JPH03226547A - High toughness fe-al intermetallic compound material - Google Patents
High toughness fe-al intermetallic compound materialInfo
- Publication number
- JPH03226547A JPH03226547A JP1801090A JP1801090A JPH03226547A JP H03226547 A JPH03226547 A JP H03226547A JP 1801090 A JP1801090 A JP 1801090A JP 1801090 A JP1801090 A JP 1801090A JP H03226547 A JPH03226547 A JP H03226547A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- intermetallic compound
- toughness
- feal
- oxidation resistance
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000765 intermetallic Inorganic materials 0.000 title claims abstract description 19
- 239000000463 material Substances 0.000 title claims abstract description 16
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 15
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 15
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910015372 FeAl Inorganic materials 0.000 claims description 23
- 239000012535 impurity Substances 0.000 claims description 7
- 230000003647 oxidation Effects 0.000 abstract description 11
- 238000007254 oxidation reaction Methods 0.000 abstract description 11
- 229910052796 boron Inorganic materials 0.000 abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 abstract description 3
- 239000003779 heat-resistant material Substances 0.000 abstract description 2
- 230000007547 defect Effects 0.000 abstract 2
- 230000000694 effects Effects 0.000 description 7
- 150000001875 compounds Chemical class 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 238000002474 experimental method Methods 0.000 description 4
- 230000005484 gravity Effects 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- 239000000919 ceramic Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 239000013585 weight reducing agent Substances 0.000 description 3
- 238000005266 casting Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 239000004615 ingredient Substances 0.000 description 2
- 238000010587 phase diagram Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910017372 Fe3Al Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013256 coordination polymer Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 238000005495 investment casting Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000013021 overheating Methods 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000003313 weakening effect Effects 0.000 description 1
- 230000004584 weight gain Effects 0.000 description 1
- 235000019786 weight gain Nutrition 0.000 description 1
Classifications
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
- F02B—INTERNAL-COMBUSTION PISTON ENGINES; COMBUSTION ENGINES IN GENERAL
- F02B3/00—Engines characterised by air compression and subsequent fuel addition
- F02B3/06—Engines characterised by air compression and subsequent fuel addition with compression ignition
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は高靭性ＦｅＡｌ金属間化合物材料に係り、特に
軽量、耐酸化性を損わず脆さを克服したＰｅＡｌ金属間
化合物材料に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a high-toughness FeAl intermetallic material, and particularly to a PeAl intermetallic material that is lightweight and overcomes brittleness without impairing oxidation resistance.
従来は、耐熱材料として、ステンレスに代表されるＮｉ
基、Ｃｏ基、Ｆｅ基という高価な材料が使用されてきた
。これらの材料は、Ｎｉが含有されているため非常に高
価であり、また重いという欠点を持っている。それに対
してＦｅＡｌは、金属間化合物であり軽量と言う利点が
あり、また融点も第８図のＦｅ−Ａｌの２元状態図に示
したように１２５０℃と言う比較的高い値であり、構造
変化も少ないと言うことで研究され出している。Conventionally, Ni, typified by stainless steel, has been used as a heat-resistant material.
Expensive materials such as Co-based, Co-based, and Fe-based have been used. These materials have the disadvantage of being very expensive and heavy because they contain Ni. On the other hand, FeAl is an intermetallic compound and has the advantage of being lightweight, and has a relatively high melting point of 1250°C, as shown in the Fe-Al binary phase diagram in Figure 8, and has a structure It is being studied because it shows little change.
