JPH08188856A - Ferritic heat resistant cast steel and its production - Google Patents

Ferritic heat resistant cast steel and its production

Info

Publication number
JPH08188856A
JPH08188856A JP1872595A JP1872595A JPH08188856A JP H08188856 A JPH08188856 A JP H08188856A JP 1872595 A JP1872595 A JP 1872595A JP 1872595 A JP1872595 A JP 1872595A JP H08188856 A JPH08188856 A JP H08188856A
Authority
JP
Japan
Prior art keywords
less
cast steel
resistant cast
heat
present
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.)
Pending
Application number
JP1872595A
Other languages
Japanese (ja)
Inventor
Kiwa Genma
喜和 弦間
Shinji Kato
真治 加藤
Masami Suzuki
正実 鈴木
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Toyota Motor Corp
Original Assignee
Toyota Motor Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Toyota Motor Corp filed Critical Toyota Motor Corp
Priority to JP1872595A priority Critical patent/JPH08188856A/en
Publication of JPH08188856A publication Critical patent/JPH08188856A/en
Pending legal-status Critical Current

Links

Landscapes

  • Exhaust Silencers (AREA)

Abstract

PURPOSE: To improve high strength and heat resistance such as thermal fatigue resistance without sacrificing oxidation resistance, machinability, and structural stability for them. CONSTITUTION: A steel, having a composition containing, by weight, 0.05-0.5% C, 1.0-2.0% Si, <0.6% Mn, <0.04% P, <O.04% S, <0.5% Ni, 10-20% Cr, 0.1-1.0% V, 0.5-1.0% Nb, 0.10-0.50% Mo, <0.01% W, 0.01-0.5O% Al, and at least one kind among 0.001-0.5% B, 0.05-0.5% Ti, and 0.1-5.0% Co, is cast and then held at 850-1000 deg.C for 1-5hr. Successively, the cast steel is cooled slowly down to <=700 deg.C to undergo annealing treatment.

Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【産業上の利用分野】本発明は、フェライト系耐熱鋳鋼
に係り、特に自動車用エンジンの排気系のエキゾースト
マニホールドやタービンハウジング等に用いて好適なフ
ェライト系耐熱鋳鋼に関する。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a ferritic heat-resistant cast steel, and more particularly to a ferritic heat-resistant cast steel suitable for use in an exhaust manifold of an automobile engine exhaust system, a turbine housing, or the like.

【0002】[0002]

【従来の技術】この種のエキゾーストマニホールドやタ
ービンハウジングには、従来一般には高Si 球状黒鉛鋳
鉄、ニレジスト等が用いられていたが、自動車用エンジ
ンの高出力化、低燃費化が進む中で、より耐熱性に優れ
た材料が望まれるようになってきている。耐熱性に優れ
た材料としては、高Ni 高Cr 系のオーステナイト系耐
熱鋼が良く知られているが、これらは鋳造性や機械加工
性に劣り、生産性とコストの点で実用性に乏しいという
問題があった。
2. Description of the Related Art In general, high Si spheroidal graphite cast iron, Niresist, etc. have been conventionally used for this kind of exhaust manifold and turbine housing. Materials having more excellent heat resistance have been desired. As a material having excellent heat resistance, a high Ni, high Cr system austenitic heat resistant steel is well known, but these are inferior in castability and machinability, and are not practical in terms of productivity and cost. There was a problem.

【0003】そこで最近、適度の鋳造性と機械加工性と
を備えているところから、高Cr フェライト系耐熱鋳鋼
が注目され、例えば特開平5−320830号公報に
は、重量%で、C: 0.05 〜0.5 、Si : 1.0〜2.0 、
Mn : 0.6未満、P:0.04未満、S:0.04未満、Ni :
0.5 未満、Cr :10〜20、V:0.1 〜1.0 、Nb : 0.5
〜1.0 、Mo : 0.1〜0.5 、W:0.01未満、Al :0.01
〜0.50から成るフェライト系耐熱鋳鋼が開示されてい
る。
Recently, therefore, high Cr ferritic heat-resistant cast steel has attracted attention because it has suitable castability and machinability. For example, in Japanese Patent Laid-Open No. 5-320830, C: 0.05 ~ 0.5, Si: 1.0 ~ 2.0,
Mn: less than 0.6, P: less than 0.04, S: less than 0.04, Ni:
Less than 0.5, Cr: 10 to 20, V: 0.1 to 1.0, Nb: 0.5
~ 1.0, Mo: 0.1 ~ 0.5, W: less than 0.01, Al: 0.01
A ferritic heat resistant cast steel consisting of .about.0.50 is disclosed.

