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WO1997014523A1 - Poudre de fer pour metallurgie des poudres, procede de production correspondant et melange de poudre a base de fer pour metallurgie des poudres - Google Patents

Poudre de fer pour metallurgie des poudres, procede de production correspondant et melange de poudre a base de fer pour metallurgie des poudres Download PDF

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Publication number
WO1997014523A1
WO1997014523A1 PCT/JP1996/003007 JP9603007W WO9714523A1 WO 1997014523 A1 WO1997014523 A1 WO 1997014523A1 JP 9603007 W JP9603007 W JP 9603007W WO 9714523 A1 WO9714523 A1 WO 9714523A1
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WIPO (PCT)
Prior art keywords
powder
weight
iron
iron powder
less
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.)
Ceased
Application number
PCT/JP1996/003007
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English (en)
Japanese (ja)
Inventor
Satoshi Uenosono
Kuniaki Ogura
Ji-Bin Yang
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.)
JFE Steel Corp
Mitsubishi Materials Corp
Original Assignee
Mitsubishi Materials Corp
Kawasaki Steel Corp
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Application filed by Mitsubishi Materials Corp, Kawasaki Steel Corp filed Critical Mitsubishi Materials Corp
Priority to JP51569097A priority Critical patent/JP3353836B2/ja
Priority to EP96935351A priority patent/EP0808681A4/fr
Publication of WO1997014523A1 publication Critical patent/WO1997014523A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%