ＦｅＡｌ金属間化合物は上記の如く、軽量で高融点で構
造変化が少ない等の利点はあるが、本質的に脆い欠点を
有する。このためＭａｔｅｒｉａｌｓ ５ｃｉｅｎｃｅ
ａｎｄ Ｅｎｇｉｎｅｅｒｉｎｇ ７７ （１９８６）
１０３−１１３のＴｈｅＩｎｆｌｕｅｎｃｅ ｏｆ
Ｇｒａｉｎ Ｓｉｇｅ ａｎｄ Ｃｏｍｐｏｓ＋ｔｌ
ｏｎ ｏｎＳｌｏｗ Ｐｌａｓｔｉ’ｃ Ｆｌｏｗ ｉ
ｎ ＦｅＡｌ ｂｅｔｗｅｅｎ １ｌＱＱ ａｎｄ１４
００Ｋに開示されているように急冷によって結晶粒を微
細化する方法も研究されている。しかし急冷であると、
作られる製品に限度がありさらに高温で使うと結晶粒が
成長してしまう欠点もある。As mentioned above, the FeAl intermetallic compound has advantages such as being lightweight, having a high melting point, and having little structural change, but has the drawback that it is inherently brittle. For this reason, Materials 5science
and Engineering 77 (1986)
103-113 The Influence of
Grain Sige and Compos+tl
on onSlow Plastic'c Flow i
n FeAl between 1lQQ and14
A method of refining crystal grains by rapid cooling is also being studied, as disclosed in 00K. However, if it is rapidly cooled,
There is a limit to the products that can be made, and there is also the disadvantage that crystal grains grow when used at high temperatures.
本発明は、その軽量、耐酸化性という特徴を損なわず、
脆さを克服した高靭性ＦｅＡｌ金属間化合物を提供する
ことを目的とする。The present invention does not impair its characteristics of light weight and oxidation resistance,
The purpose of the present invention is to provide a high toughness FeAl intermetallic compound that overcomes brittleness.
上記課題は本発明によればＡｌ２２〜３２重量％；Ｃｒ
、Ｗ及びＭｏのうち少なくとも１種を含有し、しかもＣ
ｒ、Ｗ及びＭｏの総和が３〜１２重量％：残部Ｆｅ及び
不可避的不純物からなる高靭性ＦｅＡｌ金属間化合物材
料によって解決される。According to the present invention, the above problem can be solved by
, W and Mo, and contains C
The problem is solved by a high toughness FeAl intermetallic compound material in which the sum of r, W and Mo is 3 to 12% by weight: the balance is Fe and unavoidable impurities.
本発明ではＦｅＡｌ金属間化合物にＣｒ 、Ｗ １Ｍ。In the present invention, 1M of Cr and W are added to the FeAl intermetallic compound.
を所定量添加した成分を有しており、Ａｌ量を２２〜３
２重量％とじた理由はＡｌが２２重量％未満であるとＦ
ｅＡｌの性質が弱まり、ＦｅＡｌからＦｅ３Ａｌに変化
し耐熱性が劣下し、一方ＡＩが３２重量％を超えると脆
くなり実用不可能になる。靭性の面からはＦｅが多いこ
とが好ましく２２〜２８重量％が特に好ましい。またＣ
ｒ、Ｗ及びＭｏの総和を３〜１２重量％とした理由は３
重量％未満では衝撃特性が低下し、１２重量％を超える
とＦｅＡｌ本来の軽量、耐酸化性が低下するためである
。なお本成分に更にＢ（ボロン）を０．１〜１．５重量
％添加により靭性の向上を図れる。また不可避的不純物
とはＳ・ＣＰ、Ｎｉ ＝Ｍｎ 、Ｔｉ等である。更に
上記課題は本発明によればＡｌ２２〜３２重量；Ｃｒ
２〜１２重量％；Ｗ、Ｍｏのうち少なくとも１種を含有
しＷとＭｏの総和が１〜５重量％；残部Ｆｅ及び不可避
的不純物からなる高靭性ＦｅＡｌ金属間化合物材料によ
って解決される。The aluminum content is 22 to 3.
The reason why it is limited to 2% by weight is that if Al is less than 22% by weight, F
The properties of eAl weaken and change from FeAl to Fe3Al, resulting in poor heat resistance.On the other hand, if AI exceeds 32% by weight, it becomes brittle and becomes impractical. From the viewpoint of toughness, it is preferable that the Fe content is large, and 22 to 28% by weight is particularly preferable. Also C
There are 3 reasons why the total amount of r, W and Mo is 3 to 12% by weight.
