JPH01309939A - Spheroidal graphite cast iron and its manufacture - Google Patents
Spheroidal graphite cast iron and its manufactureInfo
- Publication number
- JPH01309939A JPH01309939A JP5807889A JP5807889A JPH01309939A JP H01309939 A JPH01309939 A JP H01309939A JP 5807889 A JP5807889 A JP 5807889A JP 5807889 A JP5807889 A JP 5807889A JP H01309939 A JPH01309939 A JP H01309939A
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- weight
- spheroidal graphite
- graphite
- graphite cast
- 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
- 229910001141 Ductile iron Inorganic materials 0.000 title claims abstract description 29
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 49
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 38
- 239000010439 graphite Substances 0.000 claims abstract description 38
- 229910052797 bismuth Inorganic materials 0.000 claims abstract description 32
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 19
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 238000000034 method Methods 0.000 claims abstract description 4
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 claims description 30
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 26
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 16
- 239000010703 silicon Substances 0.000 claims description 16
- 239000011777 magnesium Substances 0.000 claims description 11
- 229910052759 nickel Inorganic materials 0.000 claims description 11
- 229910052751 metal Inorganic materials 0.000 claims description 10
- 239000002184 metal Substances 0.000 claims description 10
- 239000011651 chromium Substances 0.000 claims description 8
- 239000011572 manganese Substances 0.000 claims description 8
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 7
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 6
- 239000011574 phosphorus Substances 0.000 claims description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 5
- 239000002245 particle Substances 0.000 claims description 3
- 229910001018 Cast iron Inorganic materials 0.000 abstract description 32
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000007423 decrease Effects 0.000 description 10
- 235000000396 iron Nutrition 0.000 description 9
- 229910001562 pearlite Inorganic materials 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 7
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 230000002829 reductive effect Effects 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 229910002092 carbon dioxide Inorganic materials 0.000 description 3
- 239000001569 carbon dioxide Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000002054 inoculum Substances 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 239000008187 granular material Substances 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 235000011835 quiches Nutrition 0.000 description 2
- 101150013553 CD40 gene Proteins 0.000 description 1
- 101000874049 Magnolia grandiflora Beta-cubebene synthase Proteins 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 102100040245 Tumor necrosis factor receptor superfamily member 5 Human genes 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 150000002680 magnesium Chemical class 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
Landscapes
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
Abstract
Description
【発明の詳細な説明】 ［発明の目的］ 〈産業−Ｌの利用分野〉 本発明は高靭性の球状黒鉛鋳鉄に関する。[Detailed description of the invention] [Purpose of the invention] <Industry-L usage field> The present invention relates to high toughness spheroidal graphite cast iron.
〈従来の技術〉
従来のフェライト地を有する球状黒鉛鋳鉄ＦＣＤ３７或
いはＦＣＤ４０は伸び及び低温時以外の衝撃値は比較的
高いが低温時の衝撃値が低いため、−４０℃程度の低温
下でも使用される自動車用或いは産業用鋳物部品等に用
いるのに適当ではない。<Prior art> Conventional spheroidal graphite cast iron FCD37 or FCD40 having a ferritic base has a relatively high elongation and impact value at temperatures other than low temperatures, but its impact value at low temperatures is low, so it can be used even at temperatures as low as -40°C. It is not suitable for use in automotive or industrial casting parts.
そこで、例えば特公昭６１−３３８９７号公報には、低
温時に於ける衝撃値を向上するべくニッケル（Ｎｉ）を
添加し、フェライト化焼なましを行った球状黒鉛鋳鉄が
開示されているが、実際にはニッケルを添加し、焼なま
しを行うのみでは、−１５℃で最低１． ７ｋｇｆ’−
ｍ／ｃｒｌの衝撃値しか得ることができない。これは、
低温時の衝撃値にはニッケルの含有量以外に珪素（Ｓｉ
）の含有量が影響するためであり、上記公報に於ける実
施例ではこの珪素の含有量が２．０重量％以上となって
いることによる。また、製造上好ましくは工数の削減及
び製造コストを低減するべく焼なましを行わす鋳放しの
状態で使用可能とすると良い。Therefore, for example, Japanese Patent Publication No. 61-33897 discloses spheroidal graphite cast iron to which nickel (Ni) is added and annealed to ferrite in order to improve the impact value at low temperatures. If only nickel is added and annealing is performed, the temperature at -15°C will be at least 1. 7kgf'-
Only an impact value of m/crl can be obtained. this is,
In addition to the nickel content, the impact value at low temperatures also depends on silicon (Si).
) is affected, and in the examples in the above publication, the silicon content is 2.0% by weight or more. In addition, in order to reduce the number of man-hours and manufacturing costs, it is preferable to allow the product to be used in an as-cast state after annealing.
そこで、特公昭５９−１７１８３号公報に開示されてい
るように、本発明者らは球状黒鉛鋳鉄にニッケルを添加
することにより引張り強さ及び耐力を向上させ、かつ珪
素の含有量を低くすることにより伸びと衝撃値を向上さ
せるに至ったが、特に低温時に於ける衝撃値を更に改善
することが望まれる。Therefore, as disclosed in Japanese Patent Publication No. 59-17183, the present inventors added nickel to spheroidal graphite cast iron to improve its tensile strength and yield strength, and to lower the silicon content. Although the elongation and impact value have been improved, it is desired to further improve the impact value, especially at low temperatures.
〈発明が解決しようとする課題〉
このような従来技術の問題点と本発明者らの知見に鑑み
、本発明の主な目的は、伸び及び特に低温に於ける衝撃
値を向上し、また熱処理を省略或いは容易とすることで
製造コストが低減化された球状黒鉛鋳鉄及びその製造方
法を提供することにある。<Problems to be Solved by the Invention> In view of the problems of the prior art and the knowledge of the present inventors, the main purpose of the present invention is to improve the elongation and especially the impact value at low temperatures, and to An object of the present invention is to provide a spheroidal graphite cast iron whose manufacturing cost is reduced by omitting or simplifying the process, and a method for manufacturing the same.