Definitions

  • the present invention relates to an iron powder for powder metallurgy, a method for producing the powder, and an iron-based mixed powder for powder metallurgy, and more particularly to a powder that exhibits excellent machinability and abrasion resistance when formed into a sintered body. .
  • powder metallurgy is a technique in which a metal powder is pressurized in a mold to form a molded body, and the molded body is sintered to produce a mechanical part or the like.
  • a metal powder is pressurized in a mold to form a molded body, and the molded body is sintered to produce a mechanical part or the like.
  • iron powder for metal powder
  • Sintered body having a density of about 2 g / cm 3 To By using such powder metallurgy, machine parts with fairly complex shapes can be manufactured with high dimensional accuracy. However, when manufacturing mechanical parts with strict dimensional accuracy, the sintered body may be subjected to further machining such as cutting or drilling.
  • powder metallurgy products that is, sintered bodies
  • sintered bodies generally have poor machinability, so they are more suitable for cutting than in the case of cutting ingots (for example, materials obtained by rolling flakes manufactured by continuous sintering).
  • the life of the tool used is shortened. For this reason, there is a problem that the cost during the machining is increased.
  • the cause of the low machinability of the sintered body is due to the pores contained in the sintered body. This is because the pores cause intermittent cutting, or the thermal conductivity of the sintered body decreases, and the temperature of the cutting portion increases.
  • S and MnS have conventionally been often mixed with iron powder. These S and MnS facilitated chip breaking Alternatively, a thin film of S or MnS is formed on the rake face of the tool, and the thin film exerts a lubricating action during cutting.
  • Japanese Patent Publication No. 3-25481 discloses that molten steel containing pure iron containing 0.1 to 0.5% by weight of Mn and Si, C, etc., and further adding 0.03 to 0.07% by weight of S. It has proposed iron powder for powder metallurgy manufactured by atomizing with water or gas. However, the machinability of the sintered body manufactured using this iron powder has been improved only slightly less than twice that of the sintered body manufactured using the conventional iron powder, and further improvement has been demanded. .
  • Japanese Patent Application Laid-Open No. 61-253301 discloses that C: 0.10% by weight or less, n: 2.0% by weight or less, oxygen: 0.30% by weight or less, and Cr: 0.10% by weight. — 5.0% by weight, Ni: 0.10-5.0% by weight, Si: 2.0% by weight or less, Cu: 0.10-1.0% by weight, Mo: 0.01 -3.0% by weight, W: 0.01 -3.0% by weight, V: 0.001 to 2. ⁇ % by weight, Ti: 0.005 to 0.50% by weight, Zr: 0 005-0.
  • this alloy powder is made by water atomizing iron powder obtained by roughly reducing iron oxide such as iron ore and mill scale with fine powder coke and molten steel separately pre-alloyed with many metal elements.
  • the obtained mother alloy powder is mixed, and after that, the mixed powder is finish-reduced for production. Therefore, this alloy steel powder was not only manufactured by a very complicated method, but also contained a large amount of many alloying elements, so that it was expensive.
  • the master alloy powder obtained by the above-mentioned water atomization was as follows: C: 0.50% by weight or less, Mn: 5.0% by weight or less, oxygen content: 1.5% by weight or less, and Cr: 0.10% or less. ⁇ 20.0% by weight, Ni: 0.15 ⁇ 20.0 weight %, Si: 5.0% by weight or less, Cu: 0.15 to 20.0% by weight, Mo:
  • Nb 0.01 to 2.0% by weight
  • P 0.04 to 2.0% by weight
  • B 0.0010 to 2.0% by weight.
  • the maximum amount of residual graphite is about 0.42% by weight, and the composition of iron powder with B: more than 0.03% by weight and Mn: more than 0.1% by weight shows improvement in machinability. I could't.
  • the present invention provides an iron powder for powder metallurgy capable of producing a sintered body exhibiting more excellent machinability and wear resistance, a method for producing the same, and other powders added to the iron powder. It is intended to provide a mixed powder added.
  • the present inventors have studied on further improving the machinability and wear resistance of a sintered body with reference to the descriptions in JP-A-7-233401 and JP-A-7-233402. . That is, the present inventors have made intensive efforts to find an alloy element that increases the amount of residual graphite from the sintered body described in the above publication. As a result, a new finding that when sintering using iron powder obtained by atomizing molten steel containing B with oxygen below IOOP pm with water significantly increases the amount of residual graphite in the sintered body. was obtained. Further, the point of the present invention lies in that a certain amount or more of B is biased toward the surface of the iron powder. The present invention embodies this finding.
  • the balance consists of Fe and unavoidable impurities, and the intensity ratio of B to Fe in the emission spectrum obtained by measuring the surface by Auger electron spectrometry is 0.05 or more.
  • This is an iron powder for powder metallurgy.
  • the present invention provides that the composition contains at least one selected from S, Se and Te in a total amount of 0.001% to less than 0.20% by weight, or Mo: 0.2% by weight.
  • 05-3.5 Iron powder for powder metallurgy characterized by containing 5% by weight.
