JP3341675B2 - Iron-based sintered alloy excellent in strength and toughness and method for producing the same - Google Patents
Iron-based sintered alloy excellent in strength and toughness and method for producing the sameInfo
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- JP3341675B2 JP3341675B2 JP12674698A JP12674698A JP3341675B2 JP 3341675 B2 JP3341675 B2 JP 3341675B2 JP 12674698 A JP12674698 A JP 12674698A JP 12674698 A JP12674698 A JP 12674698A JP 3341675 B2 JP3341675 B2 JP 3341675B2
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- iron
- average particle
- weight
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Description
【０００１】[0001]
【発明の属する技術分野】この発明は、エンジン部品を
始めとする自動車部品およびコンプレッサー部品などの
各種機械部品の材料として使用される強度および靱性に
優れたた鉄基焼結合金およびその製造方法に関するもの
である。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an iron-based sintered alloy having excellent strength and toughness used as a material for various mechanical parts such as engine parts, automobile parts and compressor parts, and a method for producing the same. Things.
【０００２】[0002]
【従来の技術】一般に、エンジン部品を始めとする自動
車部品およびコンプレッサー部品などの各種機械部品の
材料として鉄基焼結合金が用いられており、この鉄基焼
結合金の１つとして、Ｃ：０．１重量％以下、Ｍｎ：
０．０８重量％以下、Ｃｒ：０．５〜３重量％、Ｍｏ：
０．１〜２重量％、Ｓ：０．０１重量％以下、Ｐ：０．
０１重量％以下、Ｏ：０．２重量％以下を含有し、残り
がＦｅおよび不可避不純物からなる組成を有する合金鋼
粉末にＣ：０．２〜１．２％を含有させた鉄基焼結合金
があることは知られている。2. Description of the Related Art Generally, iron-based sintered alloys are used as materials for various mechanical parts such as engine parts, automobile parts, compressor parts, and the like. One of the iron-based sintered alloys is C: 0.1% by weight or less, Mn:
0.08% by weight or less, Cr: 0.5 to 3% by weight, Mo:
0.1-2% by weight, S: 0.01% by weight or less, P: 0.
Iron-based sintering bonding in which alloy steel powder having a composition of not more than 01% by weight and O: 0.2% by weight and the balance being Fe and unavoidable impurities contains C: 0.2 to 1.2% It is known that there is money.
【０００３】[0003]
【発明が解決しようとする課題】しかし、近年、エンジ
ン部品を始めとする自動車部品およびコンプレッサー部
品などの各種機械部品の材料として一層優れた強度およ
び靱性を有する鉄基焼結合金が求められている。However, in recent years, iron-based sintered alloys having higher strength and toughness have been demanded as materials for various mechanical parts such as engine parts, automobile parts and compressor parts. .
【０００４】[0004]
【課題を解決するための手段】そこで、本発明者らは、
上述のような観点から、一層優れた強度および靭性を有
する鉄基焼結合金を得るべく研究を行った結果、原料粉
末として、平均粒径の大きいＦｅ粉末にＮｉ粉末および
Ｃｒ3 Ｃ2 粉末を混合し、さらに必要に応じてＣ粉末を
添加して混合し、成形し、焼結すると、マルテンサイ
ト、オーステナイトおよびパーライトの混合組織からな
る素地中にＦｅからなるフェライト相が島状に分散して
いる組織を有する鉄基焼結合金が得られ、この鉄基焼結
合金は従来よりも強度および靭性が一層向上する、とい
う知見を得たのである。Means for Solving the Problems Accordingly, the present inventors have:
From the above viewpoints, as a result of conducting research to obtain an iron-based sintered alloy having more excellent strength and toughness, Ni powder and Cr 3 C 2 powder were used as raw material powders in Fe powder having a large average particle size. After mixing, and further adding C powder as needed, mixing, molding and sintering, the ferrite phase composed of Fe is dispersed in the form of islands in a matrix composed of a mixed structure of martensite, austenite and pearlite. It has been found that an iron-based sintered alloy having a certain structure can be obtained, and that the strength and toughness of the iron-based sintered alloy are further improved as compared with the prior art.