This is because if it is less than 12% by weight, the impact properties will deteriorate, and if it exceeds 12% by weight, the inherent light weight and oxidation resistance of FeAl will decrease. The toughness can be improved by adding 0.1 to 1.5% by weight of B (boron) to this component. In addition, unavoidable impurities include S.CP, Ni=Mn, Ti, and the like. Furthermore, according to the present invention, the above-mentioned problem can be solved with Al22-32 weight; Cr
The problem is solved by a high-toughness FeAl intermetallic compound material containing at least one of W and Mo, with the total amount of W and Mo being 1 to 5% by weight; the balance being Fe and unavoidable impurities.
本成分中ＡＩの制限は上記と同様であるがＷとＭｏの総
和を１〜５重量％とした理由は熱膨張を下げ、しかもあ
る程度軽量化を図るためであり、Ｃｒ量を２〜１２重量
％とした理由は靭性を確保するためである。本成分にＢ
を０．１〜１．５重量％添加することは上記と同様に靭
性向上のために好ましい。The restrictions on AI in this component are the same as above, but the reason why the total amount of W and Mo is set at 1 to 5% by weight is to reduce thermal expansion and to reduce the weight to some extent, and the amount of Cr is set at 2 to 12% by weight. % is to ensure toughness. B in this ingredient
It is preferable to add 0.1 to 1.5% by weight of 0.1 to 1.5% by weight in order to improve toughness as mentioned above.
本発明では比重が小さく融点が高いＦｅＡｌ金属間化合
物に、Ｃｒ 、’ｖＶ、Ｍｏ及びＢを所定量添加するこ
とによりＦｅ−Ａｌ共有結合を減少させ金属結合を増大
させることができるので靭性を向上させることができる
。In the present invention, by adding predetermined amounts of Cr, 'vV, Mo, and B to the FeAl intermetallic compound with low specific gravity and high melting point, it is possible to reduce Fe-Al covalent bonds and increase metallic bonds, thereby improving toughness. can be done.
まず金属間化合物ＦｅＡｌ材料の脆性を改良するためＦ
ｅＡｌにいくつかの元素を添加して実験したので説明す
る。First, in order to improve the brittleness of the intermetallic compound FeAl material, F
An experiment was conducted by adding several elements to eAl, which will be explained below.
その実験の結果脆性を解消する成分として周期律表第６
Ａ属元素のＣｒ １Ｍｏ 、ＷｚさらにＢ（ボロン）の
添加が効果のあることがわかった。As a result of the experiment, the sixth component of the periodic table was found to be a component that eliminates brittleness.
It has been found that addition of group A elements Cr 1Mo and Wz as well as B (boron) is effective.
第表１にその結果を示す。本実験のＦｅ、ＡＩ材料の靭
性の確認は、
官能的に行い、
靭性を×Ｘ〜◎で評
価した。Table 1 shows the results. The toughness of the Fe and AI materials in this experiment was confirmed sensually, and the toughness was evaluated as ×X to ◎.
第１表
実験結果
第１表
実験結果続き
ＦｅＡｌの脆さは、Ｆｅ−Ａｌの共有結合の強さが影響
すると思われる。このため６Ａ属元素を添加すると、こ
の第６Ａ属元素がＦｅＡｌのＡＩ側に置換しＦｅ−Ａｌ
共有結合を弱め、金属結合を増加させる働きをすること
で、靭性が向上すると思われる。Table 1 Experimental Results Table 1 Experimental Results Continued The brittleness of FeAl is thought to be affected by the strength of the Fe-Al covalent bond. Therefore, when a 6A group element is added, this 6A group element is substituted on the AI side of FeAl, and the Fe-Al
Toughness is thought to be improved by weakening covalent bonds and increasing metallic bonds.
ＡＩの量としては、第１表で分かるように、３３重量％
以上であると、脆く実際の使用には耐えない。化学量論
組成よりＦｅ リッチ側の方が靭性をもつようになり望
ましい。しかし２２重量％以下であるとＦｅＡ ｌの性
質が弱まりＦｅ、ＡＩになり、耐熱性が劣る。２２重量
％以下であると第１図に示すように耐酸化性が低下する
。従って、ＡＩ量として２２〜３２重量％とした。靭性
の面から望ましくは２２〜２８重量％である。これは、
Ｆｅ リッチであると、ＦｅＡｌの共有結合性が低下
する為と考えられる。As shown in Table 1, the amount of AI is 33% by weight.