【0004】[0004]

【発明が解決しようとする課題】しかしながら、上記公
報に開示されたフェライト系耐熱鋳鋼によれば、高温強
度や耐熱疲労性などの耐熱性がいま一つ不足し、最近の
自動車用エンジンに充分に対応しきれないという問題が
あった。
However, according to the ferritic heat-resistant cast steel disclosed in the above publication, the heat resistance such as high temperature strength and heat fatigue resistance is still insufficient, and it is sufficient for recent automobile engines. There was a problem that we could not handle it.

【0005】本発明は、上記従来の問題を解決すること
を課題としてなされたもので、その目的とするところ
は、耐熱性のより一層の向上を図り、もって自動車用エ
ンジンの排気系への適用性を高めたフェライト系耐熱鋳
鋼を提供し、併せてその製造方法を提供することにあ
る。
The present invention has been made to solve the above-mentioned conventional problems, and an object thereof is to further improve heat resistance and thus to be applied to an exhaust system of an automobile engine. It is to provide a ferritic heat-resistant cast steel having improved heat resistance and a method for manufacturing the same.

【0006】[0006]

【課題を解決するための手段】上記目的を達成するた
め、本発明にかゝるフェライト系耐熱鋳鋼は、その基本
成分を、重量%(wt%)で、C: 0.05 〜0.5 、Si :
1.0〜2.0 、Mn : 0.6未満、P:0.04未満、S:0.04
未満、Ni :0.5 未満、Cr :10〜20、V:0.1〜1.0
、Nb : 0.5〜1.0 、Mo : 0.1〜0.5 、W:0.01未
満、Al :0.01〜0.50、およびB: 0.001〜0.5 ,Ti
:0.05〜0.5 ,Co : 0.1〜5.0 のうちの少なくとも
一種から成るようにしたことを特徴とする。
In order to achieve the above object, the heat-resistant ferritic cast steel according to the present invention has a basic composition of C: 0.05 to 0.5, Si:
1.0 to 2.0, Mn: less than 0.6, P: less than 0.04, S: 0.04
Less, Ni: less than 0.5, Cr: 10-20, V: 0.1-1.0
, Nb: 0.5 to 1.0, Mo: 0.1 to 0.5, W: less than 0.01, Al: 0.01 to 0.50, and B: 0.001 to 0.5, Ti.
: 0.05 to 0.5 and Co: 0.1 to 5.0.

【0007】また、本発明にかゝるフェライト系耐熱鋳
鋼の製造方法は、上記成分を有する素材を鋳造した後、
850〜1000℃に1〜5時間保持し、引き続いて700 ℃以
下の温度まで徐冷する焼なまし処理を行うようにしたこ
とを特徴とする。
Further, the method for producing a ferritic heat-resistant cast steel according to the present invention comprises:
It is characterized in that it is kept at 850 to 1000 ° C. for 1 to 5 hours, and subsequently subjected to an annealing treatment of gradually cooling to a temperature of 700 ° C. or less.

【0008】こゝで、本発明における成分限定理由につ
いて説明すると、Cは、強度と靭性の向上および溶湯の
流動性(鋳造性)の改善に有効であるが、0.05重量(w
t)%未満ではそれらの効果が充分でなく、一方0.50wt
%を越えると耐酸化性を悪化させかつ共析変態温度を下
げてオーステナイトの析出をもたらすので、これを 0.0
5 〜0.50wt%とした。
Here, the reason for limiting the components in the present invention will be explained. C is effective for improving the strength and toughness and improving the fluidity (castability) of the molten metal, but 0.05% by weight (w
Below t)%, their effects are not sufficient, while 0.50wt%
%, It deteriorates the oxidation resistance and lowers the eutectoid transformation temperature, resulting in the precipitation of austenite.
It was set to 5 to 0.50 wt%.

