JPH0390543A - Manufacture of sintered alloy steel and alloy steel powder - Google Patents
Manufacture of sintered alloy steel and alloy steel powderInfo
- Publication number
- JPH0390543A JPH0390543A JP1227239A JP22723989A JPH0390543A JP H0390543 A JPH0390543 A JP H0390543A JP 1227239 A JP1227239 A JP 1227239A JP 22723989 A JP22723989 A JP 22723989A JP H0390543 A JPH0390543 A JP H0390543A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy steel
- alloy
- tin
- weight
- 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
Links
- 239000000843 powder Substances 0.000 title claims abstract description 33
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 24
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- 238000005121 nitriding Methods 0.000 claims abstract description 12
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 11
- 239000000956 alloy Substances 0.000 claims abstract description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 9
- 239000011159 matrix material Substances 0.000 claims abstract description 7
- 239000007789 gas Substances 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229930195733 hydrocarbon Natural products 0.000 claims abstract description 4
- 150000002430 hydrocarbons Chemical class 0.000 claims abstract description 4
- 239000004215 Carbon black (E152) Substances 0.000 claims abstract description 3
- 239000002245 particle Substances 0.000 claims description 21
- 229910001315 Tool steel Inorganic materials 0.000 claims description 16
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 claims description 6
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 4
- UGFAIRIUMAVXCW-UHFFFAOYSA-N Carbon monoxide Chemical compound [O+]#[C-] UGFAIRIUMAVXCW-UHFFFAOYSA-N 0.000 claims description 3
- 229910021529 ammonia Inorganic materials 0.000 claims description 3
- 229910002092 carbon dioxide Inorganic materials 0.000 claims description 3
- 239000001569 carbon dioxide Substances 0.000 claims description 3
- 229910002091 carbon monoxide Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 abstract description 16
- 238000005255 carburizing Methods 0.000 abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 5
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 150000001247 metal acetylides Chemical class 0.000 abstract description 4
- 238000000034 method Methods 0.000 abstract description 4
- 238000004663 powder metallurgy Methods 0.000 abstract description 4
- 229910052721 tungsten Inorganic materials 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 229910001873 dinitrogen Inorganic materials 0.000 abstract description 3
- 238000005245 sintering Methods 0.000 abstract description 3
- 229910052751 metal Inorganic materials 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract description 2
- 229910052719 titanium Inorganic materials 0.000 abstract 2
- 229910000997 High-speed steel Inorganic materials 0.000 abstract 1
- 238000005520 cutting process Methods 0.000 description 10
- 150000004767 nitrides Chemical class 0.000 description 6
- 238000012360 testing method Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 239000011882 ultra-fine particle Substances 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は切削工具等を製造するに用いる焼結合金鋼及び
その原料粉末である合金鋼粉末の製造法に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a method for producing a sintered alloy steel used for producing cutting tools and the like, and an alloy steel powder that is a raw material powder thereof.
高速度工具鋼は切削工具製造用材料として溶製法や粉末
冶金法により製造されている。この合金鋼は耐摩耗性を
向上するため、主としてＷ、 Ｃｒ。High-speed tool steel is manufactured as a material for manufacturing cutting tools by melting and powder metallurgy. This alloy steel mainly contains W and Cr to improve wear resistance.
Ｖ、Ｍｏ、Ｃｏ及びＣを合金成分としてＦｅに配合した
ものである。そして従来は合金成分の配合量を増すこと
により耐摩耗性の向上が計られていた。V, Mo, Co, and C are blended with Fe as alloy components. Conventionally, wear resistance has been improved by increasing the amount of alloying components.
しかし、これらの合金成分を増すと、焼きなまし硬さが
大きくなる代わりに、鍛造、切削などの加工が困難にな
り、強度が低下し、高速度工具鋼の最大の特徴である靭
性に悪影響を及ぼす。However, when these alloy components are increased, at the cost of increasing annealing hardness, processing such as forging and cutting becomes difficult, the strength decreases, and the toughness, which is the most important characteristic of high-speed tool steel, is adversely affected. .