  • the present invention is, in the iron powder, powders, characterized in that a mixture of MO0 3 powder and 0.05 to 0.7 wt% ⁇ beauty or W0 3 powder 0.05 to 0.7 wt% It is also an iron-based mixed powder for metallurgy.
  • the present invention relates to a method for producing iron powder for powder metallurgy
  • Oxygen 1 O O ppm or less
  • molten steel in which the balance is Fe and unavoidable impurities water-atomizing the molten steel into powder, and sequentially subjecting the powder to dehydration drying and reduction, It is a manufacturing method.
  • the present invention relates to the above composition of molten steel,
  • At least one selected from the group consisting of S, Se, and Te should contain 0.001% by weight to less than 0.20% by weight, and Mo should contain 0.05% to 3.5% by weight.
  • a method for producing iron powder for powder metallurgy characterized by the following.
  • FIG. 1 is a view showing an example of a luminescent spectrum obtained by measuring the surface of the iron powder according to the present invention by an Auger electron spectroscopy.
  • FIG. 2 is a diagram showing an example of the concentration distribution of each element at each position in the depth direction from the surface of the iron powder measured by Auger electron spectroscopy.
  • the horizontal axis of the sputtering time corresponds to the distance in the depth direction from the surface of the iron powder.
  • the Cr and Mn contents in the iron powder are suppressed to a low level, and instead, B is positively contained so that B is biased on the surface of the iron powder.
  • B is positively contained so that B is biased on the surface of the iron powder.
  • the self-lubricating action of the residual graphite improves the wear resistance of the sintered body. This is because when the molten steel containing B is atomized with water, part of B is easily oxidized by water and precipitates as B-based oxide on the surface of the iron powder, and this B-based oxide is being sintered. It is thought that the amount of residual graphite increases because the diffusion of C into iron powder is suppressed.
  • the first point of the present invention is to atomize molten steel having an oxygen content of 100 ppm or less, and the second point defines the degree of segregation of B on the surface of the iron powder as described in the claims. On the point. Due to these two points, compared with Japanese Patent Application No. 7-153 638, the amount of residual graphite was increased with a high B composition and a low S composition, and the machinability was further improved. Abrasion resistance was improved. . In particular, it was found that when the amount of graphite in the sintered body was 1% by weight or more, the abrasion resistance was significantly improved.
  • the above effects are promoted by using the above B in combination with S, Se, and Te.
  • He also proposed iron powder containing Mo.
  • Contact name The M o, rather than be contained by pre-alloyed with the molten steel stage, who mix the M o 0 3 powder to the iron powder according to the present invention described above is, even more machinability of the sintered body Improve. Further, W 0 3 powder also exhibits the same effect as the M o 0 3 powder was added to the present invention.
  • the iron powder for powder metallurgy or the iron-based mixed powder according to the present invention is mixed with copper powder or graphite powder as usual to form a compact, and when the compact is sintered, a large amount of residual graphite is obtained.
  • a sintered body excellent in machinability and abrasion resistance contained in the steel can be easily obtained. The reason for limiting the content of each element will be described below.
  • Part of B added to the molten steel precipitates as an oxide on the surface of the iron powder when the molten steel is atomized with water.
  • the oxide suppresses the diffusion of carbon into the iron powder particles and increases the amount of residual graphite in the sintered body. Let As a result, the machinability and wear resistance of the sintered body are improved.
  • the B-based oxide is very stable and does not react with H 2 , even if the sintering is performed in a hydrogen atmosphere, the B-based oxide is similar to the steel powder described in Japanese Patent Application Laid-Open No. In addition, the machinability of the sintered body does not decrease. It should be noted that the method of simply mixing Fe-B alloy powder with iron powder containing no B does not increase the amount of residual graphite in the sintered body. There was no improvement in machinability and the like.
  • B on iron powder The intensity ratio of B to Fe in the luminescent spectrum measured by Auger electron spectroscopy is 0.05 or more.
  • FIG. 1 shows an example of the emission spectrum obtained by the measurement.
  • the inventors obtained the intensity ratio of B to Fe from the spectrum as shown in FIG. Specifically, as shown in the figure, the peak-to-peak value of Fe corresponding to the electron energy of 703 eV (horizontal axis), and the peak value of B at the position of 179 eV -to-Peak value ratio. According to the research of the inventor, the amount of residual graphite in the sintered body increased when the strength ratio was 0.05 or more, but was not recognized when the strength ratio was less than 0.05. Therefore, in the present invention, the condition of the iron powder is to have an intensity ratio of 0.05 or more.
  • Fig. 2 shows an example of the concentration distribution of each element in the depth direction from the iron powder surface measured by Auge electron spectroscopy. Note that the horizontal axis The aging time is a measure of the distance in the depth direction from the surface of the iron powder.
