JPH02213461A - Method for surface-hardening iron-based metallic material - Google Patents
Method for surface-hardening iron-based metallic materialInfo
- Publication number
- JPH02213461A JPH02213461A JP3282789A JP3282789A JPH02213461A JP H02213461 A JPH02213461 A JP H02213461A JP 3282789 A JP3282789 A JP 3282789A JP 3282789 A JP3282789 A JP 3282789A JP H02213461 A JPH02213461 A JP H02213461A
- Authority
- JP
- Japan
- Prior art keywords
- hardness
- iron
- crfe
- metallic material
- treatment
- 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
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 23
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 12
- 239000007769 metal material Substances 0.000 title claims abstract description 12
- 238000000034 method Methods 0.000 title claims description 11
- 229910002467 CrFe Inorganic materials 0.000 claims abstract description 10
- 238000005255 carburizing Methods 0.000 claims abstract description 9
- 210000001787 dendrite Anatomy 0.000 claims abstract 2
- 239000000463 material Substances 0.000 abstract description 15
- NLXLAEXVIDQMFP-UHFFFAOYSA-N Ammonia chloride Chemical compound [NH4+].[Cl-] NLXLAEXVIDQMFP-UHFFFAOYSA-N 0.000 abstract description 8
- 150000001247 metal acetylides Chemical class 0.000 abstract description 7
- 238000005254 chromizing Methods 0.000 abstract description 6
- 229910052804 chromium Inorganic materials 0.000 abstract description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 4
- 235000019270 ammonium chloride Nutrition 0.000 abstract description 4
- 238000005336 cracking Methods 0.000 abstract description 4
- 239000010935 stainless steel Substances 0.000 abstract description 3
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 3
- 239000004215 Carbon black (E152) Substances 0.000 abstract 1
- 229910000975 Carbon steel Inorganic materials 0.000 abstract 1
- 239000010962 carbon steel Substances 0.000 abstract 1
- 229930195733 hydrocarbon Natural products 0.000 abstract 1
- 150000002430 hydrocarbons Chemical class 0.000 abstract 1
- 230000008595 infiltration Effects 0.000 abstract 1
- 238000001764 infiltration Methods 0.000 abstract 1
- 239000011812 mixed powder Substances 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 13
- 239000007789 gas Substances 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 238000007542 hardness measurement Methods 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 230000003287 optical effect Effects 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- ATUOYWHBWRKTHZ-UHFFFAOYSA-N Propane Chemical compound CCC ATUOYWHBWRKTHZ-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 239000010883 coal ash Substances 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- 101100425892 Danio rerio tpma gene Proteins 0.000 description 1
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 241000985284 Leuciscus idus Species 0.000 description 1
- 101150048952 TPM-1 gene Proteins 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000001294 propane Substances 0.000 description 1
- 239000002356 single layer Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000002023 wood Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は硬さを必要とする鉄製金属材料の表面硬化法に
関し、例えば石炭灰等により摩耗を受けるボイラチュー
ブ構造物や自動車部品等の摺動部、その他機械構造物の
製作に有利に適用しうる表面硬化フェライト系材料（例
えば鋳鉄、次素鋼、合金鉄）、オーステナイト系材料（
Ｃｒ。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a surface hardening method for ferrous metal materials that require hardness. Surface-hardened ferritic materials (e.g. cast iron, secondary steel, ferroalloys), austenitic materials (
Cr.
Ｎ１ を含むステンレス鋼）を提供することができる
方法に関する。N1-containing stainless steel).
石炭灰等によシ摩耗等を受けるボイフチューブ、構造物
や自動車部品等の摺動部には、その摩耗対策としてクロ
マイズ処理あるいは浸炭子クロマイズ処理が実施される
場合がある。クロマイズ処理は金属Ｃｒ アルミナ
、塩化アンモニウムの混合物中に被処理材を埋め込み、
水素雰囲気中で加熱する方法であり、その厚みはフェラ
イト系鋼の場合、約１００μｍ、表面Ｃｒ濃度は１０〜
４０４前後でお沙、また硬さは２００１１１ｖ前後であ
る。一方、第１段処理として浸炭、第２段処理としてク
ロマイズする方法では、厚さ３０μｍ、硬さは１０００
〜１１００１１ｖ 前後の（ＣｒｌＦｅ）ｇｏ＠ ある
いは（ＣｒｌＰａ）ｙｅｓ の単一層が得られる。Sliding parts of boif tubes, structures, automobile parts, etc., which are subject to abrasion due to coal ash, etc., are sometimes subjected to chromization treatment or carburized chromization treatment as a countermeasure against such abrasion. Chromizing treatment involves embedding the material to be treated in a mixture of metal Cr, alumina, and ammonium chloride.