［発明の構成］
〈課題を解決するための手段〉
このような目的は本発明によれば、炭素（Ｃ）３．０重
量％〜４．０重量％、珪素（Ｓｉ）１゜５重量％〜２．
３重量％、マンガン（Ｍｎ）０゜３重量％未満、燐（Ｐ
）０．０３重量％未満、クロム（Ｃｒ）０．１０重量％
未満、マグネシウム（Ｍｇ）０．０２重量％〜０．０６
重量％、ビスマス０．００１５重量％〜０．００８重量
％、残余鉄及び不可避的不純物からなり、かつＣＥ値（
炭素当量）３．９〜４．６重量％であることを特徴とす
る球状黒鉛鋳鉄を提供することによって達成される。特
に前記ビスマスの含有重量％を０゜００１５重量％〜０
．００４重量％とし、黒鉛粒数が３００個／ｌｌｌ１１
２以上であると良い。またニッケル（Ｎｉ）を０． ５
重量％〜２．０重量％含むと良い。[Structure of the Invention] <Means for Solving the Problems> According to the present invention, such an object is achieved by using 3.0% to 4.0% by weight of carbon (C) and 1.5% by weight of silicon (Si). ~2.
3% by weight, manganese (Mn) 0° less than 3% by weight, phosphorus (P
) less than 0.03% by weight, chromium (Cr) 0.10% by weight
Less than 0.02% by weight of magnesium (Mg) to 0.06%
% by weight, bismuth from 0.0015% to 0.008% by weight, residual iron and unavoidable impurities, and has a CE value (
This is achieved by providing a spheroidal graphite cast iron characterized by a carbon equivalent content of 3.9 to 4.6% by weight. In particular, the content of bismuth is 0°0015% by weight to 0% by weight.
．． 004% by weight, and the number of graphite particles is 300/ll11
It is good if it is 2 or more. Also, nickel (Ni) was added to 0. 5
It is preferable to include 2.0% by weight.
〈作用〉
このように、適量のビスマスを添加することにより黒鉛
粒数を３００個／ｍｍ２以上とすることでパーライトを
減少させ、低温かつ短時間の熱処理或いは熱処理するこ
となしに充分な伸び及び高い衝撃値を有し、かつ適量の
ニッケルを添加することにより高い引張り強さ及び耐力
を有する球状黒鉛鋳鉄を容易に得ることができる。云う
までもなくこの球状黒鉛鋳鉄に焼なましを行うことによ
りフェライト組織とすれば更に高い伸びや靭性が得られ
る。<Effect> In this way, by adding an appropriate amount of bismuth, the number of graphite grains is increased to 300 pieces/mm2 or more, thereby reducing pearlite and achieving sufficient elongation and high strength without heat treatment at low temperature and short time. Spheroidal graphite cast iron having a high impact value and high tensile strength and proof stress can be easily obtained by adding an appropriate amount of nickel. Needless to say, if this spheroidal graphite cast iron is annealed to form a ferritic structure, even higher elongation and toughness can be obtained.
以下に、各添加物の数値限定の理由について説明する。The reasons for limiting the numerical values of each additive will be explained below.
炭素は、３．０重量％（以下ｗｔ％と記す）未満では鋳
造性が悪くなり、かつ黒鉛粒数が減少することからパー
ライトが多くなる。また、４． ０ｗｔ％を超えるとキ
ッシュ黒鉛が出易くなり強度が低下する。If the carbon content is less than 3.0% by weight (hereinafter referred to as wt%), castability deteriorates and the number of graphite grains decreases, so pearlite increases. Also, 4. If it exceeds 0 wt%, quiche graphite tends to come out and the strength decreases.
珪素は、１． ５ｗｔ％未満では炭化物が析出し易くな
り、衝撃値及び伸びが共に低下する。また、２、 ３ｗ
ｔ％を超えるとシリコフェライトの影響で衝撃値及び伸
びが低下する。Silicon is 1. If it is less than 5 wt%, carbides tend to precipitate, and both impact value and elongation decrease. Also, 2, 3w
If it exceeds t%, the impact value and elongation will decrease due to the influence of silicoferrite.
マンガンは、０．３ｗｔ％を超えるとパーライトが多く
なり衝撃値及び伸びが低下する。When manganese exceeds 0.3 wt%, pearlite increases and impact value and elongation decrease.
燐は、０． ０３ｗｔ％を超えるとステダイトの影響で
衝撃値及び伸びが低下する。Phosphorus is 0. If it exceeds 0.3 wt%, the impact value and elongation will decrease due to the influence of steadite.
ニッケルは、０． ５ｗｔ％未満では強度が得られない
。また、２． ０ｗｔ％を超えるとパーライトが多くな
り衝撃値及び伸びが低下する。Nickel is 0. If it is less than 5 wt%, no strength can be obtained. Also, 2. If it exceeds 0 wt%, the amount of pearlite increases and the impact value and elongation decrease.
クロムは、０． １ｗｔ％を超えると炭化物が析出し易
くなり衝撃値及び伸びが低下する。Chromium is 0. When it exceeds 1 wt%, carbides tend to precipitate, resulting in a decrease in impact value and elongation.
マグネシウムは、０．０２ｗｔ％未満では黒鉛が球状化
しない。また、０． ０６ｗｔ％を超えるとひけ巣及び
炭化物が出易くなるばかりでなく製造コストも高騰化す
る。When the amount of magnesium is less than 0.02 wt%, graphite does not become spheroidized. Also, 0. If it exceeds 0.06 wt%, not only shrinkage cavities and carbides are likely to appear, but also manufacturing costs will increase.