【０００５】この発明は、かかる知見にもとづいて成さ
れたものであって、 （１）Ｃｒ：０．２〜５重量％、Ｎｉ：１〜６重量％、
Ｃ：０．１〜１．０重量％を含有し、残りがＦｅおよび
不可避不純物からなる組成を有し、かつマルテンサイ
ト、オーステナイトおよびパーライトの混合組織からな
る素地中にＦｅからなるフェライト相が島状に分散して
いる組織を有する強度および靭性に優れた鉄基焼結合
金、 （２）平均粒径：３０〜９０μｍのＦｅ粉末、平均粒
径：１〜８μｍのＮｉ粉末および平均粒径：０．５〜１
５μｍのＣｒ3 Ｃ2 粉末を混合し、成形し、焼結する前
記（１）記載の強度および靭性に優れた鉄基焼結合金の
製造方法、 （３）平均粒径：３０〜９０μｍのＦｅ粉末、平均粒
径：１〜８μｍのＮｉ粉末、平均粒径：０．５〜１５μ
ｍのＣｒ3 Ｃ2 粉末および平均粒径：１〜２５μｍのＣ
粉末を混合し、成形し、焼結する前記（１）記載の強度
および靭性に優れた鉄基焼結合金の製造方法、に特徴を
有するものである。[0005] The present invention has been made based on such findings, (1) Cr: 0.2 to 5% by weight, Ni: 1 to 6% by weight,
C: 0.1 to 1.0% by weight, the remainder having a composition of Fe and unavoidable impurities, and a ferrite phase of Fe in a matrix composed of a mixed structure of martensite, austenite, and pearlite. (2) Fe powder having an average particle diameter of 30 to 90 μm, Ni powder having an average particle diameter of 1 to 8 μm, and an average particle diameter of: 0.5-1
A method for producing an iron-based sintered alloy having excellent strength and toughness according to the above (1), wherein 5 μm of Cr 3 C 2 powder is mixed, molded and sintered, and (3) an average particle size of Fe of 30 to 90 μm. Powder, average particle size: Ni powder of 1 to 8 μm, average particle size: 0.5 to 15 μm
m 3 Cr 2 powder and average particle size: 1 to 25 μm C
The method is characterized by the method for producing an iron-based sintered alloy having excellent strength and toughness according to the above (1), wherein the powder is mixed, molded and sintered.
【０００６】平均粒径の大きなＦｅ粉末にＮｉ粉末およ
びＣｒ3 Ｃ2 粉末を混合し、成形し、焼結すると、マル
テンサイト、オーステナイトおよびパーライトの混合組
織からなる素地中にＦｅからなるフェライト相が島状に
分散している組織を有する強度および靭性に優れた鉄基
焼結合金が得られるメカニズムは、下記の理由によるも
のと考えられる。[0006] When Ni powder and Cr 3 C 2 powder are mixed with Fe powder having a large average particle size, molded and sintered, a ferrite phase composed of Fe is contained in a matrix composed of a mixed structure of martensite, austenite and pearlite. The mechanism by which an iron-based sintered alloy having an island-dispersed structure and excellent strength and toughness is obtained is considered to be due to the following reasons.
【０００７】すなわち、Ｆｅ粉末、Ｎｉ粉末およびＣｒ
3 Ｃ2 粉末を混合し、成形し、焼結すると、焼結中に大
部分のＮｉ、ＣｒおよびＣはＦｅ粉末に拡散してＦｅを
主成分とするＦｅ−Ｃｒ−Ｎｉ−Ｃ合金相となり、この
Ｆｅ−Ｃｒ−Ｎｉ−Ｃ合金相はマルテンサイト、オース
テナイトおよびパーライトの混合組織となって合金の素
地を形成する。しかし、Ｆｅ粉末の平均粒径が大きい
と、Ｆｅ粉末、Ｎｉ粉末およびＣｒ3 Ｃ2 粉末からなる
混合粉末を焼結しても、大きな平均粒径を有するＦｅ粉
末の中央部までＮｉ、ＣｒおよびＣが十分に拡散せず、
Ｆｅ粉末の中央部はＦｅ粉末本来の組織であるＦｅから
なるフェライト相がそのまま残り、大きな粒径のＦｅ粉
末の周囲はＦｅ−Ｃｒ−Ｎｉ−Ｃ合金相となってマルテ
ンサイト、オーステナイトおよびパーライトに変態し素
地を形成する。That is, Fe powder, Ni powder and Cr
When 3 C 2 powder is mixed, molded and sintered, most of the Ni, Cr and C diffuse into the Fe powder during sintering to form an Fe-Cr-Ni-C alloy phase containing Fe as a main component. The Fe-Cr-Ni-C alloy phase has a mixed structure of martensite, austenite and pearlite to form a base material of the alloy. However, when the average particle diameter of the Fe powder is large, even if the mixed powder composed of the Fe powder, the Ni powder and the Cr 3 C 2 powder is sintered, the Ni, Cr and C does not diffuse enough,
At the center of the Fe powder, the ferrite phase composed of Fe, which is the original structure of the Fe powder, remains as it is, and the periphery of the Fe powder having a large grain size becomes an Fe-Cr-Ni-C alloy phase to form martensite, austenite, and pearlite. Transforms and forms a base.