This is a method of heating in a hydrogen atmosphere, and the thickness is approximately 100 μm in the case of ferritic steel, and the surface Cr concentration is 10-10 μm.
The hardness is around 404, and the hardness is around 200111v. On the other hand, in the method of carburizing as the first stage treatment and chromizing as the second stage treatment, the thickness is 30 μm and the hardness is 1000 μm.
A single layer of (CrlFe)go@ or (CrlPa)yes around ~110011v is obtained.
クロマイズ処理層の硬さは２００Ｈマ と母材のそれ（
１ａｏａマ）に比較すると大きいが、石炭灰等による損
傷抵抗を示す硬さは８００Ｈｖ前後なので、これより硬
さの低いクロマイズ層は約ａ５〜１年で消失し、十分な
効果を発揮できない等の欠点があった。The hardness of the chromized layer is 200H and that of the base material (
Although it is large compared to 1 aoa ma), the hardness that shows damage resistance from coal ash etc. is around 800 Hv, so the chromized layer with a lower hardness will disappear in about a5 to 1 year, and it may not be able to exert sufficient effect. There were drawbacks.
一方、浸炭＋クロマイズ処理では１０００〜１１００Ｈ
ｖ の硬さを有する皮膜が得られるが、その厚さが約３
０μｍと非常に薄いために耐久性の点で問題があυ、さ
らに皮膜を厚くする必要があった。また、この皮膜は単
一相であるために、割れ及び剥離等が発生しやすい傾向
にあった。On the other hand, carburizing + chromizing treatment requires 1000~1100H.
A film with a hardness of v is obtained, but its thickness is about 3
Since it is very thin at 0 μm, there is a problem with durability, and it was necessary to make the film even thicker. Furthermore, since this film is a single phase, cracking and peeling tend to occur easily.
本発明は上記技術水準に鑑み、鉄系金属材料の表面に硬
（、かつ割れ難い極厚の硬化層を形成させる方法を提供
しようとするものである。In view of the above-mentioned state of the art, the present invention seeks to provide a method for forming a hard (and hard to break) extremely thick hardened layer on the surface of an iron-based metal material.
本発明は処理温度１１００〜１２００℃でクロマイズ処
理して鉄系金属材料表面にＣｒ 濃度２０ ｗｔ１以
上で４００μｍ以上の極厚皮膜を形成させ、次に温度１
０００〜１１００℃でガス浸炭処理して該極厚皮膜中に
１０００〜１４００１１ｖ の高硬度を有する（Ｃｒｌ
Ｆ６）ｚｍｃａ あるいは（ＣｒＦｅ）７Ｃ２と比較
的低硬度を有する（ＣｒＦｅ）３０とをプントフィト状
に交互に成長させることを特徴とする鉄系金属材料の表
面硬化法である。In the present invention, an extremely thick film of 400 μm or more is formed on the surface of an iron-based metal material at a Cr concentration of 20 wt1 or more by chromizing treatment at a treatment temperature of 1100 to 1200 °C, and then at a temperature of 1
The extremely thick film has a high hardness of 1000 to 140011v by gas carburizing at 000 to 1100°C.
F6) Zmca This is a surface hardening method for iron-based metal materials characterized by growing (CrFe)7C2 and (CrFe)30 having relatively low hardness alternately in a puntophyte shape.
本発明で処理対象となる鉄系金属材料は、例えば次素鋼
、鋳鉄、Ｃｒ及びＭＯあるいはＮｉ 。The ferrous metal materials to be treated in the present invention include, for example, secondary steel, cast iron, Cr, MO, or Ni.