  • the B concentration on the iron powder surface was 17 atomic%. Further, the thickening together with the surface of B, the oxygen are also enriched with, B is Ru seems to be present in B 2 0 3 forms.
  • the accelerating voltage of the primary electron beam was 10 kV and the beam current was 1. I wA.
  • the measured data was read as 1. O OeV st step and 50 ms e c st step, the integration was performed once, and a 5-point differentiation was performed to obtain a differential spectrum.
  • Cr Since Cr easily forms oxides and covers the surface of the iron powder and inhibits surface segregation of B, its content must be kept as low as possible. Cr forms carbides and increases the hardness of the sintered body to reduce machinability. Therefore, in the present invention, Cr is set to 0.07% by weight or less. A preferable range is 0.02 to 0.06% by weight in consideration of the machinability and wear resistance of the sintered body and the production cost.
  • Mn is an element that reduces residual graphite.
  • Mn in the iron powder particles combines with S, Se, and Te to form a compound, and reduces S, Se, and Te, which are effective in increasing the residual graphite in the sintered body.
  • Mn forms oxides to cover the surface of the iron powder and inhibits segregation on the surface of B. For this reason, if the content is 0.3% by weight or more, the amount of residual graphite in the sintered body is reduced, and the machinability is reduced.
  • the preferred range is from 0.07 to 0.15% by weight in view of the refining cost required for reducing the amount of Mn in the step of adjusting the molten steel component and the machinability of the sintered body.
  • Total of one or more of S, Se, and Te 0.001 to 0.20% by weight S, Se, and Te are included to increase the amount of residual graphite in the sintered body.
  • the total amount is limited to 0.001 to less than 0.20% by weight. If the content exceeds 0.20% by weight, "soot" is generated during sintering, and the mechanical parts as products become too hot. Therefore, this value was set as the upper limit. On the other hand, if the content is less than 0.001% by weight, there is no effect of increasing the amount of residual graphite, so the content is limited to the above range.
  • Mo is included to increase the strength of the iron powder. However, if the amount is less than 0.05% by weight, no improvement in strength is observed, and if it exceeds 3.5% by weight, the machinability of the sintered body is sharply reduced. From the viewpoint of strength and machinability, a preferable range is 0.4 to 0.7% by weight.
  • Mo 0 3 powder . 0.05 to 0 7% by weight
  • W0 3 powder . 0.05 to 0 7% by weight of any one or more
  • MO0 3 and W0 3 flour then mixed with the iron powder according to the present invention is utilized to form the novel powder ⁇ gold for mixed powder.
  • the purpose of the mixing is to improve the machinability of the sintered body and to increase the strength by solid solution hardening.
  • Mixing amount of Mo 0 3 powder and WO 3 powder is at less than 0.05, the effect is not observed, and when it exceeds 0.7 wt%, bainite in the iron particles are generated, the sintered body Strength decreases. For this reason, the mixing amounts were all in the range of 0.05 to 0.7% by weight.
  • the iron powder, MO0 3 powder, W0 3 when mixed and any one or more of graphite powder and copper powder powder, known segregation prevention treatment thereto JP-1 - 1 657 01 JP It is more preferable to mix after applying.
  • MO0 3 powder, W0 3 powder is homogeneously mixed iron powder Runode, compared with the simple mixing method, because Mo in the sintered body, the formation of a solid solution in the iron powder W is uniform quality .
  • the ferrite phase in the iron particles becomes finer, and the strength of the sintered body is increased by about 15% by weight as compared with the case where it is manufactured by a simple mixing method.
  • Oxygen in molten steel 100 ppm or less
  • the iron powder according to the present invention is formed by atomizing molten steel adjusted to the above composition range with water.
  • the oxygen (0) content in the molten steel should be 100 ppm or less, preferably 70 ppm or less. If the amount of 0 in the molten steel exceeds 100 ppm, B becomes B 2 ⁇ 3 before atomization and turns into slag, and the amount of B effective for iron powder decreases. Accordingly, the suppressed as low as possible 0 amount in the molten steel, B was ⁇ Bok Mize from dissolving in the molten steel, it is important that the B with water by oxidizing to segregate the iron powder surface as B and B 2 0 3 is there.
  • the iron powder formed by water atomization is then dried, dehydrated and reduced as usual, and then crushed and classified into iron powder.
  • Iron powder composition B: 0.02 to 0.10% by weight, Cr: 0.02 to 0.04% by weight, Mn: 0.06 to 0.07% by weight, the balance being Fe and inevitable
  • iron powder composition B: 0.02 to 0.10% by weight, Cr: 0.02 to 0.04% by weight, Mn: 0.06 to 0.07% by weight, the balance being Fe and inevitable
  • molten steel having a predetermined composition at a temperature of 1630 ° C was atomized with water to obtain a powder.
  • This powder was dried under a nitrogen atmosphere at a temperature of 140 ° C. for 60 minutes, and then subjected to a reduction treatment in a pure hydrogen atmosphere at a temperature of 93 (TC temperature for 20 minutes. After cooling, the powder was taken out of the reduction furnace.
  • the powder thus obtained was pulverized and classified to obtain Nos. 1 to 6 shown in Table 1.
