にすぐれていることがわ
かる。
これらの実施例に供された希土類元素はセリウ
ム40〜50％、ランタン20〜30％、その他の希土類
元素バランスからなる組成の金属、いわゆるミツ
シユメタルの型で使用したが、希土類元素を含む
合金鉄、添加剤等を使用することにしても、最終
硅素量を同一量に調整すれば同一の結果を得るこ
とを確認した。
実施例 ５
炭素：3.8％、硅素：2.2％、マンガン：0.4％、
Ｐ：0.03％で硫黄量0.025％の溶湯に対し、実施
例−１で示した実験条件でセリウム：88.2％、ラ
ンタン：9.03％、鉄：0.06％その他希土類元素か
らなる合金添加処理後、球状化処理しさらに鉄−
硅素−（75％）合金で接種を行つた結果を第６図
に、又ランタン：99.80％、セリウム0.06％、鉄
0.02％、残部その他希土類元素を含む合金で上記
と同様の処理を行つた結果を第７図に示した。こ
の実施例−５からみて、希土類元素中のセリウ
ム、ランタン等の占める含有割合が変わることで
その効果が異なつてくるかどうかをチエツクした
わけであるが本発明の範囲内では略々同一の効果
のあることが認められた。
The present invention relates to a method for manufacturing thin-walled spheroidal graphite cast iron. Spheroidal graphite cast iron, especially thin-walled products (10°C/sec or more), must have a matrix structure of ferrite/pearlite and be chilled in order to have a fast cooling rate and excellent workability in the as-cast state. It is necessary to make it non-existent. As a basic measure for this purpose, CE
Of course, it is possible to adjust the value to a higher value or eliminate elements that stabilize carbides, but it is important to pay attention to the correlation between the number of spheroidal graphite grains present in spheroidal graphite cast iron and the amount of chill generation. It is important to do so. The method according to the present invention has a sulfur content of 0.025 to 0.18.
The purpose is to obtain healthy thin-walled spheroidal graphite cast iron without any chill as cast by processing the molten metal containing 100% of the molten metal. Normally, when producing spheroidal graphite cast iron, it is desirable that the amount of sulfur contained in the molten metal be as small as possible, as it is an element that inhibits spheroidization, and is recommended to be 0.02% or less. , we focused on the treatment of molten metal containing a higher amount of sulfur than this value. The present invention lowers the lower limit of sulfur content.
The reason why we limited it to 0.025% was because as the amount of sulfur increases compared to when the amount of sulfur is low, the allowable amount of rare earth elements to be added in order to make sound castings becomes wider, which makes the work easier on site. It is. On the other hand, the upper limit
The reason for setting the value at 0.18% is that the upper limit of the sulfur content in molten metal in general foundries is about 0.18%, and unless sulfur is specifically added for some reason, sulfur content higher than this is not allowed. This is because it is thought that there is no molten metal. In general, in molten metal containing high sulfur, cast iron loses its integrity due to nonmetallic inclusions such as dross, mainly magnesium sulfide, generated during the spheroidization process, or due to poor spheroidization. However, in the present invention, by treating the molten metal with rare earth metals, rare earth element-containing alloys, or additives, sulfides with these do not impair the integrity of cast iron within the scope of this experiment. Rather, as mentioned in the Examples, it is clear that by RE treatment according to the present invention, the tendency of increase in the number of graphite particles is remarkable in high-sulfur (sulfur content described in the present invention) molten metal. It became. The features of the present invention will be explained below with reference to Examples. Example 1 Carbon: 3.8%, Silicon: 2.2%, Manganese: 0.4%,
P: 0.03% and 0.025%, 0.05% and 0/13 of the sulfur content
After adding rare earth elements (hereinafter abbreviated as RE) corresponding to the respective sulfur content to three levels of molten metal at 1530℃ before processing an 8% magnesium-iron-silicon alloy, the same alloy became 1.6%. Perform spheroidization treatment at %,
Inoculated with 0.3% iron-silicon (75%) alloy, 1400℃
The stepped specimen shown in Figure 1 was cast into a CO 2 mold.