【0009】Si は、耐酸化性を改善し、共析変態温度
を上昇させ、また脱酸剤として有効であるが、1.0 wt%
未満ではそれらの効果が充分でなく、一方2.0 wt%を越
えると低温(常温)での靭性を悪化させかつ高温での強
度を低下させるので、これを1.0〜2.0 wt%とした。
Si improves the oxidation resistance, raises the eutectoid transformation temperature, and is effective as a deoxidizing agent, but 1.0 wt%
If less than 2.0% by weight, the effects are not sufficient, while if over 2.0% by weight, the toughness at low temperature (normal temperature) is deteriorated and the strength at high temperature is reduced, so this was made 1.0 to 2.0% by weight.

【0010】Mn は、パーライト組織の形成元素である
ことから、本発明のように基地をフェライト組織とする
耐熱鋳鋼には余り好ましくなく、また強度を低下させる
ので、これを0.6 wt%未満と低く抑えた。
Since Mn is an element for forming a pearlite structure, it is not very preferable for the heat-resistant cast steel having a ferrite structure as the matrix as in the present invention, and it lowers the strength, so that it is as low as less than 0.6 wt%. Suppressed.

【0011】P,Sは、0.04wt%以上では熱亀裂(ヒー
トクラック)の発生を助長するので、これを有害な不純
物扱いとして0.04wt%未満に低く抑えた。
When P and S are more than 0.04 wt%, the generation of heat cracks (heat cracks) is promoted, so P and S are treated as harmful impurities and are suppressed to less than 0.04 wt%.

【0012】Ni は、共析変態温度を低下させてオース
テナイトの析出を促してフェライト組織を不安定にする
ので、これを0.5 wt%未満と低く抑えた。
[0012] Ni lowers the eutectoid transformation temperature to promote the precipitation of austenite and destabilizes the ferrite structure.

【0013】Cr は、耐酸化性を改善しかつ共析変態温
度を上昇させることからきわめて有用な元素であるが、
10wt%未満ではそれらの効果が充分でなく、一方20wt%
を越えると低温での靭性を低下させ、かつ粗大な一次炭
化物の晶出を促して機械加工性を著しく悪化させるの
で、これを10〜20wt%とした。
Cr is an extremely useful element because it improves oxidation resistance and raises the eutectoid transformation temperature.
If it is less than 10 wt%, those effects are not sufficient, while 20 wt%
If it exceeds, the toughness at low temperature is lowered, and crystallization of coarse primary carbides is promoted to significantly deteriorate the machinability, so this is set to 10 to 20 wt%.

【0014】Vは、共析変態温度を大きく上昇させ、ま
たCr に優先して炭化物を形成して、機械加工性を悪化
させるCr の一次炭化物の形成を抑制することから、本
発明において特に重要な元素の一つであるが、0.1 wt%
未満ではそれらの効果が充分でなく、一方1.0 wt%を越
えると耐酸化性の悪化を招きかつ高温での強度を低下さ
せるので、これを0.1 〜1.0 wt%とした。
V significantly increases the eutectoid transformation temperature, forms carbides in preference to Cr, and suppresses the formation of primary carbides of Cr, which deteriorates machinability. Therefore, V is particularly important in the present invention. It is one of the major elements, but 0.1 wt%
If the amount is less than 1.0%, the effects are not sufficient, while if it exceeds 1.0% by weight, the oxidation resistance is deteriorated and the strength at high temperature is lowered, so the content was made 0.1 to 1.0% by weight.

【0015】Nb は、Vと同様に共析変態温度を大きく
上昇させ、またCr に優先して炭化物を形成して、機械
加工性を悪化させるCr の一次炭化物の形成を抑制し、
しかも高温における二次炭化物の析出を抑制して耐酸化
性を向上させる効果を有するが、0.5 wt%未満ではそれ
らの効果が充分でなく、一方1.0 wt%を越えると多量の
炭化物を形成して母相中のC量を著しく減少させ、強度
低下を招くので、これを0.5 〜1.0 wt%とした。
Nb, like V, greatly increases the eutectoid transformation temperature, forms carbides in preference to Cr, and suppresses the formation of primary carbides of Cr which deteriorates machinability.
Moreover, it has the effect of suppressing the precipitation of secondary carbides at high temperatures and improving the oxidation resistance, but if it is less than 0.5 wt%, those effects are not sufficient, while if it exceeds 1.0 wt%, a large amount of carbides are formed. Since the amount of C in the mother phase is remarkably reduced and the strength is lowered, this is set to 0.5 to 1.0 wt%.