Ｃｒ、Ｍｏ、Ｖ等を含む合金鋼のようなフェライト系材
料及び例えばＣｒ、Ｎ３−を含むステンＶス鋼のような
オーステナイＦ系材料があげられる。Examples include ferritic materials such as alloy steel containing Cr, Mo, V, etc. and austenite F-based materials such as stainless V steel containing Cr, N3-.
本発明のクロマイズ処理においては、一般のクロマイズ
処理と同じ種類の処理剤（金属Ｃｒ粉、アルミナ粉及び
塩化アンモニウム）、同シ雰囲気（Ｈｌ ガスのよう
な還元ガス雰囲気）及び同じ処理時間（１０〜２０時間
）が採用され、これらの条件の変更によってクロマイズ
処理層の膜厚をある程度変えることができるが、これら
の条件のみによっては極厚のクロマイズ処理層膜は得ら
れない。本発明のクロマイズ処理の最大の特徴は処理温
度を１１００〜１２００℃に設定したことであって、こ
れによって４００μｍ以上の極厚のクロマイズ層が得ら
れる。In the chromizing treatment of the present invention, the same types of treatment agents (metallic Cr powder, alumina powder, and ammonium chloride), the same atmosphere (reducing gas atmosphere such as Hl gas), and the same treatment time (10 to 20 hours), and the thickness of the chromized layer can be changed to some extent by changing these conditions, but a very thick chromized layer cannot be obtained by changing these conditions alone. The most important feature of the chromized treatment of the present invention is that the treatment temperature is set at 1100 to 1200 DEG C., thereby making it possible to obtain an extremely thick chromized layer of 400 .mu.m or more.
１１００℃未満では得られるクロマイズ層の厚厚さが１
００〜２００μｍ と薄く、かっ核層のＣｒ 濃度が
２０ ｗｔ１未満となる場合があシ、この濃度未満では
（ｃｒｙｅ）＊ｓＣｓ及び（Ｃｒ！Ｐａ）ｙｃｓ等の硬
い炭化物が得がたい。また１２００１：を越えるとクロ
マイズ処理に使用するステンレス製ボックスが熱により
酸化あるいは変形し処理不能となるからである。At less than 1100°C, the thickness of the chromized layer obtained is 1
00 to 200 μm, and the Cr concentration of the parenteral layer may be less than 20 wt1. Below this concentration, hard carbides such as (crye)*sCs and (Cr!Pa)ycs are difficult to obtain. Moreover, if it exceeds 12001:, the stainless steel box used for the chromization process will be oxidized or deformed by heat, making the process impossible.
本発明のガス浸炭処理において、処理温度が１０００℃
以下ではＣｒ 量が多く浸炭せず（ＣｒＦｅ）７Ｃ２
等は厚（形成されないが、１０００〜１１００℃に上昇
させ、かつ処理時間を５時間以上にすることによシ厚い
（２５０μｍ程度）の（Ｃｒｌ’ｅ）９０３等が得られ
るので、ガス浸炭処理温度は１０００〜１１００ｔｌ：
に設定すべきである。またガス浸度以外の浸炭法（固体
浸炭）では炭化物は形成されないので、ガス浸炭にしな
ければならない。In the gas carburizing treatment of the present invention, the treatment temperature is 1000°C
Below, the amount of Cr is large and carburization does not occur (CrFe) 7C2
Although thick (Crl'e) 903 etc. are not formed, it is possible to obtain thick (about 250 μm) (Crl'e) 903 etc. by raising the temperature to 1000 to 1100 °C and making the treatment time more than 5 hours. Temperature is 1000-1100tl:
Should be set to . Furthermore, since carbides are not formed by carburizing methods other than gas immersion (solid carburizing), gas carburizing must be used.
数巨μｍの厚さで、高硬度の炭化物を形成させたために
、従来よシ著しく耐久性が向上するとともに、高硬度及
び低硬度の炭化物が共存するために、従来よシ割れ発生
が少なく、また耐剥離性も著しく向上した。By forming a highly hard carbide with a thickness of several micrometers, the durability is significantly improved compared to conventional products, and since high hardness and low hardness carbides coexist, there is less cracking compared to conventional products. Peeling resistance was also significantly improved.