ＣＥ値は、３． ９ｗＬ％未満では炭化物が出易くなり
鋳造性も悪くなる。また、４． ６ｗｔ％を超えるとキ
ッシュ黒鉛が出易くなる。ここで、ＣＥ値は、
ＣＥ＝総炭素ｗｔ％÷（珪素ｗＬ％十燐ｗｔ％）／３に
より求められる。The CE value is 3. If it is less than 9 wL%, carbides tend to appear and castability deteriorates. Also, 4. If it exceeds 6 wt%, quiche graphite tends to appear. Here, the CE value is determined by CE=total carbon wt%/(silicon wL% ten phosphorus wt%)/3.
ビスマスは、その残留含有量が０．００１５ｗＬ％未満
では黒鉛粒数の増大効果が低下し、鋳放し組織中にセメ
ンタイトが発生するようになる。また、残留含有量が０
．００８ｗｔ％を超えると黒鉛球状化の阻害効果が現れ
、黒鉛の球状化率が８０％以下となり機械的諸性質が劣
化する。好ましくはビスマス残留含有率を０． ００４
ｗｔ％以下とし、黒鉛球状化率を９０％以上とすると良
い。尚、ビスマスは球状黒鉛鋳鉄溶湯に対する溶は込み
歩留り率が悪く、歩留り率の変動も大きいことから残留
含有量を０．００１５ｗｔ％〜０．００８ｗｔ％の範囲
にするためには、溶湯に対するビスマスの添加歯を０．
００５ｗｔ％〜０．０２５ｗＬ％の範囲に設定する必要
がある。If the residual content of bismuth is less than 0.0015 wL%, the effect of increasing the number of graphite grains will be reduced, and cementite will occur in the as-cast structure. Also, the residual content is 0
．． If it exceeds 0.008 wt%, the effect of inhibiting graphite spheroidization appears, and the spheroidization rate of graphite becomes 80% or less, resulting in deterioration of various mechanical properties. Preferably, the bismuth residual content is 0. 004
It is preferable to make the graphite spheroidization rate 90% or more. In addition, since bismuth has a poor melt penetration yield rate in molten spheroidal graphite cast iron and large fluctuations in yield rate, in order to keep the residual content in the range of 0.0015 wt% to 0.008 wt%, Added tooth 0.
It is necessary to set it within the range of 0.005wt% to 0.025wL%.
黒鉛粒数は、３００００ｍｍ２未満では、黒鉛粒間の距
離が大きくなりパーライトの析出が多くなることから衝
撃値及び伸びが低下する。If the number of graphite grains is less than 30,000 mm2, the distance between the graphite grains becomes large and pearlite precipitation increases, resulting in a decrease in impact value and elongation.
〈実施例〉
第１表は、本発明に基づく第１の実施例に於ける球状黒
鉛鋳鉄の成分表である。<Example> Table 1 is a composition table of spheroidal graphite cast iron in a first example based on the present invention.
（以下余白）
本実施例の鋳型は厚さ２５ｍｍ、長さ２５０ｍｍのＹブ
ロック（ＪＩＳ Ｇ ５５０２）の鋳型を二酸化炭
素（ＣＯ２）鋳型にて造型した。(The following is a blank space) The mold of this example was a Y block (JIS G 5502) mold having a thickness of 25 mm and a length of 250 mm, and was molded using a carbon dioxide (CO2) mold.
この鋳型に第１表の成分からなる各溶湯を注入し、Ｆｅ
−Ｓｉ合金（Ｓｉ７０ｗＬ％〜７５ｗＬ％）からなる粘
度２０〜１００メツシユの接種剤をこの溶湯に対して０
．１０ｗｔ％の割合で接種してテストピースを作成した
。ここで、実際には上記接種剤を０ 、 ０５ ｗＬ％
〜０ 、 ３０ ｗＬ％の割合で接種すれば良く、０
．３０ｗＬ％よりも多いと鋳鉄中の珪素の含有■が過多
となり、０． ０５ｗｃ％よりも少ないと黒鉛生成効果
が低下する。尚、本実施例ではビスマスを高さ１５ｍｍ
、底面の直径２５ｍｍ〜３０ｍｍの円錐形をなす塊状で
溶湯に添加したために比較的歩留りが悪かったが、例え
ば、直径１ ｍｍ〜３ｍｍの粒状にし、紙等に包み溶湯
に添加することにより添加率０．０２５ｗ［％に対して
含有率０゜００８ｗｔ％、添加率０．Ｏ１５ｗＬ％に対
して含有率０．００４ｗｔ％、添加率０． ００５ｗＬ
％に対して含有率０．００１５ｗｔ％とすることができ
る。Each molten metal consisting of the components listed in Table 1 was poured into this mold, and Fe
- An inoculant made of Si alloy (70 wL% to 75 wL% Si) with a viscosity of 20 to 100 mesh is applied to this molten metal at zero
．． A test piece was prepared by inoculating at a rate of 10 wt%. Here, the above inoculant was actually added to 0.05 wL%.
It is sufficient to inoculate at a rate of 0 to 30 wL%, and 0
．． If it is more than 30wL%, the silicon content in the cast iron will be excessive, and the silicon content will be 0. If it is less than 0.05wc%, the graphite generation effect will be reduced. In this example, the bismuth is 15 mm in height.
However, the yield was relatively low because it was added to the molten metal in the form of a conical lump with a bottom diameter of 25 mm to 30 mm. Content rate is 0°008wt%, addition rate is 0.025w[%]. Content rate is 0.004 wt% with respect to O15wL%, addition rate is 0. 005wL
%, the content can be set to 0.0015 wt%.