【0016】Mo は、強度を向上させかつ共析変態温度
を上昇させる効果を有するが、0.10wt %未満ではそれ
らの効果が充分でなく、一方0.50wt%を越えると低温で
の靭性を低下させかつ耐酸化性を悪化させるので、これ
を 0.10 〜0.50wt%とした。
Mo has the effect of improving the strength and raising the eutectoid transformation temperature, but if it is less than 0.10 wt%, these effects are not sufficient, while if it exceeds 0.50 wt%, the toughness at low temperatures decreases. In addition, since the oxidation resistance is deteriorated, this is set to 0.10 to 0.50 wt%.

【0017】Wは、耐酸化性を著しく悪化させる有害な
元素であるので、本発明ではこれを不純物扱いとして0.
01wt%未満の低い値に抑えた。
Since W is a harmful element which significantly deteriorates the oxidation resistance, it is treated as an impurity in the present invention in an amount of 0.1.
The value was suppressed to a low value of less than 01wt%.

【0018】Al は、結晶粒を微細化して熱疲労寿命を
著しく延長させるが、0.01wt%未満ではそれらの効果が
充分でなく、一方0.50wt%を越えると低温での靭性を低
下させるので、これを0.01〜0.50wt%とした。
Al makes the crystal grains finer and prolongs the thermal fatigue life remarkably, but if it is less than 0.01 wt%, these effects are not sufficient, while if it exceeds 0.50 wt%, the toughness at low temperature decreases. This was set to 0.01 to 0.50 wt%.

【0019】Bは、結晶粒を微細化して熱疲労寿命を著
しく延長させるため、本発明において特に重要な元素で
あるが、0.001 wt%未満ではその効果が充分でなく、0.
5wt%を越えると低温での靭性を低下させるので、これ
を 0.001〜0.5wt %とした。
B is a particularly important element in the present invention because it refines the crystal grains to prolong the thermal fatigue life remarkably, but if it is less than 0.001 wt%, its effect is not sufficient, and
If it exceeds 5% by weight, the toughness at low temperature decreases, so this was made 0.001 to 0.5% by weight.

【0020】Ti は、結晶粒を微細化して熱疲労寿命を
著しく延長させるため、Bと同様に極めて重要な元素で
あるが、0.05wt%未満ではその効果が充分でなく、0.5w
t %を越えると低温での靭性を低下させるので、これを
0.05〜0.5wt %とした。
Ti is an extremely important element like B because it refines the crystal grains and prolongs the thermal fatigue life remarkably, but if it is less than 0.05 wt%, its effect is not sufficient and 0.5 w.
If it exceeds t%, the toughness at low temperature will decrease.
It was set to 0.05 to 0.5 wt%.

【0021】Co は、高温強度を著しく向上させるた
め、本発明において特に重要な元素であるが、0.1 wt%
未満ではその効果が充分でなく、5.0wt %を越えると靭
性を低下させるので、これを 0.1〜5.0 wt%とした。
Co is a particularly important element in the present invention because it remarkably improves the high temperature strength.
If it is less than 5.0 wt%, the effect is not sufficient, and if it exceeds 5.0 wt%, the toughness decreases, so this was made 0.1 to 5.0 wt%.

【0022】[0022]

【作用】上記のように構成したフェライト系耐熱鋳鋼に
おいては、Mn 、Ni 、Wを低く抑える一方で、C,S
i ,Cr ,V,Nb ,Mo ,Al ,B,Ti ,Co 等を
所定の割合で含有させたので、耐酸化性、機械加工性、
組織的安定性などを損なうことなく耐熱強度、耐熱疲労
性を大幅の向上を図ることができる。さらに、鋳造後に
所定の温度に保持し引続いて徐冷する焼なまし処理を行
うことにより、マルテンサイトが分解してフェライト組
織となる。
In the ferritic heat-resistant cast steel configured as described above, Mn, Ni, and W are kept low, while C, S
Since i, Cr, V, Nb, Mo, Al, B, Ti, Co, etc. are contained at a predetermined ratio, oxidation resistance, machinability,
The heat resistance and heat fatigue resistance can be significantly improved without impairing the structural stability. Further, by carrying out an annealing treatment of maintaining a predetermined temperature after casting and then gradually cooling, martensite is decomposed to form a ferrite structure.

【0023】[0023]

【実施例】以下、本発明の実施例を添付図面も参照して
説明する。
Embodiments of the present invention will be described below with reference to the accompanying drawings.