一方、超硬合金に劣る耐摩耗性を向上するために、高速
度工具鋼粉末に炭化物や窒化物を混合して焼結すること
も提案されている。On the other hand, in order to improve the wear resistance, which is inferior to that of cemented carbide, it has also been proposed to mix carbides or nitrides into high-speed tool steel powder and sinter it.
高速度工具鋼粉末に炭化物や窒化物の粉末を混合して焼
結する場合、通常粉末冶金に用いられている粉末の粒径
である数μｍ程度の粒径の炭化物や窒化物の粉末を用い
ると、焼結体中の高速度工具鋼の粒界に炭化物、窒化物
が網状に集合してしまい焼結体の靭性が著しく低いもの
となる。炭化物、窒化物の粉末にサブミクロンの超微粒
子を用いることも考えられるが、このような超微粒子は
凝集しやすく均一に分散させることが困難で、希望の組
織を得ることができない現状にある。When mixing carbide or nitride powder with high-speed tool steel powder and sintering it, use carbide or nitride powder with a particle size of several μm, which is the particle size of powder normally used in powder metallurgy. Then, carbides and nitrides aggregate in a network at the grain boundaries of the high-speed tool steel in the sintered body, resulting in extremely low toughness of the sintered body. Although it is possible to use submicron ultrafine particles for carbide and nitride powders, such ultrafine particles tend to aggregate and are difficult to disperse uniformly, making it impossible to obtain the desired structure.
本発明は高速度工具鋼の最大の特徴である靭性を有する
と同時に、耐摩耗性に優れた焼結合金鋼及びその原料と
して用いる合金鋼粉末の製造法を提供することを課題と
する。An object of the present invention is to provide a sintered alloy steel that has toughness, which is the most important feature of high-speed tool steel, and has excellent wear resistance, and a method for producing alloy steel powder used as a raw material for the same.
本発明は、重量％でＴｉ１０〜３０％、（！ｒ ２．５
〜４．０％ 、Ｍｏ ３．０〜１５％、Ｎ５．０〜１５
％、Ｃ０，８〜３．０％、Ｎ２．５〜８．５％、Ｏｏｌ
、５〜１２％、残部Ｆｅ及び不可避不純物からなる組成
を有し、高速度工具鋼のマトリックス中に粒径が０．３
μｍ以下のＴｉＮからなる硬質相の粒子を１０〜６０体
積％分散含有する焼結合金鋼、重量％でＴｉ１Ｏ〜３０
％、Ｃｒ２．５〜４．０％、Ｍｏ３．０〜１５％、Ｎ５
．０〜１５％、Ｃｏ １．５〜１２％、残部Ｆｅからな
る組成の合金を調製して粒径１００μｍ以下の粉末とし
、この粉末を窒素あるいはアンモニア雰囲気中で３００
〜１１００Ｃに加熱して窒化処理し、更に炭化水素ガス
、又は一酸化炭素、二酸化炭素を含む雰囲気中で２００
〜１０００ Ｃ”に加熱して浸炭処理する合金鋼粉末の
製造法にある。The present invention has Ti 10-30% by weight%, (!r 2.5
~4.0%, Mo 3.0~15%, N5.0~15
%, C0.8-3.0%, N2.5-8.5%, Ool
, 5 to 12%, the balance being Fe and unavoidable impurities, and the grain size is 0.3% in the matrix of high speed tool steel.
Sintered alloy steel containing 10 to 60 volume % of dispersed hard phase particles consisting of TiN of μm or less, Ti1O to 30 in weight %
%, Cr2.5-4.0%, Mo3.0-15%, N5
．． An alloy with a composition of 0 to 15% Co, 1.5 to 12% Co, and the balance Fe is prepared into a powder with a particle size of 100 μm or less, and this powder is heated to 300 μm in a nitrogen or ammonia atmosphere.