このように作成したテストピースについて第１図（ａ）
、（ｂ）、（Ｃ）、（ｄ）及び（ｅ）に顕微鏡組織写真
を示す。第１図（ａ）に示す鋳鉄（１）、第１図（ｂ）
に示す鋳鉄（２）及び第１図（ｃ）に示す鋳鉄（３）は
本発明に基づく球状黒鉛鋳鉄であり、第１図（ｄ）及び
（ｅ）は各々従来の球状黒鉛鋳鉄ＦＣＤ４０及びＦＣＤ
６０を示す。Figure 1 (a) shows the test piece created in this way.
, (b), (C), (d) and (e) show microscopic structural photographs. Cast iron (1) shown in Figure 1(a), Figure 1(b)
Cast iron (2) shown in Figure 1(c) and cast iron (3) shown in Figure 1(c) are spheroidal graphite cast irons based on the present invention, and Figures 1(d) and (e) are conventional spheroidal graphite cast irons FCD40 and FCD, respectively.
60 is shown.
第１図（ａ）、（ｂ）及び（Ｃ）に良く示すように、ニ
ッケルの添加量が多くなるに従い、パーライト量が増加
していく。また、従来のＦＣＤ４０及びＦＣＤ６０に比
較して本発明に基づく鋳鉄（１）〜（３）は黒鉛粒数が
黒鉛粒数が多くなっている。これは、各鋳鉄（１）〜（
３）に適量のビスマスが添加されていることによる。As clearly shown in FIGS. 1(a), (b), and (C), as the amount of nickel added increases, the amount of pearlite increases. Furthermore, compared to the conventional FCD40 and FCD60, the cast irons (1) to (3) based on the present invention have a larger number of graphite grains. This is for each cast iron (1) ~ (
This is due to the addition of an appropriate amount of bismuth to 3).
第２図及び第３図にこれら各鋳鉄の機械的性質を示す。Figures 2 and 3 show the mechanical properties of each of these cast irons.
両図に良く示すように、本発明に基づく鋳鉄（１）は引
張り強さ及び耐力はＦＣＤ４０に比較してやや劣るもの
の伸び及び衝撃値が極めて優れている。また、鋳鉄（２
）は、引張り強さ、耐力及び伸びが共にＦＣＤ４０と路
間等であるが、衝撃値が著しく優れている。ここで、云
うまでもなく： ＦＣＤ６０に比較するとより高い伸び
及び衝撃値を示している。更に、本発明に基づく鋳鉄（
３）は、ＦＣＤ４０に比較して引張り強さに優れ、伸び
がやや劣り衝撃値が路間等である。また、ＦＣＤ６０に
比較すると、引張り強さ及び耐力はやや低いが伸び及び
衝撃値が優れている。As clearly shown in both figures, the cast iron (1) based on the present invention has slightly inferior tensile strength and yield strength compared to FCD40, but is extremely superior in elongation and impact value. Also, cast iron (2
) has tensile strength, yield strength, and elongation that are all on par with FCD40, but the impact value is significantly superior. Here, it goes without saying: Compared to FCD60, it exhibits higher elongation and impact values. Furthermore, cast iron according to the present invention (
3) is superior in tensile strength to FCD40, has slightly inferior elongation, and has a low impact value. Also, compared to FCD60, the tensile strength and yield strength are slightly lower, but the elongation and impact value are excellent.
このように本発明に基づく鋳鉄（１）〜（３）は従来の
鋳鉄（ＦＣＤ４０、ＦＣＤ６０）に比較して極めて優れ
ている。As described above, cast irons (1) to (3) according to the present invention are extremely superior to conventional cast irons (FCD40, FCD60).
第４図（ａ）、（ｂ）、（Ｃ）及び（ｄ）は本発明に基
づく第２の実施例に於ける第１の実施例と同様の顕微鏡
組織写真である。第４図（ａ）に示す鋳鉄（４）は第１
の実施例の鋳鉄（１）、第４図（ｂ）に示す鋳鉄（５）
は鋳鉄（２）、第４図（ｃ）に示す鋳鉄（６）は鋳鉄（
３）、第４図（ｄ）ｉ、ｌ：示ｔＦｃＤ４０ （熱処理
）４；ｔＦｃＤ４．０に各々以下の熱処理サイクルにて
フェライト化焼なましを行ったものである。FIGS. 4(a), (b), (C), and (d) are microscopic structural photographs of the second embodiment based on the present invention, similar to those of the first embodiment. The cast iron (4) shown in Fig. 4(a) is
Cast iron (1) of the example shown in Fig. 4(b), cast iron (5) shown in Fig. 4(b)
is cast iron (2), and cast iron (6) shown in Fig. 4(c) is cast iron (
3), FIG. 4(d) i, l: tFcD40 (Heat treatment) 4; tFcD4.0 was annealed to ferrite using the following heat treatment cycle.
９００℃×２時間→７２０℃×２時間→炉冷第４図（ａ
）、（ｂ）及び（ｃ）に示すように、ニッケルの添加量
を増加し、２． Ｑｗｔ％まで含有させても完全にフ
ェライト化している。また、上記熱処理を施した後でも
本発明に基づく鋳鉄（４）〜（６）の黒鉛粒数は第４図
（ｄ）に示すＦＣＤ４０の熱処理材よりも多い。900°C x 2 hours → 720°C x 2 hours → Furnace cooling Figure 4 (a
), (b) and (c), the amount of nickel added was increased, and 2. Even if it is contained up to Qwt%, it is completely converted into ferrite. Further, even after the above-mentioned heat treatment, the number of graphite grains in cast irons (4) to (6) based on the present invention is larger than that in the heat-treated material of FCD 40 shown in FIG. 4(d).