  • an iron powder containing S: 0.02 to 0.10% by weight in addition to the composition of the iron powder was manufactured by the same manufacturing method. These are Nos. 7 to 10 shown in Table 1.
  • the oxygen content of the molten steel before atomization was adjusted to 40 to 200 ppm by adding iron carbide.
  • the surfaces of Nos. 1 to 9 produced in this way were analyzed by Auger electron spectroscopy. And the intensity ratio of the Peak-to-Peak value of B (179 eV) to the Peak-to-Peak value of Fe (703 eV) is measured from the spectrum. Calculated. The measurement method and measurement conditions are as described above. Next, 1.2% by weight of graphite powder and 2.0% by weight of copper powder were mixed with these iron powders, and 1 part by weight of zinc stearate was added to 100 parts by weight of the mixed powder. Pressure was applied to a density of 6.85 gXcm 3 to obtain a columnar molded body. These compacts were sintered at a temperature of 1130 ° C. for 20 minutes under a nitrogen stream containing 10% by volume of hydrogen.
  • the amount of residual graphite in the obtained sintered body was determined by an infrared absorption method from a filtrate obtained by dissolving a part (sample) of the sintered body with nitric acid and filtering the residue through a glass filter.
  • the machinability of each sintered body was evaluated separately by using these iron powders to produce a columnar sintered body with an outer diameter of 60 m ⁇ and a height of 1 Omm, and evaluating the sintered body as a test piece. Valued. Specifically, first, a high-speed steel drill with a diameter of 2 mm ⁇ is rotated under the conditions of 10000 rpm and 0.012 mmZreV, and a number of holes are drilled in the test piece. Then, the average number of holes drilled before the drill cannot be drilled (the average value of three drills) is obtained, and the larger the value (the longer the life of the tool used), the better the machinability. It was.
  • Table 1 summarizes the characteristics of the iron powder and the sintered body described above.
  • the sintered body manufactured from the iron powder for powder metallurgy according to the present invention has oxygen in the molten steel of 100 ppm or less, and is measured on the surface of the iron powder by Auger electron spectroscopy.
  • the intensity ratio of B to Fe in the spectrum obtained in this way is all 0.05 or more.
  • the amount of residual graphite in the sintered body was larger than that in the comparative example, and the machinability was greatly improved.
  • Example 5 After treating these iron powder and iron-base mixed powder in the same manner as in Example 1, the peak-to-peak value of Fe on the iron powder surface (703_, eV The peak intensity ratio of the Peak-to-Peak value (179 eV) of B with respect to) was measured. Further, the compact was sintered under the same conditions as in Example 1, and the amount of residual graphite and the machinability of the obtained sintered body were evaluated.
  • Table 2 shows that the sintered body manufactured from the atomized iron powder or the iron-based mixed powder according to the present invention has a large amount of residual graphite, a long tool life, and excellent machinability.
  • Water atomized iron powder having the composition shown in Table 3 was produced in the same manner as described above. They are four types of iron powder according to the present invention (Nos. 25 to 28) and three types of comparative examples (Nos. 29 to 31). 2% by weight of graphite powder and 15% by weight of copper powder are added to these iron powders, and 1% by weight of zinc stearate is further mixed as a lubricant, and the mixture is pressed to a density of 6.85 g / cm 3 and molded. Created body. Next, the molded body was sintered at a temperature of 1130 ° C. for 20 minutes in an atmosphere of RX gas (end temperature).
  • Table 3 also shows the amount of residual graphite in the sintered body and the vector intensity ratio between Fe and B by the above-mentioned Auge spectroscopy.
  • a cylindrical test specimen with an inner diameter of 1 ⁇ outer diameter of 20 mm ⁇ and a height of 8 mm was manufactured for each sintered body, and an S 45C shaft of 1 Omm ⁇ was placed inside the cylinder, with clearance from the hole wall. Inserted at 20 wm. Then, the abrasion resistance test was performed by rotating the shaft at a peripheral speed of 1 OOmZmin under a dry condition and gradually increasing the contact load from a low load. That is, the contact load when the shaft and the inner wall of the cylinder were seized was used as an index of the wear resistance of the sintered body.
  • the iron powder Nos. 25 to 28 according to the present invention had wear resistance of a load of 4 kgfZcm 2 or more.
  • the amount of graphite in the sintered body is 1% by weight or more, the abrasion resistance is remarkably improved.
  • No. 29 of the iron powder used as a comparative example had little segregation of B, and No. 30 did not contain B, and No. 31 contained excessive B, so The abrasion resistance of the sintered body manufactured using this was inferior to the iron powder according to the present invention.
  • the powdered metallurgy iron and the iron-based mixed powder according to the present invention when consolidated into a consolidated compact, has improved machinability and abrasion property of the consolidated body as compared with conventional iron powder and mixed powder. . Therefore, if these powders are used and mechanical parts are manufactured by powder metallurgy, the dimensional accuracy of the mechanical parts will increase and the life will be prolonged. It is.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)