第１図に示すようにαｏ７４ｃ１２．２゛５４０ｒ、
１４Ｍｏ％α７４Ｎｂ％（Ｌ６１Ｔｉ、ＥａｊＦｅの
組成を有するボイフチューブ（５（Ｌ８φ×＆０ｔＸ５
００ｊ）１を金属Ｃｒ、 アルミナ、塩化アンモニウ
ムの混合物２中に埋め込み水素雰囲気中で１２００℃で
１０時間加熱しクロマイズ処理を実施した。As shown in Figure 1, αo74c12.2゛540r,
Boif tube (5 (L8φ×&0tX5
00j) 1 was embedded in a mixture 2 of metal Cr, alumina, and ammonium chloride and heated at 1200° C. for 10 hours in a hydrogen atmosphere to carry out chromization treatment.
第２図はこの処理により得られた皮膜層３の断面の光学
顕微鏡組織を示す写真、第３図は、ＭＰＭム（Ｘ線マイ
クロアナライザ）による？ｅ及びＣｒの濃度分布を示す
図表、第４図はビッカース硬さ測定結果を示す図表であ
る。これらのデータかられかるように皮膜３の性状は、
皮膜厚さが５３０μｍ％Ｃｒ濃度が１０〜５０％。Fig. 2 is a photograph showing an optical microscopic structure of a cross section of the film layer 3 obtained by this treatment, and Fig. 3 is a photograph taken using an MPM (X-ray microanalyzer). FIG. 4 is a chart showing the concentration distribution of e and Cr, and FIG. 4 is a chart showing the Vickers hardness measurement results. As can be seen from these data, the properties of film 3 are as follows:
The film thickness is 530 μm% and the Cr concentration is 10 to 50%.
また硬さは１７０〜２３０ Ｈｖ前後であった。Moreover, the hardness was around 170 to 230 Hv.
次に、これを１１００℃で５時間の処理条件でプロパン
ガス雰囲気中で浸炭処理を実施した。Next, this was carburized in a propane gas atmosphere at 1100° C. for 5 hours.
第５図はこの処理により得られた皮膜層の断面の光学顕
微鏡組織を示す写真、第６図は］！ｔＰＭＡによるＩＰ
ｅ、Ｃｒ及び０の濃度分布を示す図表、第７図はビッカ
ース硬さ測定結果を示す図表である。なお、第８図に皮
膜層４を拡大してみた光学顕微鏡組織を示した。Figure 5 is a photograph showing the optical microscopic structure of a cross section of the film layer obtained by this treatment, and Figure 6 is]! IP by tPMA
FIG. 7 is a chart showing the concentration distribution of e, Cr and 0, and FIG. 7 is a chart showing the Vickers hardness measurement results. Incidentally, FIG. 8 shows an enlarged optical microscopic structure of the film layer 4.
第５図及び第８図において、約２５０μｍの厚さを有す
る皮膜層４において、白色にみえるものは、ｌＰＭムに
よる元素分析の結果、Ｃを５．４〜ａ３４、ＩＦｅ を
２９．７４、Ｃｒ を５９５幅含有した炭化物で、また
黒色にみえるものは、Ｃを＆３４、ＩＦｅを７ａ３４、
Ｃｒを１２．９４含有した炭化物で・あることがわかっ
た。これらは、この組成比よシ白色炭化物が（’ｒｌ’
８）！３０１１、（ａｒｙｅ）、ａ、及び黒色炭化物が
（ＣｒＦｅ）３０ と推定されたが、第９図に示すよう
にＸｍ回折結果によっても、これらの炭化物が形成され
ていることが明らかである。In FIG. 5 and FIG. 8, what appears to be white in the film layer 4 having a thickness of about 250 μm is composed of 5.4 to a34 C, 29.74 IFe, and Cr. The carbide containing 595 widths of C, and those that appear black, are C &34, IFe 7a34,
It was found to be a carbide containing 12.94% Cr. These have a whiter carbide than this composition ratio ('rl'
8)! 3011, (arye), a, and black carbides were estimated to be (CrFe)30, but as shown in FIG. 9, it is clear from the Xm diffraction results that these carbides were formed.