第５図及び第６図にこれら各鋳鉄の機械的性質を示す。Figures 5 and 6 show the mechanical properties of each of these cast irons.
両図に良く示すように、鋳鉄（４）は、引張り強さ及び
耐力はＦＣＤ４０ （熱処理）と略同様であるが、伸び
及び衝撃値が著しく優れている。特に低温（−４０℃）
に於ける衝撃値が優れている。また、鋳鉄（５）は、Ｆ
ＣＤ４０ （熱処理）に比較して引張り強さ、耐力、伸
び及び衝撃値が共に優れている。更に、鋳鉄（６）は、
ＦＣＤ４０（熱処理）に比較して伸び及び衝撃値がやや
低いものの引張り強さ及び耐力が著しく優れている。As clearly shown in both figures, cast iron (4) has approximately the same tensile strength and yield strength as FCD40 (heat treated), but is significantly superior in elongation and impact value. Especially at low temperatures (-40℃)
Excellent impact value. In addition, cast iron (5) is F
It has superior tensile strength, yield strength, elongation, and impact value compared to CD40 (heat treated). Furthermore, cast iron (6) is
Although the elongation and impact value are slightly lower than FCD40 (heat treated), the tensile strength and yield strength are significantly superior.
第２表は、本発明に基づく第３の実施例に於ける球状黒
鉛鋳鉄の成分表である。Table 2 is a composition table of spheroidal graphite cast iron in the third embodiment of the present invention.
本実施例の鋳型は、第１の実施例と同様に厚さ２５ｍｍ
、長さ２５０ ｍｍのＹブロックの鋳型を二酸化炭素（
Ｃｏ□）鋳型にて造型した。The mold of this example has a thickness of 25 mm as in the first example.
, a Y block mold with a length of 250 mm was heated with carbon dioxide (
Co□) Molded using a mold.
この鋳型に溶湯を注入し、第１の実施例と同様Ｆｅ−Ｓ
ｉ合金（Ｓｉ７０ｗｔ％〜７５ｗｔ％）からなる粘度２
０〜１００メツシユの接種剤をこの溶湯に対して０．１
０ｗｔ％の割合で接種して作成したテストピースについ
て第７図（ａ）、（ｂ）、（Ｃ）及び（ｄ）に顕微鏡組
織写真を示す。尚、第１の実施例と同様に本実施例に於
てもビスマスを高さ１５ｍｍ、底面の直径２５ｍｍ 〜
３０ｍｍの円錐形をなす塊状で溶湯に添加した。Molten metal was poured into this mold, and Fe-S
Viscosity 2 consisting of i alloy (Si70wt% to 75wt%)
Add 0 to 100 mesh of inoculant to this molten metal at 0.1
FIGS. 7(a), (b), (C), and (d) show microscopic microstructure photographs of test pieces prepared by inoculating at a ratio of 0 wt%. Incidentally, as in the first embodiment, in this embodiment, the bismuth is 15 mm in height and 25 mm in diameter at the bottom.
It was added to the molten metal in the form of a 30 mm cone-shaped block.
第７図（ａ）に示す鋳鉄（７）は本発明に基づく球状黒
鉛鋳鉄であり、第７図（ｂ）は従来の球状黒鉛鋳鉄ＦＣ
Ｄ４０、第７図（Ｃ）は珪素の含有ｗｔ％を低く（７た
ＦＣＤ４０、第７図（ｄ）はビスマスを添加し７たＦＣ
Ｄ４０を示す。The cast iron (7) shown in FIG. 7(a) is the spheroidal graphite cast iron based on the present invention, and FIG. 7(b) is the conventional spheroidal graphite cast iron FC.
D40, Figure 7(C) is FCD40 with low silicon content (7), Figure 7(d) is FC with added bismuth.
Indicates D40.
第７図（ａ）、（ｂ）、（Ｃ）及び（ｄ）に良く示すよ
うに、ＦＣＤ４０、珪素の含有ｗｔ％を低くしたＦＣＤ
４０及びビスマスを添加したＦＣＣ４０に比較して本発
明に基づく鋳鉄（７）は、黒鉛粒数が多くかつフェライ
ト組織が多くなっている。これに対してＦＣＤ４０は黒
鉛粒数が少なくパーライトが多くなっている。また、珪
素の含Ｙ１ｗｔ％の低いＦＣＤ４０にあっては黒鉛粒数
が少なくパーライトが極めて多くなっている。更に、ビ
スマスを添加したＦＣＤ４０は、黒鉛粒数が比較的多く
、かつフェライト組織も多くなっている。As clearly shown in Figure 7 (a), (b), (C) and (d), FCD40, FCD with low silicon content wt%
Cast iron (7) based on the present invention has a larger number of graphite grains and a larger ferrite structure than FCC40 containing 40 and bismuth. On the other hand, FCD40 has fewer graphite grains and more pearlite. Furthermore, in FCD40 with a low silicon content of 1 wt %, the number of graphite grains is small and pearlite is extremely large. Furthermore, FCD40 containing bismuth has a relatively large number of graphite grains and a large number of ferrite structures.
第８図及び第９図にこれら各鋳鉄の機械的性質を示す。Figures 8 and 9 show the mechanical properties of each of these cast irons.