【０００８】このようにして得られたマルテンサイト、
オーステナイトおよびパーライトの混合組織からなる素
地中にＦｅからなるフェライト相が島状に分散している
組織を有する鉄基焼結合金は、高強度のマルテンサイ
ト、オーステナイトおよびパーライトの混合組織からな
る素地を有する鉄基焼結合金に破壊が発生しても柔らか
いフェライト相で破壊の進行が阻害され、靭性が向上す
るものと考えられる。The martensite thus obtained,
An iron-based sintered alloy having a structure in which a ferrite phase composed of Fe is dispersed in the form of islands in a body composed of a mixed structure of austenite and pearlite has a high strength martensite, a substrate composed of a mixed structure of austenite and pearlite. It is considered that even if fracture occurs in the iron-based sintered alloy, the progress of the fracture is hindered by the soft ferrite phase, and the toughness is improved.
【０００９】したがって、この発明の強度および靱性に
優れた鉄基焼結合金の製造には、平均粒径の大きなＦｅ
粉末を用いることが必要であり、さらに還元が難しいＣ
ｒをＣｒ3 Ｃ2 中のＣにより容易に還元し、Ｆｅ中へ拡
散しやすくするためにＣｒ3Ｃ2 粉末を用いることが必
要である。この場合、Ｃ含有量を調整するためにＣｒ 3
Ｃ2 粉末と共にＣ粉末を添加しても良い。Therefore, the strength and toughness of the present invention
For the production of excellent iron-based sintered alloys, Fe
It is necessary to use powder and it is difficult to reduce C
r for CrThreeCTwoEasily reduced by C in the steel and expanded into Fe
Cr for easy dispersalThreeCTwoIt is necessary to use powder
It is important. In this case, to adjust the C content, Three
CTwoC powder may be added together with the powder.
【００１０】前述のごとく、この発明の強度および靱性
に優れた鉄基焼結合金の製造には、平均粒径の大きなＦ
ｅ粉末を用いることが必要であり、そのＦｅ粉末の平均
粒径は３０〜９０μｍの範囲内にあることが好ましく、
このＦｅ粉末に対して添加するＮｉ粉末、Ｃｒ3 Ｃ2 粉
末およびＣ粉末の平均粒径はそれぞれＮｉ粉末：１〜８
μｍ、Ｃｒ3 Ｃ2 粉末：０．５〜１５μｍおよびＣ粉
末：１〜２５μｍの範囲内にあることが好ましい。As described above, in order to produce the iron-based sintered alloy having excellent strength and toughness according to the present invention, F
It is necessary to use e powder, and the average particle diameter of the Fe powder is preferably in the range of 30 to 90 μm,
The average particle diameters of the Ni powder, Cr 3 C 2 powder and C powder added to the Fe powder are Ni powder: 1 to 8 respectively.
μm, Cr 3 C 2 powder: 0.5 to 15 μm and C powder: preferably 1 to 25 μm.