The presence or absence of chill was examined for the 3 m/m thick part, and the number of graphite particles with a diameter of 1 μm or more in a field of view of 2 mm 2 was measured using an image analysis processing device at a magnification of 200 times. Figure 2 shows the results of investigating the relationship between the presence or absence of chill, the amount of RE added, and the number of graphite particles. In Figure 2, indicates S: 0.025% molten metal, S: 0.05% molten metal,
Indicates the case of Fe-Si inoculation by adding RE to the S: 0.130% molten metal. In addition, FIG. 2 shows that after adding RE, which constitutes the present invention,
The same molten metal as in the above test was treated with an 8% magnesium-iron-silicon-calcium alloy, then inoculated with an iron-silicon (75%) alloy, and CO 2 was heated to a thickness of 3 m/m at 1400°C.
The relationship between the amount of RE added and the number of graphite particles poured into the mold (see Figure 1) is also shown in Figure 1.
% calcium), the number of graphite grains was also greater than that of the magnesium-iron-silicon alloy treated with the same amount of addition. In addition, Figure 3 shows the microscopic structures of test pieces (100
times). In Figure 3, the number of graphite particles is 487/mm 2 with RE: 0.08% added, and the number of graphite particles with chill is RE:
0.10% additive, 700 graphite particles/mm 2 , no chilling,
is the one with RE: 0.30% addition and the number of graphite particles is 689/
mm 2 , without chilling, indicates that RE: 0.40% was added and the number of graphite particles was 510/mm 2 , with chilling. If the amount of RE added is appropriate, the number of graphite particles will be large and no chill will occur. Example 2 Carbon: 3.8%, silicon: 2.2%, manganese: 0.4%,
P: 0.03% and sulfur content of 0.004% and 0.08% of the molten metal were added with rare earth elements corresponding to the respective sulfur content at 1530℃ at the same time as 8% magnesium-iron-silicon alloy. Regarding a sample taken from a 3 m/m thick stepped specimen CO 2 type (see Figure 1), which is the same as that shown in Example-1, and inoculated with silicon (75%) alloy and heated at 1400 °C, Presence or absence of chill and RE
The relationship between the amount added and the number of graphite particles was investigated, and the relationship is shown in Figure 4. In Figure 4, the amount of sulfur is 0.004%,
indicates the case of molten metal with a sulfur content of 0.08%. Even with this method, similar to the results shown in Example-1,
When the appropriate amount of RE is added according to the amount of sulfur contained,
It was found that there was no chill and there were many graphite particles. Example 3 0.9% RE was added to a molten metal containing 3.75% carbon, 2.38% silicon, and 0.14% sulfur before, simultaneously, and after the spheroidization treatment, and 0.3% iron-silicon (75%) alloy was added.
After inoculation, it was cast into a CO 2 mold (see Figure 1) with an average wall thickness of 3 m/m at 1400°C, and a test piece was made from a round bar with a diameter of 10 m/mψ, which corresponds to the cooling rate for this wall thickness. The mechanical properties and microscopic structure were investigated and the results are shown in Table 1 and Figure 5. Figure 5 is
FIG. 5 shows the case where RE treatment and spheroidization treatment were performed at the same time, and FIG. 5 shows the case where RE treatment was performed after spheronization treatment (3% nital x 100). In the case where RE was added after the spheroidization process, the number of graphite particles was low and chilling occurred, and the mechanical properties were also significantly deteriorated, so no effect was obtained. Therefore, it can be said that good results can be obtained by adding RE before or simultaneously with the spheroidization treatment according to the present invention. Regarding the same molten metal as the above-mentioned treated molten metal,
As a result of microstructural observation, it was found that the 3m/m thick iron-silicon (75%) alloy without inoculation treatment did not cause chilling. The number of graphite grains is
The numbers were 680 cells/mm 2 and 671 cells/mm 2 , showing almost the same tissue as the inoculated one. Example 4 Cyupora molten metal with 3.80% carbon, 2.30% silicon, and 0.10% sulfur was treated with 0.7% RE and 1.6% without treatment, respectively.