If it is more than that, it becomes brittle and cannot withstand actual use. The Fe-rich side is more desirable than the stoichiometric composition because it provides toughness. However, if it is less than 22% by weight, the properties of FeAl weaken and become Fe and AI, resulting in poor heat resistance. If it is less than 22% by weight, the oxidation resistance decreases as shown in FIG. Therefore, the amount of AI was set at 22 to 32% by weight. From the viewpoint of toughness, the content is preferably 22 to 28% by weight. this is,
This is considered to be because the covalent bonding property of FeAl decreases when it is Fe rich.
Ｃｒ 、Ｗ、Ｍｏの量は、第１表に示すように、ある
程度添加すると効果が顕著になる。このためＣｒ ＋Ｍ
ｏ ＋Ｗの量で評価することにし衝撃値で評価した。そ
の結果を第２図に示す。この値は、Ａｌ２８重■％で、
８０９５重量％添加した値である。As shown in Table 1, when Cr, W, and Mo are added in a certain amount, the effect becomes noticeable. For this reason, Cr +M
It was decided to evaluate by the amount of o + W, and the impact value was evaluated. The results are shown in FIG. This value is Al28 weight ■%,
This value represents an addition of 8095% by weight.
第２図に示すように、３重量％以下では効果が少ない。As shown in FIG. 2, if it is less than 3% by weight, the effect is small.
また１２重量％以上であるとＦｅＡｌ本来の軽量、耐酸
化性が損なわれる。このため３〜１２重量％に規定した
。Moreover, if it is 12% by weight or more, the original light weight and oxidation resistance of FeAl will be impaired. For this reason, it is specified to be 3 to 12% by weight.
尚、耐熱性を高める方法の一つに熱膨張率の低下がある
が、単体の熱膨張率はＷｌＭｏが低く、このためＷ、Ｍ
ｏをあるていど添加した方がよい。Incidentally, one of the ways to increase heat resistance is to reduce the coefficient of thermal expansion, but WlMo has a low coefficient of thermal expansion as a single unit, so W, M
It is better to add o.
しかし、Ｗ、Ｍｏは比重が重く、このため余り入れると
軽量化の効果が妨げられる。このため、Ｗ＋Ｍｏ＝１〜
５重量％に設定する。なお靭性を確保するためにＣｒＯ
量として２〜１２重量％重量％型ましい（第３図）。However, W and Mo have a high specific gravity, so if too much is added, the weight reduction effect will be hindered. Therefore, W+Mo=1~
Set to 5% by weight. In addition, to ensure toughness, CrO
The amount is preferably 2 to 12% by weight (Figure 3).
さらに、粒界に偏析して粒界破壊を防止すると思われこ
のためＢを添加する実験を実施した。Ｂを添加するとさ
らに靭性を向上できることがわかった。第４図はＡｌ２
８重量％、Ｃｒ ５重量％、Ｍｏ １重量％にＢを添
加したときの結果である。Furthermore, it is believed that B segregates at grain boundaries and prevents grain boundary fracture, so an experiment was conducted in which B was added. It was found that adding B can further improve toughness. Figure 4 shows Al2
These are the results when B was added to 8% by weight, 5% by weight of Cr, and 1% by weight of Mo.
０．１重量％以下では、靭性効果が上がらず、また１、
５重量％以上では靭性効果はぼり変化しない。If it is less than 0.1% by weight, the toughness effect will not increase;
At 5% by weight or more, the toughness effect does not significantly change.
このため、Ｂは０，１〜１．５重量％が望ましい。Therefore, B is preferably 0.1 to 1.5% by weight.
実施例１
本発明材料を用いて自動車部品ディーゼルチャンバーを
試作した。Example 1 An automobile parts diesel chamber was prototyped using the material of the present invention.
この部品は、従来ステンレス鋳鋼で作られており、また
一部にセラミック（５１３Ｎ４） も使用されていた
。このディーゼルチャンバーはディーゼルエンジンの燃
焼火炎が吹き出すところであり、特に耐熱性と、耐熱疲
労性が必要とされる。また、ディーゼルエンジンは低温
での始動性も重要であり、低温での断熱性が必要となる
。This part has traditionally been made of cast stainless steel, and some ceramics (513N4) have also been used. This diesel chamber is where the combustion flame of the diesel engine blows out, and requires particularly high heat resistance and thermal fatigue resistance. Furthermore, startability at low temperatures is also important for diesel engines, which requires insulation at low temperatures.