【００１１】この発明の強度および靱性に優れた鉄基焼
結合金の製造方法を一層具体的に述べると、原料粉末と
して、Ｆｅ粉末、Ｎｉ粉末、Ｃｒ3 Ｃ2 粉末および黒鉛
粉末を用意し、これら原料粉末を金型成形時の潤滑剤で
あるステアリン酸亜鉛粉末またはエチレンビスステアラ
ミドとともにダブルコーンミキサーで混合し、プレス成
形して圧粉体を作製し、圧粉体を水素を含む窒素雰囲気
中、温度：１０００〜１２００℃で焼結する。焼結温度
は１１１０〜１１５０℃が一層好ましい。温度：１１０
０〜１１５０℃で焼結すると、平均粒径：３０〜９０μ
ｍを有するＦｅ粉末の内でも粒径の大きい６０μｍ以上
のＦｅ粉末の中央部までＮｉ、ＣｒおよびＣが十分に拡
散せず、靱性に富むＦｅ粉末本来のフェライト相を維持
できる。The method for producing an iron-based sintered alloy having excellent strength and toughness according to the present invention will be described in more detail. Fe powder, Ni powder, Cr 3 C 2 powder and graphite powder are prepared as raw material powders. These raw material powders are mixed with zinc stearate powder or ethylene bisstearamide, which is a lubricant at the time of molding, in a double cone mixer, and press-molded to produce a green compact. Medium, sintering at a temperature of 1000-1200 ° C. The sintering temperature is more preferably 1110 to 1150 ° C. Temperature: 110
When sintered at 0 to 1150 ° C., the average particle size is 30 to 90 μm.
Even among the Fe powders having m, Ni, Cr and C are not sufficiently diffused to the central portion of the Fe powder having a large particle diameter of 60 μm or more, and the original ferrite phase of the tough Fe powder can be maintained.
【００１２】つぎに、この発明の強度および靱性に優れ
た鉄基焼結合金の成分組成を上記のごとく限定した理由
について説明する。 （ａ）Ｃｒ Ｃｒは、靱性を低下させることなく強度を向上させる効
果があるが、その含有量が０．２重量％未満ではその効
果が十分でなく、一方、５重量％を越えてもそれ以上の
効果が望めない。したがって、Ｃｒの含有量は０．２〜
５重量％に定めた。Ｃｒの含有量の一層好ましい範囲は
２〜４重量％である。Next, the reason why the component composition of the iron-based sintered alloy having excellent strength and toughness of the present invention is limited as described above will be described. (A) Cr Cr has the effect of improving the strength without lowering the toughness. However, if its content is less than 0.2% by weight, its effect is not sufficient. The above effects cannot be expected. Therefore, the content of Cr is 0.2 to
It was determined to be 5% by weight. A more preferable range of the Cr content is 2 to 4% by weight.
【００１３】（ｂ）Ｎｉ Ｎｉは、Ｆｅ合金相の強度および靱性を向上させる作用
があるが、その含有量が１重量％未満ではその効果が十
分でなく、一方６重量％を越えて含有してもそれ以上の
効果が少ない。したがって、Ｎｉの含有量は１〜６重量
％に定めた。Ｎｉの含有量の一層好ましい範囲は３〜５
重量％である。(B) Ni Ni has the effect of improving the strength and toughness of the Fe alloy phase, but if its content is less than 1% by weight, its effect is not sufficient, while its content exceeds 6% by weight. Even so, there is little effect. Therefore, the content of Ni is set to 1 to 6% by weight. A more preferred range for the Ni content is 3-5.
% By weight.
【００１４】（ｃ）Ｃ Ｃは、強度を向上させまた硬さを向上させる作用がある
が、その含有量が０．１重量％未満では強度向上効果が
十分でなく、一方、１．０重量％を越えて含有する靱性
を低下させるので好ましくない。したがって、Ｃの含有
量は０．１〜１．０重量％に定めた。Ｃの含有量の一層
好ましい範囲は０．３〜０．８重量％である。(C) C C has the effect of improving the strength and the hardness, but if its content is less than 0.1% by weight, the effect of improving the strength is not sufficient. % Is not preferred because the toughness contained in excess of% is reduced. Therefore, the content of C is set to 0.1 to 1.0% by weight. A more preferable range of the content of C is 0.3 to 0.8% by weight.