Abstract

La présente invention concerne une poudre de fer et un mélange de poudre à base de fer pour la métallurgie des poudres, permettant d'obtenir des produits de frittage présentant d'excellentes qualités d'usinabilité et de résistance à l'usure. Cette poudre de fer contient de 0,03 à 0,3 % en masse de bore, au maximum 0,07 % en masse de chrome, moins de 0,3 % en masse de manganèse, le reste étant constitué de fer et des inévitables impuretés. Le spectre de surface de la poudre en spectroscopie Auger donne un rapport d'intensités d'au moins 0,05 entre bore et fer. Cette poudre sert à augmenter la quantité de graphite restant dans les produits de frittage de façon à améliorer l'usinabilité et la résistance à l'usure de ces produits de frittage. On réalise une autre poudre de fer en ajoutant à la première poudre du soufre, du sélénium, du tellure, du molybdène ou similaire. Ces poudres, mélangées à de la poudre de MoO3 ou du WO3, donnent finalement ce qu'on appelle mélange de poudre à base de fer. Ce mélange s'obtient par atomisation à l'eau des poudres ci-dessus tout en ramenant la teneur en oxygène de l'acier en fusion à 100 ppm ou moins.
PCT/JP1996/003007 1995-10-18 1996-10-17 Poudre de fer pour metallurgie des poudres, procede de production correspondant et melange de poudre a base de fer pour metallurgie des poudres Ceased WO1997014523A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP51569097A JP3353836B2 (ja) 1995-10-18 1996-10-17 粉末冶金用鉄粉、その製造方法及び粉末冶金用鉄基混合粉
EP96935351A EP0808681A4 (fr) 1995-10-18 1996-10-17 Poudre de fer pour metallurgie des poudres, procede de production correspondant et melange de poudre a base de fer pour metallurgie des poudres

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Application Number Priority Date Filing Date Title
JP27027595 1995-10-18
JP7/270275 1995-10-18

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WO1997014523A1 true WO1997014523A1 (fr) 1997-04-24

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RU2162390C1 (ru) * 1999-12-09 2001-01-27 Общество с ограниченной ответственностью фирма "Спецметаллы" Железный порошок, полученный распылением металлов
US9469890B2 (en) 2009-03-20 2016-10-18 Hoganas Ab (Publ) Iron vanadium powder alloy
KR101026236B1 (ko) * 2009-12-09 2011-03-31 한국원자력연구원 레이저유도 플라즈마 스펙트럼을 이용한 원자로 냉각수 누설 감지 시스템 및 방법

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JPH0892708A (ja) * 1994-07-28 1996-04-09 Kawasaki Steel Corp 粉末冶金用混合鉄粉および切削性に優れた焼結鋼の製造方法

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JPS61253301A (ja) * 1985-04-30 1986-11-11 Daido Steel Co Ltd 粉末冶金用合金鋼粉末及びその製造方法
JPH03247743A (ja) * 1990-02-26 1991-11-05 Kawasaki Steel Corp 耐食性、被削性および鏡面性に優れた焼結合金鋼およびその製造方法
JPH07233402A (ja) * 1993-12-28 1995-09-05 Kawasaki Steel Corp 切削性、耐摩耗性に優れたアトマイズ鋼粉およびその焼結鋼

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EP0808681A4 (fr) 1999-12-29
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