本実施例の成分はＡｌ ；２５重量％、Ｃｒ；８重量
％、Ｗ；１重量％、Ｍｏ；１重量％、Ｂ；１重量％、残
部Ｆｅ及び不可避的不純物とした。溶解は、Ａｒ雰囲気
中で高周波溶解炉により実施し、鋳造は、精密鋳造によ
り行なった。鋳造時の注湯温度は１５３０℃であった。The components of this example were Al: 25% by weight, Cr: 8% by weight, W: 1% by weight, Mo: 1% by weight, B: 1% by weight, and the balance was Fe and unavoidable impurities. Melting was carried out in an Ar atmosphere using a high frequency melting furnace, and casting was carried out by precision casting. The pouring temperature during casting was 1530°C.
第５図に、この成分の熱伝導度を示す。第５図に示す様
に、低温では熱伝導が低く高温で高くなる特殊な形態で
あり、このことにより低温では速く温度が上昇し低温始
動性が向上し、高温では熱が逃げて、過熱が避けられる
ことになる。Figure 5 shows the thermal conductivity of this component. As shown in Figure 5, it has a special form in which heat conduction is low at low temperatures and high at high temperatures.As a result, the temperature rises quickly at low temperatures, improving low-temperature startability, and at high temperatures, heat escapes, preventing overheating. It will be avoided.
この部品は耐熱性が向上し、さらに性能も向上した。コ
ストの点でも耐熱性が高いセラミックは非常に高価であ
り、それよりも大幅に安く、また金属製の物と比べても
Ｎ１を使用していないためコストも低減できた。This part has improved heat resistance and also improved performance. In terms of cost, ceramics with high heat resistance are very expensive, but it is much cheaper than that, and compared to metal products, it does not use N1, so the cost can be reduced.
実施例２
ガソリンエンジンのエキゾウストマニホールド（エキマ
ニ）を製作した。成分はＡｌ；２８重量％、Ｃｒ；５重
量％、Ｗ；１重量％、Ｂ ； ０．５重量％、残部Ｆｅ
及び不可避的不純物である。この部品も耐熱性が要求さ
れる。また大物部品であり、軽量化の要求も高い。Example 2 An exhaust manifold (exhaust manifold) for a gasoline engine was manufactured. Ingredients are Al: 28% by weight, Cr: 5% by weight, W: 1% by weight, B: 0.5% by weight, balance Fe.
and unavoidable impurities. This part also requires heat resistance. Furthermore, since it is a large component, there is a high demand for weight reduction.
本成分の比重は、６．０であり普通の鋳鋼の７．９に比
べて軽量であり、本部品では、１２００ ｇの軽量化と
なった。The specific gravity of this component is 6.0, which is lighter than that of ordinary cast steel, which is 7.9, and the weight of this component was reduced by 1200 g.
また、耐熱性も向上して９５０℃にも耐えられるため、
燃費、馬力が向上した。In addition, it has improved heat resistance and can withstand temperatures of 950 degrees Celsius.
Fuel efficiency and horsepower improved.
耐酸化性を調べたデータを、第６図に示す。空気中１０
００℃で１００ｈのテ′−夕である。The data obtained by examining the oxidation resistance are shown in FIG. 10 in the air
The temperature was 100 hours at 00°C.
本部品の一部の金属組織写真を第７図に示す。Fig. 7 shows a photograph of the metallographic structure of a part of this part.
以上説明した様に本発明によれば下記イ）〜ホ）イ）従
来のステンレス鋼に比べてＮｉを含まないために大幅な
低コストになる。As explained above, according to the present invention, compared to the following a) to e) and b) conventional stainless steels, the cost is significantly lower because it does not contain Ni.
口）比重が５，３〜６，２程度であり２０〜３０％の軽
量化になる。Mouth) The specific gravity is about 5.3 to 6.2, resulting in a weight reduction of 20 to 30%.