また、これらの炭化物はチューブ１の管内面方向に向っ
てプントフィト状に交互に成長してお夛その硬さは、（
ＣｒＦｅ）ＴＯｓが１０００〜１１８０Ｈｖ 一方（
ＣｒｌＦｅ）３０は、その生成領域が小さいために確認
することはできなかったが、この炭化物の化学組成と第
１０図に示す基本図（硬さと、０、Ｆθ及びＣｒの組成
データ）から推定すると７００〜８００Ｈマ前後と考え
られる。In addition, these carbides grow alternately in a puntophyte shape toward the inner surface of the tube 1, and their hardness is (
CrFe)TOs is 1000~1180Hv while (
CrlFe)30 could not be confirmed due to its small production area, but it is estimated from the chemical composition of this carbide and the basic diagram shown in Figure 10 (hardness, 0, Fθ, and Cr composition data). It is thought to be around 700 to 800 hours.
なお、第６図及び第７図において皮膜４のデータは、（
ＣｒｌＦｅ）γＣ３を代表してプロットしている。In addition, the data of the film 4 in FIGS. 6 and 7 are (
CrlFe)γC3 is plotted as a representative.
また皮膜層５については、フェライト及び（ｏｒＦｅ）
３０が形成されているが、これについては、特に高硬度
を示していないのでその詳細は省略する。Regarding the film layer 5, ferrite and (orFe)
30, but since this does not exhibit particularly high hardness, its details will be omitted.
クロマイズ温度１１００〜１２００℃で鉄系金属材料の
表面に４００μｍ以上の極厚皮膜を形成させこの際のＣ
ｒ濃度を高（（２０ｗｔ４以上）保持し、次に１０００
〜１１００℃で、ガス浸炭処理を行ったことにより皮膜
中に１１００〜１１８０Ｈｖ の高硬度を有する（Ｃｒ
Ｆｅ）１３０ｇ、（（！ｒＩＦｅ）、Ｏ，及び比較的低
硬度を有する（ｏｒｐｅ）、ｃをプントフィト状に交互
に成長させた。これにより耐割れ性が著しく改善されま
た耐摩耗性も大巾に向上した鉄系金属材料を得ることが
できる。C
Keep r concentration high ((20wt4 or higher), then 1000
The film has a high hardness of 1100 to 1180 Hv (Cr
Fe) 130g, ((!rIFe), O, and (orpe), which has relatively low hardness, were grown alternately in a puntophyte shape.This significantly improved the cracking resistance and greatly increased the wear resistance. It is possible to obtain iron-based metal materials with improved properties.
第１図は本発明のクロマイズ処理状況を示す概略図、第
２図はクロマイズ処理材の金属組織を示す断面光学顕微
鏡組織写真、第３図はクロマイズ処理材のＩ！ｉＰＭＡ
によるＩＦｅ及びＣｒの濃度分布を示す図表、第４図は
、クロマイズ処理材の硬さ測定結果を示す図表、第５図
は、クロマイズ＋浸炭処理材の金属組織を示す断面光学
顕微鏡組織写真、第６図はクロマイズ＋浸炭処理材の断
面の１１ｆｉ’ＭＡによる０ｒＦｅ及び０の濃度分布を
示す図表、第７図はクロマイズ＋浸炭処理材の硬さ測定
結果を示す図表、第８図は、クロマイズ＋浸炭処理材の
金属組織を示す薪面の拡大顕微鏡組織写真、第９図は、
クロマイズ＋浸炭処理材の表面からのＸ線回折結果を示
す図表、第１０図は、炭化物の化学組成と硬さとの関係
を示す図表である。FIG. 1 is a schematic diagram showing the chromization process of the present invention, FIG. 2 is a cross-sectional optical microscope photograph showing the metal structure of the chromized material, and FIG. 3 is the I! of the chromized material. iPMA
Figure 4 is a diagram showing the hardness measurement results of chromized material, Figure 5 is a cross-sectional optical microscopic microstructure photograph showing the metal structure of chromized + carburized material, and Figure 4 is a diagram showing the concentration distribution of IFe and Cr. Figure 6 is a chart showing the concentration distribution of 0rFe and 0 by 11fi'MA on the cross section of the chromized + carburized material, Figure 7 is a chart showing the hardness measurement results of the chromized + carburized material, and Figure 8 is the chart showing the hardness measurement results of the chromized + carburized material. Figure 9 is an enlarged micrograph of the firewood surface showing the metal structure of carburized wood.