【0024】表1に示すようにC、Si 、Ni 、Cr 、
V、Nb 、Mo 、Al を含む基本組成(P、S、Wは不
可避不純物)に対してB、Ti 、Co を単独にまたは複
合添加した本発明材1〜8を鋳造し、この鋳造材に93
0℃に3時間保持した後、650℃まで炉冷(徐冷)す
る焼なまし処理を施し、その後、各鋳造材から所定の試
験片を採取してそれぞれを後述する熱疲労試験および高
温引張り試験に供した。なお、比較のため、表2に示す
ように本発明材の基本組成(B、Ti 、Co を取り除い
た)を有する比較材9,10、汎用の高Si 球状黒鉛鋳
鉄である比較材11、ニレジストである比較材12およ
びJIS SCH1である比較材13を鋳造し、比較材
11(高Si 球状黒鉛鋳鉄)および比較材12(ニレジ
スト)については鋳造のまゝとし、比較材13(SCH
1)については鋳造材に850℃に2時間保持した後、
600℃まで炉冷する焼なまし処理を施し、それぞれを
熱疲労試験および高温引張り試験に供した。こゝで、熱
疲労試験は直径10mm、長さ15mmの切欠付試験片を両
端固定し(拘束率100%)、200℃から950℃の
熱サイクルを与えて破断するまでの繰返し数を求める方
法により行い、高温引張り試験は950で行った。
As shown in Table 1, C, Si, Ni, Cr,
Materials 1 to 8 of the present invention in which B, Ti, and Co are added individually or in combination to a basic composition containing V, Nb, Mo, and Al (P, S, and W are unavoidable impurities) are cast. 93
After holding it at 0 ° C for 3 hours, it was annealed by furnace cooling (gradual cooling) to 650 ° C, and then, predetermined test pieces were taken from each casting material and subjected to the thermal fatigue test and high temperature tensile test described below. It was submitted to the test. For comparison, as shown in Table 2, Comparative Materials 9 and 10 having the basic composition of the material of the present invention (B, Ti and Co are removed), Comparative Material 11 which is general-purpose high Si spheroidal graphite cast iron, Niresist Comparative material 12 and JIS SCH1 comparative material 13 were cast, and comparative material 11 (high Si spheroidal graphite cast iron) and comparative material 12 (niresist) were left as casting, and comparative material 13 (SCH
Regarding 1), after holding the cast material at 850 ° C. for 2 hours,
It was annealed by furnace cooling to 600 ° C. and subjected to a thermal fatigue test and a high temperature tensile test. Here, the thermal fatigue test is a method of fixing the both ends of a notched test piece having a diameter of 10 mm and a length of 15 mm (restriction rate 100%), and applying a heat cycle from 200 ° C to 950 ° C to obtain the number of repetitions until breakage. The high temperature tensile test was performed at 950.

【0025】[0025]

【表1】[Table 1]

【0026】[0026]

【表2】[Table 2]

【0027】図1は、熱疲労試験の結果を示したもので
ある。同図に示す結果より、基本組成に対してBを単独
添加した本発明材1,2、Ti を単独添加した本発明材
3,4、B,Ti ,Co を複合添加した本発明材7,8
の熱疲労寿命は、何れも従来汎用の比較材11〜13よ
り大幅に延長すると共に、本発明の基本組成である比較
材9および10よりも延長し、耐熱疲労性に著しく優れ
ていることが明らかとなった。なお、本発明材の中で
は、B,Ti ,Co を複合添加したものが、これらを単
独添加したものより熱疲労寿命は延長している。また、
全体として各元素を低目に添加したものが、全体として
各元素を高目に添加したものよりもわずかに熱疲労寿命
が延長する傾向にあるが、これは靭性の差から生じたも
のと推量される。
FIG. 1 shows the result of the thermal fatigue test. From the results shown in the figure, the present invention materials 1 and 2 in which B was added alone to the basic composition, the invention materials 3 and 4 in which Ti was added alone, and the invention material 7 in which B, Ti and Co were added in combination, 8
The thermal fatigue lives of all of the materials are significantly longer than those of the conventional general-purpose comparative materials 11 to 13, and are also longer than those of the comparative materials 9 and 10 which are the basic compositions of the present invention, and thus are significantly excellent in heat fatigue resistance. It became clear. Among the materials of the present invention, the composite addition of B, Ti and Co has a longer thermal fatigue life than the addition of these alone. Also,
As a whole, when each element was added at a low level, the thermal fatigue life tended to be slightly extended compared to when each element was added at a high level, but it is assumed that this was caused by the difference in toughness. To be done.