ハ）熱伝導度が低温で低く、高温で高いために、暖まり
やすく、過熱されにくい特性を持つ。c) Because thermal conductivity is low at low temperatures and high at high temperatures, it has the characteristics of being easily warmed and difficult to overheat.
二）従来の金属材に比べて改良はされても脆い欠点を持
つ。しかしセラミックに比べると格段に、靭性が優れて
いる。2) Although it has been improved compared to conventional metal materials, it has the disadvantage of being brittle. However, it has much better toughness than ceramic.
ホ）耐熱性がＮ１基耐熱合金とほぼ同様である。e) Heat resistance is almost the same as that of N1 base heat resistant alloy.
の効果が得られる。The effect of this can be obtained.
第１図はＦｅ −５Ｃｒ−０，５Ｂ化合物のＡｌ量と酸
化増量の関係を示す図であり、
第２図はＦｅＡ Ｉ化合物のＣｒ ＋Ｗ＋Ｍｏの添加重
量％と衝撃値の関係を示す図であり、
第３図は熱間割れに関してＣｒ添加重量％とＷ＋Ｍｏの
添加重量％との関係を示す図であり、第４図はＦｅＡ
１化合物に関してＢ（ボロン）添加重量％と衝撃値との
関係を示す図であり、第５図は本発明に係るＦｅ−Ａｌ
化合物の熱伝導度を示す図であり、
第６図は実施例２のＦｅＡｌ化合物の耐酸化性を調べた
データであり、
第７図は実施例２のＦｅＡｌ化合物の金属組織写真であ
り、
第８図はＦｅ−Ａｌの２元状態図である。Fig. 1 is a diagram showing the relationship between the Al content and oxidation weight gain of Fe-5Cr-0,5B compound, and Fig. 2 is a diagram showing the relationship between the addition weight % of Cr + W + Mo and impact value of FeA I compound. , Figure 3 is a diagram showing the relationship between the weight % of Cr added and the weight % of W + Mo added with respect to hot cracking, and Figure 4 is a graph showing the relationship between the weight % of Cr added and the weight % of W+Mo added.
FIG. 5 is a diagram showing the relationship between B (boron) addition weight % and impact value for one compound, and FIG.
FIG. 6 is a diagram showing the thermal conductivity of the compound; FIG. 6 is data obtained by examining the oxidation resistance of the FeAl compound of Example 2; FIG. 7 is a photograph of the metallographic structure of the FeAl compound of Example 2; FIG. 8 is a binary phase diagram of Fe-Al.
Claims (1)
なくとも１種を含有し、しかもＣｒ、Ｍｏ及びＷの総和
が３〜１２重量％；残部Ｆｅ及び不可避的不純物からな
る高靭性ＦｅＡｌ金属間化合物材料。 ２、さらにＢ０．１〜１．５重量％を含有することを特
徴とする特許請求の範囲第１項記載の高靭性ＦｅＡｌ金
属間化合物材料。 ３、Ａｌ２２〜３２重量％；Ｃｒ２〜１２重量％；Ｗ、
Ｍｏのうち少なくとも１種を含有しＷとＭｏの総和が１
〜５重量％；残部Ｆｅ及び不可避的不純物からなる高靭
性ＦｅＡｌ金属間化合物材料。 ４、さらにＢ０．１〜１．５重量％を含有することを特
徴とする特許請求の範囲第３項記載の高靭性ＦｅＡｌ金
属間化合物材料。[Claims] 1. Al22 to 32% by weight; Contains at least one of Cr, W, and Mo, and the total of Cr, Mo, and W is 3 to 12% by weight; The balance is Fe and unavoidable impurities. High toughness FeAl intermetallic compound material. 2. The high toughness FeAl intermetallic compound material according to claim 1, further containing 0.1 to 1.5% by weight of B. 3, Al22-32% by weight; Cr2-12% by weight; W,
Contains at least one type of Mo, and the sum of W and Mo is 1
~5% by weight; high toughness FeAl intermetallic compound material consisting of balance Fe and unavoidable impurities. 4. The high toughness FeAl intermetallic compound material according to claim 3, further containing 0.1 to 1.5% by weight of B.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2018010A JP2555750B2 (en) | 1990-01-30 | 1990-01-30 | High toughness FeAl intermetallic compound material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2018010A JP2555750B2 (en) | 1990-01-30 | 1990-01-30 | High toughness FeAl intermetallic compound material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03226547A true JPH03226547A (en) | 1991-10-07 |
| JP2555750B2 JP2555750B2 (en) | 1996-11-20 |
Family
ID=11959708
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2018010A Expired - Fee Related JP2555750B2 (en) | 1990-01-30 | 1990-01-30 | High toughness FeAl intermetallic compound material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2555750B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0695811A1 (en) | 1994-08-05 | 1996-02-07 | Toyota Jidosha Kabushiki Kaisha | High heat-resisting iron-base alloy |