両図に良く示すように、鋳鉄（７）は、引張り強さ及び
耐力はＦＣＤ４０よりも低くなっているが、伸び及び衝
撃値に優れている。特に、低温時（−４０℃）に於ける
衝撃値は、１．７ｋｇｆ’＊ｒｎ／ｃｍ２程度の良好な
値が得られる。また、珪素の含有ｗＬ％の低いＦＣＤ４
０では、パーライトが多いことにより引張り強さ及び耐
力が高くなっているが、伸び及び衝撃値が著しく低くな
っている。更に、ビスマスを添加したＦＣＤ４０は黒鉛
が微細化され各フェライト組織が多くなっているが、鋳
鉄（７）に比較すると延び及び衝撃値が低くなっている
。特に−４０℃に於ける低温時の衝撃値は鋳鉄（７）の
方が著しく高いことがわかる。As clearly shown in both figures, cast iron (7) has lower tensile strength and yield strength than FCD40, but is superior in elongation and impact value. In particular, a good impact value at low temperatures (-40°C) of about 1.7 kgf'*rn/cm2 can be obtained. In addition, FCD4 with low silicon content wL%
0, the tensile strength and yield strength are high due to the large amount of pearlite, but the elongation and impact value are significantly low. Furthermore, FCD40 containing bismuth has finer graphite and more ferrite structures, but has lower elongation and impact value than cast iron (7). In particular, it can be seen that the impact value at low temperatures of -40°C is significantly higher for cast iron (7).
このように、本発明に基づく鋳鉄（７）は従来の鋳鉄（
ＦＣＤ４０、珪素低含有ＦＣＤ４０、ビスマス添加ＦＣ
Ｄ４０）に比較して極めて優れている。In this way, the cast iron (7) based on the present invention is different from the conventional cast iron (
FCD40, low silicon content FCD40, bismuth added FC
D40).
尚、本実施例の鋳鉄（７）は熱処理を行わなくとも優れ
た性質が得られる。In addition, the cast iron (7) of this example can obtain excellent properties even without heat treatment.
第１０図のグラフ及び第１１図（ａ）〜（１）の顕微鏡
組織写真は、球状黒鉛鋳鉄のビスマスの含有率（ｗＬ％
）による黒鉛球状化率（％）の変化を示す。ここで本実
施例の球状黒鉛鋳鉄は、炭素３、 ５５ｗＬ％〜３．７
５ｗｔ％、珪素２． ＯｗＬ％〜２、 ３ｗｔ％、マ
ンガン０． ３ｗＬ％未満、リン０゜３３ｗｔ％未満、
クロム０．０５ｗｔ％未満、硫黄０゜００５ｗｔ％未満
、マグネシウム０．０２７ｗｔ％〜０、 ０４０ｗＬ％
及びビスマスを含有し、残余鉄及び不可避的不純物から
なり、ビスマスの添加率を調整してその食台率を０゜０
０１０ｗｔ％〜０．００９６ｗｔ％の範囲で変化させて
鋳造した。The graph in Figure 10 and the microscopic structure photographs in Figures 11 (a) to (1) show the bismuth content (wL%) of spheroidal graphite cast iron.
) shows the change in graphite spheroidization rate (%). Here, the spheroidal graphite cast iron of this example contains carbon 3, 55 wL% to 3.7
5wt%, silicon 2. OwL%~2,3wt%, manganese 0. less than 3wL%, phosphorus less than 0°33wt%,
Chromium less than 0.05wt%, sulfur less than 0°005wt%, magnesium 0.027wt%~0, 040wL%
It contains residual iron and unavoidable impurities, and the addition rate of bismuth is adjusted to bring the table rate to 0°0.
Casting was performed by varying the amount from 0.010 wt% to 0.0096 wt%.
第１１図（ａ）〜（１）から求めたビスマス含有率に対
する黒鉛球状化率をグラフ化した第１０図に示すように
、ビスマスの含有率が０．００１５ｗｔ％〜０．００８
ｗＬ％の範囲にあるときには、各成分を上記した範囲で
含有している場合に於て、黒鉛球状化率が８０％以上と
なり、望ましい結果が得られた。特にビスマスの含有率
が０．００１５ｖｔ％〜０． ００４ｗＬ％の範囲であ
ると、黒鉛球状化率が９０％以上となり、また比較的黒
鉛球状化率のばらつきもなくなる。As shown in FIG. 10, which is a graph of the graphite nodularization rate against the bismuth content determined from FIG.
When the content of each component was within the range of wL%, the graphite nodularity was 80% or more, and desirable results were obtained. In particular, the bismuth content is between 0.0015vt% and 0.0015vt%. In the range of 0.004 wL%, the graphite nodularity is 90% or more, and there is relatively no variation in the graphite nodularity.
ここで、ビスマス含有率が０．００１５ｗＬ％未満であ
るとチルの発生が懸念され、また、０．００４ｗｔ％を
越えると黒鉛球状化率が急激に低下して、特にビスマス
含有率が０．００８ｗｔ％を越えると黒鉛球状化率が８
０％未満となり所望量の球状黒鉛が得られず鋳鉄の低温
時の衝撃地及び伸びが著しく劣化する。このとき、ビス
マスの食台率を０．００１５ｗｔ％−”０． ００８ｖ
ｔ％の範囲にするためは、鋳造時の溶湯にビスマス０．
００５ｗｔ％〜０．０２５ｗｔ％を直径１ ｍｍ〜３
ｍｍの粒状として紙に包んで添加すると良い。また、
ビスマスの含有率を０．００１５ｗｔ％〜０． ００４
ｗＬ％の範囲にするためは、鋳造時の溶湯にビスマス０
．００５Ｗ［％〜０．０１５ｗＬ％を直径１ｍｆｆ１〜
３ｍ１１１の粒状として紙に包んで添加すると良い。Here, if the bismuth content is less than 0.0015 wL%, there is a concern that chill will occur, and if it exceeds 0.004 wt%, the graphite nodularity rate will decrease rapidly, especially if the bismuth content is 0.008 wL%. If it exceeds %, the graphite spheroidization rate will be 8.