【0028】図2は、高温引張り試験の結果を示したも
のである。同図に示す結果より、基本組成に対してCo
を単独添加した本発明材5,6、B,Ti ,Co を複合
添加した本発明材7,8の引張強さは、何れも従来汎用
の比較材11〜13より大幅に増大すると共に、本発明
の基本組成である比較材9および10よりも増大し、高
温強度に著しく優れていることが明らかとなった。な
お、本発明材の中では、全体として各元素を高目に添加
したものが、全体として各元素を低目に添加したものよ
りも引張強さが増大する傾向にある。
FIG. 2 shows the results of the high temperature tensile test. From the results shown in the figure, the Co
The tensile strengths of the present invention materials 5 and 6, which are added alone, and the present invention materials 7 and 8 to which B, Ti, and Co are added in addition, are significantly increased as compared with the conventional general-purpose comparative materials 11 to 13, and It was revealed that the strength was higher than that of the comparative materials 9 and 10 which are the basic compositions of the invention, and that the high temperature strength was remarkably excellent. In addition, among the materials of the present invention, those in which each element is added at a higher level as a whole tend to have a higher tensile strength than those in which each element is added at a low level as a whole.

【0029】[0029]

【発明の効果】以上、詳細に説明したように、本発明に
かゝるフェライト系耐熱鋳鋼によれば、耐酸化性、機械
加工性、組織的安定性などを損なうことなく耐熱強度、
耐熱疲労性の大幅な向上を図ることができ、例えば自動
車の高出力エンジンの排気系に適用して充分なる性能を
発揮するものとなる。また、耐熱性が向上する分、薄肉
化を図ることができ、軽量化にも寄与するものとなる。
さらに、本発明にかゝるフェライト系耐熱鋳鋼の製造方
法によれば、フェライト組織を安定して得ることがで
き、所望の耐熱性の確保に大きく寄与する。
As described above in detail, according to the ferritic heat-resistant cast steel according to the present invention, the heat-resistant strength without impairing the oxidation resistance, machinability, structural stability, etc.,
The thermal fatigue resistance can be greatly improved, and sufficient performance can be exerted when applied to, for example, an exhaust system of a high-power engine of an automobile. Further, since the heat resistance is improved, the wall thickness can be reduced, which contributes to the weight reduction.
Further, according to the method for producing a ferritic heat-resistant cast steel according to the present invention, a ferrite structure can be stably obtained, which greatly contributes to ensuring desired heat resistance.

【図面の簡単な説明】[Brief description of drawings]

【図1】本フェライト系耐熱鋳鋼の耐熱疲労性を比較材
と対比して示すグラフである。
FIG. 1 is a graph showing the thermal fatigue resistance of the present ferritic heat-resistant cast steel in comparison with a comparative material.

【図2】本フェライト系耐熱鋳鋼の高温強度を比較材と
対比して示すグラフである。
FIG. 2 is a graph showing high temperature strength of the present ferritic heat resistant cast steel in comparison with a comparative material.

Claims (2)

【特許請求の範囲】[Claims] 【請求項1】 重量%で、C: 0.05 〜0.5 、Si :
1.0〜2.0 、Mn : 0.6未満、P:0.04未満、S:0.04
未満、Ni :0.5 未満、Cr :10〜20、V:0.1 〜1.0
、Nb : 0.5〜1.0 、Mo : 0.1〜0.5 、W:0.01未
満、Al :0.01〜0.50、およびB: 0.001〜0.5 ,Ti
:0.05〜0.5 ,Co : 0.1〜5.0 のうちの少なくとも
一種から成ることを特徴とするフェライト系耐熱鋳鋼。
1. By weight%, C: 0.05 to 0.5, Si:
1.0 to 2.0, Mn: less than 0.6, P: less than 0.04, S: 0.04
Less, Ni: less than 0.5, Cr: 10-20, V: 0.1-1.0
, Nb: 0.5 to 1.0, Mo: 0.1 to 0.5, W: less than 0.01, Al: 0.01 to 0.50, and B: 0.001 to 0.5, Ti.
: 0.05 to 0.5, Co: 0.1 to 5.0, at least one kind of ferritic heat-resistant cast steel.
【請求項2】 請求項1に記載の成分を有する素材を鋳
造した後、 850〜1000℃で1〜5時間保持し、引き続い
て700 ℃以下の温度まで徐冷する焼なまし処理を行うこ
とを特徴とするフェライト系耐熱鋳鋼の製造方法。
2. After casting the material having the components according to claim 1, holding the material at 850 to 1000 ° C. for 1 to 5 hours, and subsequently performing an annealing treatment of gradually cooling it to a temperature of 700 ° C. or less. A method for producing a ferritic heat-resistant cast steel, characterized by:
JP1872595A 1995-01-11 1995-01-11 Ferritic heat resistant cast steel and its production Pending JPH08188856A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP1872595A JPH08188856A (en) 1995-01-11 1995-01-11 Ferritic heat resistant cast steel and its production