FIG. 10 is a chart showing the results of X-ray diffraction from the surface of the chromized + carburized material, and is a chart showing the relationship between the chemical composition of carbide and hardness.
Claims (1)
系金属材料表面にＣｒ濃度２０ｗｔ％以上で４００μｍ
以上の極厚皮膜を形成させ、次に温度１０００〜１１０
０℃でガス浸炭処理して該極厚皮膜中に１０００〜１４
００Ｈｖの高硬度を有する（ＣｒＦｅ）＿２＿３Ｃ＿６
あるいは（ＣｒＦｅ）＿７Ｃ＿２と比較的低硬度を有す
る（ＣｒＦｅ）＿３Ｃとをデンドライト状に交互に成長
させることを特徴とする鉄系金属材料の表面硬化法。Chromize treatment at a treatment temperature of 1100 to 1200°C to form a 400 μm thick layer on the surface of iron-based metal materials with a Cr concentration of 20 wt% or more.
Form an extremely thick film as described above, then at a temperature of 1000 to 110
Gas carburizing treatment at 0°C gives 1000 to 14
(CrFe)_2_3C_6 with high hardness of 00Hv
Alternatively, a surface hardening method for iron-based metal materials characterized by growing (CrFe)_7C_2 and (CrFe)_3C having relatively low hardness alternately in a dendrite shape.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1032827A JP2607668B2 (en) | 1989-02-14 | 1989-02-14 | Surface hardening method for iron-based metallic materials |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1032827A JP2607668B2 (en) | 1989-02-14 | 1989-02-14 | Surface hardening method for iron-based metallic materials |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02213461A true JPH02213461A (en) | 1990-08-24 |
| JP2607668B2 JP2607668B2 (en) | 1997-05-07 |
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ID=12369660
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1032827A Expired - Lifetime JP2607668B2 (en) | 1989-02-14 | 1989-02-14 | Surface hardening method for iron-based metallic materials |
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| Country | Link |
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| JP (1) | JP2607668B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007063667A (en) * | 2005-08-02 | 2007-03-15 | Honda Motor Co Ltd | LAYERED Fe-BASED ALLOY AND PROCESS FOR PRODUCTION THEREOF |
| JP2007063665A (en) * | 2005-08-02 | 2007-03-15 | Honda Motor Co Ltd | LAYERED Fe-BASED ALLOY AND PROCESS FOR PRODUCTION THEREOF |
| JP2007063666A (en) * | 2005-08-02 | 2007-03-15 | Honda Motor Co Ltd | LAYERED Fe-BASED ALLOY AND PROCESS FOR PRODUCTION THEREOF |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63192854A (en) * | 1987-02-04 | 1988-08-10 | Mitsubishi Heavy Ind Ltd | Surface hardening method for metal |
-
1989
- 1989-02-14 JP JP1032827A patent/JP2607668B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63192854A (en) * | 1987-02-04 | 1988-08-10 | Mitsubishi Heavy Ind Ltd | Surface hardening method for metal |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007063667A (en) * | 2005-08-02 | 2007-03-15 | Honda Motor Co Ltd | LAYERED Fe-BASED ALLOY AND PROCESS FOR PRODUCTION THEREOF |
| JP2007063665A (en) * | 2005-08-02 | 2007-03-15 | Honda Motor Co Ltd | LAYERED Fe-BASED ALLOY AND PROCESS FOR PRODUCTION THEREOF |
| JP2007063666A (en) * | 2005-08-02 | 2007-03-15 | Honda Motor Co Ltd | LAYERED Fe-BASED ALLOY AND PROCESS FOR PRODUCTION THEREOF |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2607668B2 (en) | 1997-05-07 |
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