If it is less than 0%, the desired amount of spheroidal graphite cannot be obtained, and the impact strength and elongation of cast iron at low temperatures are significantly deteriorated. At this time, the table ratio of bismuth is 0.0015wt% - "0.008v
In order to keep it within the t% range, 0.0% bismuth is added to the molten metal during casting.
005wt%~0.025wt% with a diameter of 1mm~3
It is best to add it in the form of millimeter granules wrapped in paper. Also,
The bismuth content is 0.0015wt% to 0.0015wt%. 004
In order to keep the wL% range, bismuth 0 is added to the molten metal during casting.
．． 005W[%~0.015wL% to diameter 1mff1~
It is best to wrap it in paper and add it in the form of granules of 3m111.
尚、成分中のマグネシウムは黒鉛の球状化を促進するが
、硫黄は、ＭｇＳやＭｇ２５等を形成することによりこ
のマグネシウムを非金属介在物に変化させることにより
黒鉛の形成及び球状化を阻害する元素として知られてい
る。従って、上記鋳鉄のマグネシウムを多くするか或い
は硫黄を少なくすることにより第１０図の曲線の傾きが
小さくなり、ビスマスの含有率がやや多くても所望の黒
鉛球状化率が得られるようになる。In addition, magnesium in the component promotes the spheroidization of graphite, but sulfur is an element that inhibits the formation of graphite and spheroidization by changing this magnesium into nonmetallic inclusions by forming MgS, Mg25, etc. known as. Therefore, by increasing the magnesium content or decreasing the sulfur content in the cast iron, the slope of the curve in FIG. 10 becomes smaller, and the desired graphite nodularity can be obtained even if the bismuth content is slightly higher.
［発明の効果］
このように本発明によれば、鋳放し状態で優れた引張り
強さ、延び及び衝撃値を有する球状黒鉛鋳鉄が得られる
ようになることから、熱処理の工数を削減することがで
きる。また、この鋳鉄に熱処理を施することにより一層
優れた延び及び衝撃値が得られ、特に低温に於ける衝撃
値が著しく向上する。従って、本発明は球状黒鉛鋳鉄の
機械的性質の向上及び製造原価の低減化に極めて高い効
果をもたらすものである。[Effects of the Invention] As described above, according to the present invention, spheroidal graphite cast iron having excellent tensile strength, elongation, and impact value in the as-cast state can be obtained, so that the number of heat treatment steps can be reduced. can. In addition, by subjecting this cast iron to heat treatment, even better elongation and impact values can be obtained, and especially the impact values at low temperatures are significantly improved. Therefore, the present invention is extremely effective in improving the mechanical properties of spheroidal graphite cast iron and reducing manufacturing costs.
第１図（ａ）、（ｂ）、（ｃ）、（ｄ）及び（ｅ）は、
本発明に基づく第１の実施例を示す金属顕微鏡組織写真
である。
第２図及び第３図は、共に第１図（ａ）〜（ｅ）に示す
本発明に基づく各鋳鉄及び比較材の機械的性質を示すグ
ラフである。
第４図（ａ）、（ｂ）、（Ｃ）、及び（ｄ）は、本発明
に基づく第２の実施例を示す金属顕微鏡写真である。
第５図及び第６図は、共に第４図（ａ）〜（ｄ）に示す
本発明に基づく各鋳鉄及び比較材の機械的性質を示すグ
ラフである。
第７図（ａ）、（ｂ）、（Ｃ）、及び（ｄ）は、本発明
に基づく第３の実施例を示す金属顕微鏡写真である。
第８図及び第９図は、共に第７図（ａ）〜（ｄ）に示す
本発明に基づく鋳鉄及び比較材の機械的性質を示すグラ
フである。
第１０図は、球状黒鉛鋳鉄のビスマス含有率と黒鉛球状
化率との関係を示すグラフである。
第１１図（ａ）〜（１）は球状黒鉛鋳鉄のビスマスの含
有率と黒鉛球状化率との関係を示す金属顕微鏡組織写真
である。Figures 1 (a), (b), (c), (d) and (e) are
1 is a metallurgical microscopic photograph showing a first example based on the present invention. FIGS. 2 and 3 are graphs showing the mechanical properties of each cast iron according to the present invention and comparative materials shown in FIGS. 1(a) to (e). FIGS. 4(a), (b), (C), and (d) are metallurgical micrographs showing a second embodiment based on the present invention. 5 and 6 are graphs showing the mechanical properties of each cast iron according to the present invention and the comparative material shown in FIGS. 4(a) to 4(d). FIGS. 7(a), (b), (C), and (d) are metallurgical micrographs showing a third embodiment based on the present invention. 8 and 9 are graphs showing the mechanical properties of the cast iron according to the present invention and the comparative material shown in FIGS. 7(a) to 7(d). FIG. 10 is a graph showing the relationship between bismuth content and graphite nodularity of spheroidal graphite cast iron. FIGS. 11(a) to 11(1) are metallographic microstructure photographs showing the relationship between bismuth content and graphite nodularity of spheroidal graphite cast iron.
Claims (6)
Ｓｉ）１．５重量％〜２．３重量％、マンガン（Ｍｎ）
０．３重量％未満、燐（Ｐ）０．０３重量％未満、クロ
ム（Ｃｒ）０．１０重量％未満、マグネシウム（Ｍｇ）
０．０２重量％〜０．０６重量％、ビスマス（Ｂｉ）０
．００１５重量％〜０．００８重量％、残余鉄及び不可
避的不純物からなり、かつＣＥ値（炭素当量）３．９〜
４．６重量％であることを特徴とする球状黒鉛鋳鉄。(1) Carbon (C) 3.0% to 4.0% by weight, silicon (
Si) 1.5% to 2.3% by weight, manganese (Mn)
less than 0.3% by weight, phosphorus (P) less than 0.03% by weight, chromium (Cr) less than 0.10% by weight, magnesium (Mg)
0.02% to 0.06% by weight, bismuth (Bi) 0
．． 0015% by weight to 0.008% by weight, consisting of residual iron and unavoidable impurities, and CE value (carbon equivalent) 3.9 to
Spheroidal graphite cast iron characterized by having a content of 4.6% by weight.