| CN1140379C (en) * | 2001-09-26 | 2004-03-03 | 上海康阜实业有限公司 | Anticorrosion refractory tubular welding wire |
| KR100742689B1 (en) * | 2005-08-03 | 2007-07-25 | 나태엽 | The heat resisting steel alloy matter Method |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012201893A (en) * | 2011-03-23 | 2012-10-22 | Yokohama National Univ | Corrosion-resistant material |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59107041A (en) * | 1982-11-29 | 1984-06-21 | ゼネラル・エレクトリツク・カンパニイ | Method of rendering strength and ductility to intermetallic compound phase |
-
1990
- 1990-01-30 JP JP2018010A patent/JP2555750B2/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59107041A (en) * | 1982-11-29 | 1984-06-21 | ゼネラル・エレクトリツク・カンパニイ | Method of rendering strength and ductility to intermetallic compound phase |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0695811A1 (en) | 1994-08-05 | 1996-02-07 | Toyota Jidosha Kabushiki Kaisha | High heat-resisting iron-base alloy |
| CN1140379C (en) * | 2001-09-26 | 2004-03-03 | 上海康阜实业有限公司 | Anticorrosion refractory tubular welding wire |
| KR100742689B1 (en) * | 2005-08-03 | 2007-07-25 | 나태엽 | The heat resisting steel alloy matter Method |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2555750B2 (en) | 1996-11-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US6482275B1 (en) | Nickel based alloys for internal combustion engine valve seat inserts, and the like | |
| JPH1112674A (en) | Aluminum alloy for internal combustion engine piston, and piston made of aluminum alloy | |
| JPS6184347A (en) | Hollow valve for internal-combustion engine | |
| JPH03226547A (en) | High toughness fe-al intermetallic compound material | |
| JPS60121254A (en) | Composite cylinder liner | |
| JPH0835027A (en) | Copper alloy excellent in high temperature wear resistance | |
| JP5400140B2 (en) | Heat resistant steel for engine valves with excellent high temperature strength | |
| JPS6339654B2 (en) | ||
| JPH0737346B2 (en) | Joined body of ceramic body and metal body and joining method thereof | |
| JP2000054053A (en) | Aluminum-base alloy excellent in heat resistance, and its production | |
| JPH06299276A (en) | Ti-al alloy parts | |
| JP3605874B2 (en) | Heat-resistant cast steel | |
| JPH09209092A (en) | Secondary combustion chamber mouthpiece for diesel engine | |
| JPS61238942A (en) | Heat resisting alloy | |
| JPH02221349A (en) | Lightweight casting material | |
| EP0440220A1 (en) | Automotive engine parts composed of heat resistant ferritic cast steel having excellent thermal fatigue resistance | |
| JP2592440B2 (en) | Ti-Al lightweight heat and oxidation resistant material | |
| JPH0588294B2 (en) | ||
| JP3840762B2 (en) | Heat resistant steel with excellent cold workability | |
| JPH0639891B2 (en) | Engine valve mechanism | |
| JPS59126750A (en) | Aluminum alloy | |
| JPH051622A (en) | Al alloy piston for internal combustion engine and its manufacture | |
| JPH01159355A (en) | Heat resistant cast steel | |
| JPS62214149A (en) | Heat resistant alloy for exhaust valve | |
| JP2686342B2 (en) | High strength heat resistant alloy for injection molding powder metallurgy for high temperature structural members |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| LAPS | Cancellation because of no payment of annual fees |