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP1872595A JPH08188856A (en) 1995-01-11 1995-01-11 Ferritic heat resistant cast steel and its production

Publications (1)

Publication Number Publication Date
JPH08188856A true JPH08188856A (en) 1996-07-23

Family

ID=11979652

Family Applications (1)

Application Number Title Priority Date Filing Date
JP1872595A Pending JPH08188856A (en) 1995-01-11 1995-01-11 Ferritic heat resistant cast steel and its production

Country Status (1)

Country Link
JP (1) JPH08188856A (en)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1553198A1 (en) * 2002-06-14 2005-07-13 JFE Steel Corporation Heat-resistant ferritic stainless steel and method for production thereof
EP2316981A4 (en) * 2009-04-27 2013-08-21 Aisin Takaoka Ltd Ferritic heat-resistant cast steel and exhaust system component

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1553198A1 (en) * 2002-06-14 2005-07-13 JFE Steel Corporation Heat-resistant ferritic stainless steel and method for production thereof
EP1553198A4 (en) * 2002-06-14 2005-07-13 Jfe Steel Corp Heat-resistant ferritic stainless steel and method for production thereof
US7806993B2 (en) 2002-06-14 2010-10-05 Jfe Steel Corporation Heat-resistant ferritic stainless steel and method for production thereof
EP2316981A4 (en) * 2009-04-27 2013-08-21 Aisin Takaoka Ltd Ferritic heat-resistant cast steel and exhaust system component
US8721808B2 (en) 2009-04-27 2014-05-13 Aisin Takaoka Co., Ltd. Ferrite system heat-resistant cast steel and exhaust system component

Similar Documents

Publication Publication Date Title
JPH0734202A (en) Steam turbine rotor
JPH02290950A (en) Ferritic heat resisting steel excellent in strength at high temperature
JPH0559498A (en) Ferritic heat resistant cast steel and its manufacture
JP2002212634A (en) Method for producing austenitic heat resistant steel tue having excellent creep rupture strength
JPS5834129A (en) Heat-resistant metallic material
JP2947913B2 (en) Rotor shaft for high temperature steam turbine and method of manufacturing the same
US5106578A (en) Cast-to-near-net-shape steel body of heat-resistant cast steel
JP3121478B2 (en) Ferritic heat-resistant cast steel and method for producing the same
JP2001073092A (en) 9-12% Cr HEAT RESISTING STEEL EXCELLENT IN HIGH TEMPERATURE STRENGTH AND TOUGHNESS, AND ITS MANUFACTURE
JPH11241145A (en) Austenitic stainless steel excellent in high temperature setting resistance and its production
JPH08188856A (en) Ferritic heat resistant cast steel and its production
JPH10195587A (en) Spheroidal graphite cast iron and exhaust manifold excellent in intermediate temperature ductility, and production thereof
JPH07197209A (en) Ferritic heat resistant cast steel excellent in castability and exhaust system parts made thereof
JPH07238349A (en) Heat resistant steel
JPH0770713A (en) Heat resistant cast steel
JPH05320830A (en) Ferritic heat resistant cast steel and its manufacture
JP2000273582A (en) Cast steel for pressure vessel and production of pressure vessel using the same
JPH1036944A (en) Martensitic heat resistant steel
JPH1068050A (en) Stainless steel for spring excellent in thermal settling resistance
JP6745050B2 (en) Ni-based alloy and heat-resistant plate material using the same
JPH0524977B2 (en)
JPH10130790A (en) Heat resistant alloy excellent in cold workability and overaging characteristic
JPS6233744A (en) Heat-resistant cast steel
JPH0359967B2 (en)
JPH04147949A (en) Heat-resistant alloy for engine valve