〜０．００４重量％としたことを特徴とする特許請求の
範囲第１項に記載の球状黒鉛鋳鉄。(2) The content of bismuth is 0.0015% by weight.
Spheroidal graphite cast iron according to claim 1, characterized in that the content is 0.004% by weight.
特徴とする特許請求の範囲第１項若しくは第２項に記載
の球状黒鉛鋳鉄。(3) Spheroidal graphite cast iron according to claim 1 or 2, characterized in that the number of graphite particles is 300 pieces/mm^2 or more.
含むことを特徴とする特許請求の範囲第１項乃至第３項
のいずれかに記載の球状黒鉛鋳鉄。(4) 0.5% to 2.0% by weight of nickel (Ni)
Spheroidal graphite cast iron according to any one of claims 1 to 3, characterized in that the spheroidal graphite cast iron comprises:
Ｓｉ）１．５重量％〜２．３重量％、マンガン（Ｍｎ）
０．３重量％未満、燐（Ｐ）０．０３重量％未満、クロ
ム（Ｃｒ）０．１０重量％未満、マグネシウム（Ｍｇ）
０．０２重量％〜０．０６重量％、残余鉄及び不可避的
不純物からなり、かつＣＥ値（炭素当量）３．９〜４．
６％である溶湯に、ビスマス（Ｂｉ）を０．００５重量
％〜０．０２５重量％添加すると同時にまたは添加後に
接種し、黒鉛粒数を３００個／ｍｍ＾２以上としたこと
を特徴とする球状黒鉛鋳鉄の製造方法。(5) Carbon (C) 3.0% to 4.0% by weight, silicon (
Si) 1.5% to 2.3% by weight, manganese (Mn)
less than 0.3% by weight, phosphorus (P) less than 0.03% by weight, chromium (Cr) less than 0.10% by weight, magnesium (Mg)
0.02% to 0.06% by weight, consisting of residual iron and unavoidable impurities, and CE value (carbon equivalent) of 3.9 to 4.
It is characterized by adding 0.005% to 0.025% by weight of bismuth (Bi) to a 6% molten metal and inoculating it at the same time or after the addition, so that the number of graphite particles is 300 pieces/mm^2 or more. Method for manufacturing spheroidal graphite cast iron.
．０重量％含むことを特徴とする特許請求の範囲第５項
に記載の球状黒鉛鋳鉄の製造方法。(6) The molten metal contains 0.5% to 2% by weight of nickel (Ni)
．． The method for producing spheroidal graphite cast iron according to claim 5, characterized in that it contains 0% by weight.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US165873 | 1988-03-09 | ||
| US07/165,873 US4889687A (en) | 1987-03-09 | 1988-03-09 | Nodular cast iron having a high impact strength and process of treating the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01309939A true JPH01309939A (en) | 1989-12-14 |
| JP2730959B2 JP2730959B2 (en) | 1998-03-25 |
Family
ID=22600835
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1058078A Expired - Fee Related JP2730959B2 (en) | 1988-03-09 | 1989-03-09 | Spheroidal graphite cast iron and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2730959B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105861920A (en) * | 2016-06-17 | 2016-08-17 | 沈阳铸造研究所 | High-dimensional-stability cast iron and preparing method thereof |
| CN114058937A (en) * | 2021-11-19 | 2022-02-18 | 襄阳金耐特机械股份有限公司 | Low-temperature high-toughness nodular cast iron and application thereof |
| US11254993B2 (en) | 2015-07-15 | 2022-02-22 | I2C Co., Ltd. | Method for producing die-cast product of spheroidal graphite cast iron having ultrafine spheroidal graphite, and die-cast product of spheroidal graphite cast iron |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS64246A (en) * | 1987-03-09 | 1989-01-05 | Hitachi Metals Ltd | Spheroidal graphite cast iron |
| JPS64245A (en) * | 1987-03-09 | 1989-01-05 | Hitachi Metals Ltd | Spheroidal graphite cast iron |
-
1989
- 1989-03-09 JP JP1058078A patent/JP2730959B2/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS64246A (en) * | 1987-03-09 | 1989-01-05 | Hitachi Metals Ltd | Spheroidal graphite cast iron |
| JPS64245A (en) * | 1987-03-09 | 1989-01-05 | Hitachi Metals Ltd | Spheroidal graphite cast iron |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US11254993B2 (en) | 2015-07-15 | 2022-02-22 | I2C Co., Ltd. | Method for producing die-cast product of spheroidal graphite cast iron having ultrafine spheroidal graphite, and die-cast product of spheroidal graphite cast iron |
| CN105861920A (en) * | 2016-06-17 | 2016-08-17 | 沈阳铸造研究所 | High-dimensional-stability cast iron and preparing method thereof |
| CN105861920B (en) * | 2016-06-17 | 2018-10-09 | 沈阳铸造研究所 | A kind of high-dimensional stability cast iron and preparation method thereof |
| CN114058937A (en) * | 2021-11-19 | 2022-02-18 | 襄阳金耐特机械股份有限公司 | Low-temperature high-toughness nodular cast iron and application thereof |
| CN114058937B (en) * | 2021-11-19 | 2022-07-15 | 襄阳金耐特机械股份有限公司 | Low-temperature high-toughness nodular cast iron and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2730959B2 (en) | 1998-03-25 |
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