Nitriding treatment is performed by heating to ~1100C, and further 200C in an atmosphere containing hydrocarbon gas, carbon monoxide, and carbon dioxide.
A method for producing alloy steel powder that is heated to ~1000 C'' and carburized.
本発明合金鋼は、一般にＴｉ、Ｏｒ、 ＭＯ％ ＷＳＯ
ｏｚＦｅを秤量配合して真空溶解し、溶湯を窒素ガスで
アトマイズし、得られた粉末を篩でふるって、１００μ
ｍ以下の粒径に整え、窒素あるいはアンモニア雰囲気中
で３００〜１１００σに加熱して窒化処理し、続いて炭
化水素又は一酸化炭素、二酸化炭素を含む雰囲気で２０
０〜１００ＱＣ’に加熱して浸炭処理し、更に粉砕して
粒径ｌ〜５０μｍの合金鋼粉末とし、これを焼結して得
るものである。The alloy steel of the present invention generally contains Ti, Or, MO% WSO
ozFe was weighed and blended and melted in vacuum, the molten metal was atomized with nitrogen gas, and the resulting powder was sieved to a size of 100 μm.
The particles are adjusted to a particle size of less than 200 m, heated to 300 to 1100σ in a nitrogen or ammonia atmosphere, and nitrided, and then heated in an atmosphere containing hydrocarbons, carbon monoxide, and carbon dioxide for 200 sigma.
It is obtained by carburizing by heating to 0 to 100 QC', then pulverizing to obtain alloy steel powder with a particle size of 1 to 50 μm, and sintering this.
本発明合金鋼において、Ｔｉ１０〜３０％、Ｎ２．５〜
８．５％は、合金中にＴｉＮからなる硬質相の粒子を１
０〜６０体積％を生成せしめるに必要な成分であり、こ
の硬質相が１０体積％未満では耐摩耗性が充分でなく、
６０体積％を超えると靭性が低下するＯ
この硬質相の粒子の粒径を０．３μｍ以下とすることで
、ＴｉＨの網状集合を生成させずに高速度工具鋼のマト
リックス中にＴｉＮを均一に分散でき、靭性を低下させ
ずに耐摩耗性を向上出来る。In the alloy steel of the present invention, Ti10~30%, N2.5~
8.5% means that 1 hard phase particle consisting of TiN is added to the alloy.
It is a necessary component to generate 0 to 60% by volume, and if this hard phase is less than 10% by volume, the wear resistance is insufficient.
If the content exceeds 60% by volume, the toughness decreases. By setting the particle size of this hard phase to 0.3 μm or less, TiN can be uniformly distributed in the matrix of high-speed tool steel without forming a network of TiH. It can be dispersed and improve wear resistance without reducing toughness.
Ｏｒ ２．５〜４．０％、Ｍｏ３．０〜１５％、Ｎ５．
０〜１５％、（！０．８〜３．０％、Ｃ０１，５〜１２
％、残部Ｆｅは、高速度工具鋼のマトリックスを形成す
る成分であり、ＩＦｅ以外の成分の添加量は、粒径が０
．３μｍ以下のＴｉＮからなる硬質相の粒子を１０〜６
０体積％以外は、通常の高速度工具鋼の成分添加量であ
って、これら添加量が下限より少ないと耐摩耗性が不充
分となり、逆に上限より多いと耐摩耗性は大きくなるが
靭性が小さくなるのでこの範囲とする。Or 2.5-4.0%, Mo3.0-15%, N5.
0-15%, (!0.8-3.0%, C01,5-12
%, the remainder Fe is a component that forms the matrix of high-speed tool steel, and the amount of components other than IFe is determined when the grain size is 0.
．． 10 to 6 hard phase particles made of TiN with a diameter of 3 μm or less
Values other than 0% by volume are the additive amounts of ordinary high-speed tool steels, and if these amounts are less than the lower limit, the wear resistance will be insufficient, and if they are greater than the upper limit, the wear resistance will increase, but the toughness will decrease. is set in this range because it is small.