8% magnesium-iron-silicon alloy or 8% magnesium-iron-silicon-4% calcium alloy is spheroidized and cast into a 3m/m thick CO 2 mold (see Figure 1). Table 2 shows the observation results of the microscopic structure. From these results, it is clear that the effect of the present invention of performing spheroidization treatment or simultaneous RE and spheroidization treatment after RE treatment is remarkable, and in addition, the magnesium-iron-silicon alloy containing calcium is It can be seen that the number of graphite particles increases and the non-chilling property is excellent. The rare earth elements used in these examples were metals with a composition consisting of 40 to 50% cerium, 20 to 30% lanthanum, and a balance of other rare earth elements, so-called Mitsushi Metal type, but alloy iron containing rare earth elements, It was confirmed that even if additives were used, the same results could be obtained if the final amount of silicon was adjusted to the same amount. Example 5 Carbon: 3.8%, silicon: 2.2%, manganese: 0.4%,
A molten metal containing 0.03% P and 0.025% sulfur was spheroidized after being treated with an alloy consisting of 88.2% cerium, 9.03% lanthanum, 0.06% iron and other rare earth elements under the experimental conditions shown in Example-1. Processed and further iron-
Figure 6 shows the results of inoculation with silicon-(75%) alloy, and lanthanum: 99.80%, cerium 0.06%, iron.
FIG. 7 shows the results of the same treatment as above performed on an alloy containing 0.02% and the balance other rare earth elements. In view of this Example-5, we checked whether the effect would be different by changing the content ratio of cerium, lanthanum, etc. in the rare earth element, but within the scope of the present invention, the effect is almost the same. It was recognized that there is.
【表】【table】
第１図は階段状試験片CO2型を示す図で、Ａは
平面図、Ｂは側面図、Ｃは底面図、第２図はRE
添加量と黒鉛粒数の変化を示すグラフ、第３図は
硫黄量0.05％溶湯に対するRE効果を示す試験片
の金属組織を示す写真、第４図はRE添加量と黒
鉛粒数の変化を示すグラフ、第５図は3m／ｍ肉
厚試験片の顕微鏡組織の比較を示す写真、第６図
はCe添加量と黒鉛粒数との関係を示すグラフ、
第７図はLa添加量と黒鉛粒数との関係を示すグ
ラフである。
Figure 1 shows a stepped specimen CO 2 type, where A is a top view, B is a side view, C is a bottom view, and Figure 2 is a RE
A graph showing changes in the amount of added graphite particles and the number of graphite particles. Figure 3 is a photograph showing the metallographic structure of a test piece showing the RE effect on 0.05% sulfur molten metal. Figure 4 shows changes in the amount of added RE and the number of graphite particles. Graph, Figure 5 is a photograph showing a comparison of the microscopic structures of 3m/m wall thickness specimens, Figure 6 is a graph showing the relationship between the amount of Ce added and the number of graphite grains,
FIG. 7 is a graph showing the relationship between the amount of La added and the number of graphite particles.