【００１５】[0015]
【発明の実施の形態】実施例１ 原料粉末として、平均粒径：５５μｍのＦｅ粉末、平均
粒径：５μｍのＮｉ粉末、平均粒径：１０μｍのＣｒ3
Ｃ2 粉末および平均粒径：１７μｍのＣ粉末を用意し、
これら原料粉末を表１〜表２に示される配合組成となる
ように配合し、さらに金型成形時の潤滑剤であるステア
リン酸亜鉛粉末またはエチレンビスステアラミド粉末を
外掛けで０．８重量％に当たる量だけ添加し、ダブルコ
ーンミキサーで混合し、プレス成形して３０ｍｍ×１２
ｍｍ×６ｍｍの寸法を有する抗折試験片形状および５５
ｍｍ×１０ｍｍ×１０ｍｍの寸法を有するシャルピー衝
撃試験片形状の圧粉体を作製した。なお、ステアリン酸
亜鉛粉末を潤滑剤として用いる場合は常温で、エチレン
ビスステアラミド粉末を潤滑剤として用いる場合は、混
合する粉末および金型の温度を１３５℃としてプレス成
形した。得られた圧粉体をＮ2 −５％Ｈ2 の混合雰囲気
中、温度：１１５０℃、２０分保持の条件で焼結したの
ち、０．５℃／ｓｅｃの冷却速度で冷却し、表１〜表２
に示される成分組成の本発明焼結合金１〜７および比較
焼結合金１〜６からなる抗折試験片およびシャルピー衝
撃試験片を作製した。DESCRIPTION OF THE PREFERRED EMBODIMENTS Example 1 As a raw material powder, an Fe powder having an average particle size of 55 μm, a Ni powder having an average particle size of 5 μm, and a Cr 3 having an average particle size of 10 μm were used.
C 2 powder and C powder having an average particle size of 17 μm were prepared,
These raw material powders are blended so as to have a blending composition shown in Tables 1 and 2, and zinc stearate powder or ethylenebisstearamide powder which is a lubricant at the time of molding is 0.8% by weight. , And mixed with a double cone mixer, press-molded to 30 mm x 12
Form of bending test specimen having dimensions of mm × 6 mm and 55 mm
A compact having a shape of a Charpy impact test specimen having a size of mm × 10 mm × 10 mm was prepared. In addition, when zinc stearate powder was used as a lubricant, press molding was performed at room temperature, and when ethylene bisstearamide powder was used as a lubricant, the temperature of the mixed powder and the mold was set at 135 ° C. to perform press molding. The obtained compact was sintered in a mixed atmosphere of N 2 -5% H 2 at a temperature of 1150 ° C. for 20 minutes and then cooled at a cooling rate of 0.5 ° C./sec. ~ Table 2
The bending test pieces and the Charpy impact test pieces were prepared from the sintered alloys 1 to 7 of the present invention and the comparative sintered alloys 1 to 6 having the component compositions shown in FIG.
【００１６】さらに比較のために、Ｃ：０．８重量％、
Ｍｎ：０．０４重量％、Ｃｒ：１．０３重量％、Ｍｏ：
０．９２重量％、Ｓ：０．００５重量％、Ｐ：０．００
４重量％、Ｏ：０．０８重量％を含有し、残りがＦｅお
よび不可避不純物からなる従来焼結合金を用意した。こ
の従来焼結合金からなる抗折試験片およびシャルピー衝
撃試験片を作製した。For further comparison, C: 0.8% by weight,
Mn: 0.04% by weight, Cr: 1.03% by weight, Mo:
0.92% by weight, S: 0.005% by weight, P: 0.00
A conventional sintered alloy containing 4% by weight and 0.08% by weight of O and the balance of Fe and inevitable impurities was prepared. A bending test piece and a Charpy impact test piece made of this conventional sintered alloy were produced.
【００１７】さらにこれら本発明焼結合金１〜７、比較
焼結合金１〜６および従来焼結合金の密度を測定してそ
の値を表３に示した後、ＩＳＯ３３２５に基づき、支点
間距離２５ｍｍで抗折試験を行うことにより抗折力を測
定し、またＪＩＳ Ｚ２２４２ＮＩ準じてノッチなしの
シャルピー衝撃試験片を用いてシャルピー衝撃を測定
し、その結果を表３に示した。Further, the densities of these sintered alloys 1 to 7 of the present invention, comparative sintered alloys 1 to 6 and conventional sintered alloys were measured and the values are shown in Table 3. Based on ISO3325, the distance between fulcrums was 25 mm. The bending force was measured by performing a bending test in Table 1. The Charpy impact was measured using a notched Charpy impact test piece according to JIS Z2242NI. The results are shown in Table 3.