本発明の合金鋼粉末の製造法においては、Ｎ及びＣを除
く成分を合金粉末化し、窒化処理することにより、高速
度工具鋼のマトリックス中にＴｉＮの硬質粒子を均一に
分散した状態を生成することが可能となる。この窒化処
理に当たって粒径１００μｍ以下の粉末とするのは、粒
径が１００μｍを超えると窒化処理により粒径０．３μ
ｍ以下のＴｉＮを生成せしめることが困難となるばかり
でなく、その粒内の中心部まで窒化することが困難にな
るからである。In the method for producing alloy steel powder of the present invention, components other than N and C are turned into alloy powder and subjected to nitriding treatment, thereby creating a state in which hard particles of TiN are uniformly dispersed in the matrix of high-speed tool steel. becomes possible. In this nitriding treatment, the powder with a particle size of 100 μm or less is made; if the particle size exceeds 100 μm, the particle size is 0.3 μm by nitriding treatment.
This is because not only is it difficult to generate TiN with a particle diameter of less than m, but also it is difficult to nitride the center of the grain.
窒化処理を３００〜１１００ Ｃ’の温度範囲で行なう
のは、３００ Ｃ”未満の温度では合金成分中のＴｉが
ＴｉＮに変化する反応が遅くなり、１１００ Ｃ’を超
えると生成したＴｉＮが粒成長を起こすからである。The reason why the nitriding treatment is carried out in the temperature range of 300 to 1100 C' is because at temperatures below 300 C', the reaction in which Ti in the alloy components changes to TiN slows down, and at temperatures above 1100 C', the produced TiN slows down to grain growth. This is because it causes
窒化処理の後に浸炭処理を行なうのは、窒化処理の前に
浸炭処理を行なうと、合金中のＴｉがＴｉＣに変化して
しまうからであり、窒化処理の後に浸炭処理することは
、ＴｉＮの生成した後の合金マトリックスを高速度工具
鋼に変換するために必要である。この浸炭処理を２００
〜１０００σの温度範囲で行なうのは、２００Ｃ°未満
では高速度工具鋼に変換できず、１０００Ｃ°を超える
温度では生成したＴｉＮと高速度工具鋼中の炭化物が粒
成長するからである。Carburizing is performed after nitriding because if carburizing is performed before nitriding, Ti in the alloy will change to TiC, and carburizing after nitriding prevents the formation of TiN. This is necessary to convert the alloy matrix into high-speed tool steel. This carburizing treatment
The reason why this is carried out in the temperature range of ~1000σ is that if the temperature is less than 200°C, it cannot be converted into high-speed tool steel, and if the temperature exceeds 1000°C, the produced TiN and carbides in the high-speed tool steel will undergo grain growth.
実施例Ｉ
Ｔｉ １５重量％、Ｏｒ ４重量％、Ｍｏ５．５重Ｍ％
、Ｗ６．５重量％、Ｏｏ８．０重量％、残部Ｆｅからな
る組成の合金を真空中で溶解して窒化ガスでアトマイズ
し、得られた粉末を篩でふるって、粒径１００μｍ以下
の粉末を得た。この粉末を窒素ガス雰囲気中で６００Ｃ
”に１時間保持して窒化処理し、次いでメタン、水素の
混合ガス中で５００Ｃ’に１．５時間保持して浸炭処理
を施し、ボールミルで粉砕して粒径５〜４０μｍの合金
鋼粉末を得た。Example I Ti 15% by weight, Or 4% by weight, Mo 5.5% by weight M
, 6.5% by weight of W, 8.0% by weight of Oo, and the balance of Fe is melted in vacuum and atomized with nitriding gas, and the resulting powder is sieved to obtain powder with a particle size of 100 μm or less. Ta. This powder was heated at 600C in a nitrogen gas atmosphere.
The steel was then held at 500 C' for 1.5 hours in a mixed gas of methane and hydrogen for carburization, and ground in a ball mill to produce alloy steel powder with a particle size of 5 to 40 μm. Obtained.