Claims (1)
て硫黄含有量に対し、2.0〜7.0倍量の希土類金属
又は希土類元素を含む合金或はその添加剤で処理
し、引続き黒鉛球状化に十分な量のマグネシウム
又はマグネシウムを含む合金或は、その添加剤で
処理することを特徴とする高硫黄溶湯からの薄肉
球状黒鉛鋳鉄製造方法。 ２ 特許請求の範囲第１項記載の高硫黄溶湯から
の薄肉球状黒鉛鋳鉄製造方法に続いて、更に接種
処理を施すことを特徴とする高硫黄溶湯からの薄
肉球状黒鉛鋳鉄製造方法。 ３ マグネシウム又はマグネシウムを含む合金或
はその添加剤での処理時にカルシウム或は、含カ
ルシウム合金又はその添加剤をカルシウムとして
0.01〜0.07％添加することを特徴とする特許請求
の範囲第１項又は第２項記載の高硫黄溶湯からの
薄肉球状黒鉛鋳鉄製造方法。 ４ 0.025〜0.18％の硫黄を含有する溶湯につい
て硫黄含有量に対し、2.0〜7.0倍量の希土類金属
又は希土類元素を含む合金或はその添加剤とマグ
ネシウム又はマグネシウムを含む合金或はその添
加剤を同時に添加することを特徴とする高硫黄溶
湯からの薄肉球状黒鉛鋳鉄製造方法。 ５ 特許請求の範囲第４項記載の高硫黄溶湯から
の薄肉球状黒鉛鋳鉄製造方法に続いて、更に接種
処理を施すことを特徴とする高硫黄溶湯からの薄
肉球状黒鉛鋳鉄製造方法。 ６ 希土類金属又は希土類元素を含む合金鉄或は
その添加剤とを同時添加処理する際にカルシウム
或は含カルシウム合金又はその添加剤をカルシウ
ムとして0.01〜0.07％添加することを特徴とする
特許請求の範囲第４項又は第５項記載の高硫黄溶
湯からの薄肉球状黒鉛鋳鉄の製造方法。[Scope of Claims] 1. A molten metal containing 0.025 to 0.18% sulfur is treated with a rare earth metal, an alloy containing a rare earth element, or an additive thereof in an amount of 2.0 to 7.0 times the sulfur content, and then graphite is formed into spherical shapes. 1. A method for producing thin-walled spheroidal graphite cast iron from a high-sulfur molten metal, characterized by treating it with a sufficient amount of magnesium or an alloy containing magnesium, or an additive thereof. 2. A method for producing thin-walled spheroidal graphite cast iron from high-sulfur molten metal, which comprises further performing an inoculation treatment following the method for producing thin-walled spheroidal graphite cast iron from high-sulfur molten metal according to claim 1. 3. Calcium or calcium-containing alloys or their additives are treated as calcium during treatment with magnesium or magnesium-containing alloys or their additives.
A method for producing thin-walled spheroidal graphite cast iron from a high-sulfur molten metal according to claim 1 or 2, characterized in that 0.01 to 0.07% is added. 4 For molten metal containing 0.025 to 0.18% sulfur, 2.0 to 7.0 times the amount of rare earth metals or alloys containing rare earth elements or their additives and magnesium or alloys containing magnesium or their additives to the sulfur content. A method for producing thin-walled spheroidal graphite cast iron from high-sulfur molten metal, characterized in that the addition of sulfur at the same time is carried out. 5. A method for producing thin-walled spheroidal graphite cast iron from high-sulfur molten metal, which further comprises performing an inoculation treatment following the method for producing thin-walled spheroidal graphite cast iron from high-sulfur molten metal as set forth in claim 4. 6. A patent claim characterized in that 0.01 to 0.07% of calcium or a calcium-containing alloy or its additive is added as calcium when simultaneously adding rare earth metals, rare earth element-containing ferroalloys, or their additives. A method for producing thin-walled spheroidal graphite cast iron from a high-sulfur molten metal according to scope 4 or 5.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13454484A JPS6115910A (en) | 1984-06-29 | 1984-06-29 | Manufacture of thin spheroidal graphite cast iron from molten high sulfur metal |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13454484A JPS6115910A (en) | 1984-06-29 | 1984-06-29 | Manufacture of thin spheroidal graphite cast iron from molten high sulfur metal |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6115910A JPS6115910A (en) | 1986-01-24 |
| JPH0418002B2 true JPH0418002B2 (en) | 1992-03-26 |
Family
ID=15130796
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13454484A Granted JPS6115910A (en) | 1984-06-29 | 1984-06-29 | Manufacture of thin spheroidal graphite cast iron from molten high sulfur metal |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6115910A (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5100612A (en) * | 1989-06-21 | 1992-03-31 | 501 Hitachi Metals, Ltd. | Spheroidal graphite cast iron |
| JP4974591B2 (en) * | 2005-12-07 | 2012-07-11 | 旭テック株式会社 | Graphite spheroidizing agent and method for producing spheroidal graphite cast iron using the same |
-
1984
- 1984-06-29 JP JP13454484A patent/JPS6115910A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6115910A (en) | 1986-01-24 |
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