【００１８】この発明の強度および靭性に優れた鉄基焼
結合金の組織を一層理解しやすくするために、表１に示
される本発明焼結合金３を切断し、研磨し、金属顕微鏡
による組織写真を取り、その組織写真を図１に示した。
図２は本発明焼結合金３の金属組織の写生図である。図
１および図２において黒く見える部分は空孔３であり、
１は素地、２はＦｅからなるフェライト相（以下、フェ
ライト相という）である。図１の組織写真および図２金
属組織の写生図から明らかなように、本発明焼結合金３
の素地はマルテンサイト、オーステナイトおよびパーラ
イトの混合組織からなり、素地１の中にフェライト相２
が島状に分散していることが分かる。In order to make it easier to understand the structure of the iron-based sintered alloy having excellent strength and toughness of the present invention, the sintered alloy 3 of the present invention shown in Table 1 is cut, polished, and examined by a metallographic microscope. A photograph was taken and a photograph of the structure is shown in FIG.
FIG. 2 is a sketch of the metal structure of the sintered alloy 3 of the present invention. In FIG. 1 and FIG.
Reference numeral 1 denotes a base, and 2 denotes a ferrite phase made of Fe (hereinafter, referred to as a ferrite phase). As is clear from the structure photograph of FIG. 1 and the sketch of the metal structure of FIG.
The base material has a mixed structure of martensite, austenite and pearlite.
Are dispersed in an island shape.
【００１９】さらに、前記本発明焼結合金３の組織の素
地１およびフェライト相２の部分の成分含有量をＥＰＭ
Ａにより測定した結果、素地１はＮｉ、ＣｒおよびＣは
Ｆｅ粉末に拡散してＦｅを主成分とするＦｅ−Ｃｒ−Ｎ
ｉ−Ｃ合金相となり、このＦｅ−Ｃｒ−Ｎｉ−Ｃ合金相
はマルテンサイト、オーステナイトおよびパーライトの
混合組織となっているが、この素地の中に島状に分散し
ているフェライト相２にはＮｉ、ＣｒおよびＣがほとん
ど含まれないことを確認した。Further, the component contents of the base material 1 and the ferrite phase 2 of the structure of the sintered alloy 3 of the present invention were determined by EPM.
As a result of measurement by A, the base material 1 was Ni, Cr and C were diffused into Fe powder, and Fe—Cr—N containing Fe as a main component.
The Fe-Cr-Ni-C alloy phase has a mixed structure of martensite, austenite, and pearlite, and the ferrite phase 2 dispersed in the form of islands in the matrix has an i-C alloy phase. It was confirmed that Ni, Cr and C were hardly contained.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】[0022]
【表３】 [Table 3]
【００２３】表１〜表３に示される結果から、本発明焼
結合金１〜７と従来焼結合金を比較すると、本発明焼結
合金１〜７は従来焼結合金と比べて、抗折力および衝撃
値が優れていることが分かる。しかし、この発明の範囲
から外れている成分組成を有する比較焼結合金１〜６
は、抗折力および衝撃値のうちの少なくともいずれかが
劣ることが分かる。From the results shown in Tables 1 to 3, when the sintered alloys 1 to 7 of the present invention are compared with the conventional sintered alloys, the sintered alloys 1 to 7 of the present invention are more deflected than the conventional sintered alloy. It can be seen that the force and impact values are excellent. However, comparative sintered alloys 1 to 6 having a component composition outside the scope of the present invention.
Indicates that at least one of the bending force and the impact value is inferior.
【００２４】[0024]
【発明の効果】上述のように、この発明の鉄基焼結合金
は、抗折力および衝撃値が高い値を示し、さらに強度お
よび靱性に優れ、自動車部品およびコンプレッサー部品
などの各種機械部品の材料として適しており、機械産業
の発展に大いに貢献し得るものである。As described above, the iron-based sintered alloy of the present invention exhibits high values of the transverse rupture strength and the impact value, and also has excellent strength and toughness, and is suitable for various mechanical parts such as automobile parts and compressor parts. It is suitable as a material and can greatly contribute to the development of the machinery industry.
【図１】この発明の強度および靱性に優れた鉄基焼結合
金の金属顕微鏡による組織写真である。FIG. 1 is a micrograph of a structure of an iron-based sintered alloy having excellent strength and toughness according to the present invention, taken by a metallurgical microscope.
【図２】この発明の強度および靱性に優れた鉄基焼結合
金の組織の写生図である。FIG. 2 is a sketch drawing of the structure of an iron-based sintered alloy having excellent strength and toughness according to the present invention.