この粉末の組成はＴｉ １４，２重量％、Ｏｒ３．８重
量％、Ｍｏ５，２重量％、Ｗ６．２重ｉ％、Ｏｏ７．６
重量％、ａＯ，Ｓ重量％、Ｎ４．３重量％、残部Ｆｅ及
び不可避不純物であった。又この粉末中には最大粒径が
０．３μｍで平均粒径０，１μｍのＴｉＮが均一に分散
して析出しており、ＴｉＮの全体に占める体積は２５％
であった。The composition of this powder is Ti: 14.2% by weight, Or: 3.8% by weight, Mo: 5.2% by weight, W: 6.2% by weight, Oo: 7.6% by weight.
Weight%, aO, S weight%, N4.3% by weight, balance Fe and unavoidable impurities. In addition, TiN with a maximum particle size of 0.3 μm and an average particle size of 0.1 μm is uniformly dispersed and precipitated in this powder, and the volume of TiN accounts for 25% of the total volume.
Met.
この合金鋼粉末を軟鋼中に真空封止し、１１５０Ｃ°に
加熱後、熱間押出を行なった。得られた合金から丸棒を
切り出し、熱処理後最終加工を経て、試験用の外径１０
耶のエンドミルを作成した。This alloy steel powder was vacuum sealed in mild steel, heated to 1150°C, and then hot extruded. A round bar is cut out from the obtained alloy, heat treated and final processed to a diameter of 10 mm for testing.
Created an end mill.
このエンドミルを下記条件で切削試験に供した。This end mill was subjected to a cutting test under the following conditions.
被削材 ＳＣＭ ４４０ （Ｈａ ３２）切削
速度 ８０ ｍ／ｍｉｎ
送 リ ０．２１ｎｆ／ｒｅｖ・刃切
り込み Ａｄ＝１５門、Ｒｄ＝１間切削長さ
２０ ｍ
切削試験の結果は逃げ面摩耗幅０．０９−で正常摩耗で
あった。Work material SCM 440 (Ha 32) Cutting speed 80 m/min Feed rate 0.21nf/rev・Blade depth of cut Ad=15 gates, Rd=1 Cutting length
The results of the 20 m cutting test showed normal wear with a flank wear width of 0.09-.
比較例
上記発明品と同組成になるようにＴｉＮ粉末と高速度工
具鋼粉末を混合し、通常の粉末冶金法により焼結体を得
た。この焼結体から実施例と同様の処Ｗによりエンドミ
ルを試作し、同じ切削試験を行なった結果は、逃げ面摩
耗幅０．２３＋ｎｓであり、刃先にはチッピングが多発
していた。Comparative Example TiN powder and high-speed tool steel powder were mixed to have the same composition as the above-mentioned invention product, and a sintered body was obtained by a normal powder metallurgy method. An end mill was prototyped from this sintered body using the same process W as in the example, and the same cutting test was conducted.The results were that the flank wear width was 0.23+ns, and the cutting edge was frequently chipped.
本発明合金鋼によれば、従来の高速度工具鋼と同様の靭
性を有するうえに従来よりも耐摩耗性に優れた切削用材
料を提供でき、本発明製造法により本発明の合金鋼の製
造を可能とする。According to the alloy steel of the present invention, it is possible to provide a cutting material that has the same toughness as conventional high-speed tool steel and has superior wear resistance than conventional ones, and the alloy steel of the present invention can be manufactured by the manufacturing method of the present invention. is possible.
出 願 人 住友電気工業株式会社 手 続 補 正 １よ （自発） １゜ 事件の表示 平成 年 特 許 願 第２２７２３９ 号 ２発明の名称 焼結合金鋼及び合金鋼粉末の製造法 ３、 補正をする者 事件との関係Out wish Man Sumitomo Electric Industries, Ltd. hand Continued Supplementary Positive 1. (spontaneous) 1゜ Display of incidents Heisei Year Special permission wish No. 227239 issue 2. Name of the invention Manufacturing method of sintered alloy steel and alloy steel powder 3. Person making the amendment Relationship with the incident
Claims (2)
％、Ｍｏ３．０〜１５％、Ｗ５．０〜１５％、Ｃ０．８
〜３．０％、Ｎ２．５〜８．５％、Ｃｏ１．５〜１２％
、残部Ｆｅ及び不可避不純物からなる組成を有し、高速
度工具鋼のマトリツクス中に粒径が０．３μｍ以下のＴ
ｉＮからなる硬質相の粒子を１０〜６０体積％分散含有
する焼結合金鋼。(1) Ti10-30%, Cr2.5-4.0 in weight%
%, Mo3.0-15%, W5.0-15%, C0.8
~3.0%, N2.5~8.5%, Co1.5~12%
, the balance is Fe and unavoidable impurities, and T with a grain size of 0.3 μm or less is present in the matrix of high-speed tool steel.
A sintered alloy steel containing 10 to 60 volume % of hard phase particles made of iN dispersed therein.
％、Ｍｏ３．０〜１５％、Ｗ５．０〜１５％、Ｃｏ１．
５〜１２％、残部Ｆｅからなる組成の合金を調製して粒
径１００μｍ以下の粉末とし、この粉末を窒素あるいは
アンモニア雰囲気中で３００〜１１００℃に加熱して窒
化処理し、更に炭化水素ガス、又は一酸化炭素、二酸化
炭素を含む雰囲気中で２００〜１０００℃に加熱して浸
炭処理する合金鋼粉末の製造法。(2) Ti10-30%, Cr2.5-4.0 in weight%
%, Mo3.0-15%, W5.0-15%, Co1.
An alloy having a composition of 5 to 12% Fe with the balance being Fe is prepared to form a powder with a particle size of 100 μm or less, and this powder is heated to 300 to 1100°C in a nitrogen or ammonia atmosphere to undergo a nitriding treatment, and then a hydrocarbon gas, Or a method for producing alloy steel powder, which is heated to 200 to 1000°C and carburized in an atmosphere containing carbon monoxide and carbon dioxide.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1227239A JPH0390543A (en) | 1989-09-01 | 1989-09-01 | Manufacture of sintered alloy steel and alloy steel powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1227239A JPH0390543A (en) | 1989-09-01 | 1989-09-01 | Manufacture of sintered alloy steel and alloy steel powder |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0390543A true JPH0390543A (en) | 1991-04-16 |
Family
ID=16857698
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1227239A Pending JPH0390543A (en) | 1989-09-01 | 1989-09-01 | Manufacture of sintered alloy steel and alloy steel powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0390543A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005123306A1 (en) * | 2004-06-18 | 2005-12-29 | Metso Powdermet Oy | Method for manufacturing composite materials, and a composite material manufactured with the method |
| CN103658638A (en) * | 2013-12-12 | 2014-03-26 | 河南省大地合金股份有限公司 | Manufacturing method of bar material of hard alloy end mill for machining stainless steel |
| CN103736990A (en) * | 2014-01-15 | 2014-04-23 | 涂秀琼 | Pre-alloyed powder material and preparation method thereof |
-
1989
- 1989-09-01 JP JP1227239A patent/JPH0390543A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005123306A1 (en) * | 2004-06-18 | 2005-12-29 | Metso Powdermet Oy | Method for manufacturing composite materials, and a composite material manufactured with the method |
| CN103658638A (en) * | 2013-12-12 | 2014-03-26 | 河南省大地合金股份有限公司 | Manufacturing method of bar material of hard alloy end mill for machining stainless steel |
| CN103736990A (en) * | 2014-01-15 | 2014-04-23 | 涂秀琼 | Pre-alloyed powder material and preparation method thereof |
| CN103736990B (en) * | 2014-01-15 | 2016-01-20 | 涂秀琼 | A kind of prealloy powder powder material and preparation method thereof |
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