１ 素地 ２ フェライト相 ３ 空孔 1 Base 2 Ferrite phase 3 Void
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭52−78704（ＪＰ，Ａ) 特開 昭62−63646（ＪＰ，Ａ) 特開 昭61−67759（ＪＰ，Ａ) 特開 平９−195012（ＪＰ，Ａ) 特開 平９−195014（ＪＰ，Ａ) 特開 昭61−183448（ＪＰ，Ａ) 特開 昭51−145410（ＪＰ，Ａ) 特開 平３−219040（ＪＰ，Ａ) 特開 平10−25533（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 304 C22C 33/02 C22C 38/40 ──────────────────────────────────────────────────続 き Continuation of front page (56) References JP-A-52-78704 (JP, A) JP-A-62-63646 (JP, A) JP-A-61-67759 (JP, A) 195012 (JP, A) JP-A-9-195014 (JP, A) JP-A-61-183448 (JP, A) JP-A-51-145410 (JP, A) JP-A-3-219040 (JP, A) JP-A-10-25533 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C22C 38/00 304 C22C 33/02 C22C 38/40
Claims (3)
重量％、Ｃ：０．１〜１．０重量％を含有し、残りがＦ
ｅおよび不可避不純物からなる組成を有し、かつマルテ
ンサイト、オーステナイトおよびパーライトの混合組織
からなる素地中にＦｅからなるフェライト相が島状に分
散している組織を有することを特徴とする強度および靭
性に優れた鉄基焼結合金。1. Cr: 0.2 to 5% by weight, Ni: 1 to 6
% By weight, C: 0.1 to 1.0% by weight, the balance being F
having a composition consisting of e and unavoidable impurities, and Marte
Structure of austenite, austenite and pearlite
An iron-based sintered alloy having excellent strength and toughness, characterized by having a structure in which a ferrite phase composed of Fe is dispersed in an island shape in a base composed of .
平均粒径：１〜８μｍのＮｉ粉末および平均粒径：０．
５〜１５μｍのＣｒ 3 Ｃ 2 粉末を混合し、成形し、焼結
することを特徴とする請求項１記載の強度および靭性に
優れた鉄基焼結合金の製造方法。2. Fe powder having an average particle size of 30 to 90 μm.
Average particle size: Ni powder of 1 to 8 μm and average particle size:
Mixing the Cr 3 C 2 powder 5 to 15 [mu] m, molded, strength, and a manufacturing method excellent iron-based sintered alloy toughness according to claim 1, wherein the sintering.
平均粒径：１〜８μｍのＮｉ粉末、平均粒径：０．５〜
１５μｍのＣｒ 3 Ｃ 2 粉末および平均粒径：１〜２５μ
ｍのＣ粉末を混合し、成形し、焼結することを特徴とす
る請求項１記載の強度および靭性に優れた鉄基焼結合金
の製造方法。 3. An Fe powder having an average particle size of 30 to 90 μm;
Average particle size: 1-8 μm Ni powder, average particle size: 0.5-
15 μm Cr 3 C 2 powder and average particle size: 1 to 25 μ
The method for producing an iron-based sintered alloy having excellent strength and toughness according to claim 1, wherein m powders of C are mixed, molded and sintered.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12674698A JP3341675B2 (en) | 1998-04-21 | 1998-04-21 | Iron-based sintered alloy excellent in strength and toughness and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12674698A JP3341675B2 (en) | 1998-04-21 | 1998-04-21 | Iron-based sintered alloy excellent in strength and toughness and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11302806A JPH11302806A (en) | 1999-11-02 |
| JP3341675B2 true JP3341675B2 (en) | 2002-11-05 |
Family
ID=14942893
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP12674698A Expired - Lifetime JP3341675B2 (en) | 1998-04-21 | 1998-04-21 | Iron-based sintered alloy excellent in strength and toughness and method for producing the same |
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| Country | Link |
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|---|---|---|---|---|
| JP3970060B2 (en) * | 2002-03-12 | 2007-09-05 | 株式会社リケン | Ferrous sintered alloy for valve seat |
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1998
- 1998-04-21 JP JP12674698A patent/JP3341675B2/en not_active Expired - Lifetime
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| Publication number | Publication date |
|---|---|
| JPH11302806A (en) | 1999-11-02 |
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