CN1701129A - Alloy steel powder for metal injection molding improved in sintering characteristics and sintered article - Google Patents

Alloy steel powder for metal injection molding improved in sintering characteristics and sintered article Download PDF

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CN1701129A
CN1701129A CN 200480001037 CN200480001037A CN1701129A CN 1701129 A CN1701129 A CN 1701129A CN 200480001037 CN200480001037 CN 200480001037 CN 200480001037 A CN200480001037 A CN 200480001037A CN 1701129 A CN1701129 A CN 1701129A
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sintering
steel powder
injection molding
metal injection
improves
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CN100497709C (en
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曽田裕二
相原道孝
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Mitsubishi Steel KK
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Mitsubishi Steel KK
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Abstract

An alloyed steel powder for metal injection molding that eliminates the problems of decreased product strength and difficulty of temperature control which exist in conventional alloys for sintering and that improves productivity of the sintering furnace is provided, together with a sintered body thereof. This is an alloyed steel powder for metal injection molding which consists as mass percentages of 0.1 to 1.8% C, 0.3 to 1.2% Si, 0.1 to 0.5% Mn, 11 to 18% Cr, 2 to 5% Nb and the remainder Fe and unavoidable impurities, and which may further comprise 5.0% or less of at least one of Mo, V and W, or a sintered body (wherein C is 0.1 to 1.7%) of these powders. As shown in Figures 6 through 9, the alloyed steel powder for metal injection molding of the present invention results in a sintered body with a constant sintered density over a 50 DEG C range of sintering temperatures, thereby facilitating sintering temperature control and improving productivity.

Description

The metal ejection formation that coking property improves Alloy Steel Powder and sintered compact
Technical field
The effective metal injection molding (MIM) of complicated shape part that the present invention relates to be used to obtain the martensitic stainless steel of the good high rigidity of dimensional precision, high corrosion resistance and alloy tool steel is with Alloy Steel Powder and sintered compact.
Background technology
Metal ejection formation powder as for the sintered compact that obtains high rigidity, high corrosion resistance uses SKD11, SUS420, SUS440C etc. all the time.Obtain the steel class of hardness based on these Cr carbide, present the austenite phase in its sintering range, to move (diffusion) speed slower than ferritic phase for the element that sintering is carried out, and coking property is bad.On the other hand, if temperature is brought up to the temperature range that liquid phase occurs for carrying out sintering, then generate a large amount of liquid phases once, carbide forms netted on the crystal grain interface, product strength is significantly descended, or even the distortion to keep article shape occurs.For avoiding the generation of above-mentioned situation, sintering temperature must be controlled at ± 5 ℃, promptly carry out sintering in the very narrow temperature range about 10 ℃.Thus, have to sacrifice productivity and limit sintering oven may use the field.
Summary of the invention
The object of the invention is to provide the reduction of elimination as the product strength of the problem of above-mentioned existing sintering alloy, sintering control difficulty, and the metal ejection formation that helps the productivity improving article characteristic and improve sintering oven is with Alloy Steel Powder and sintered compact.
For solving above-mentioned problem, the present invention is constructed as follows.
(1) a kind of metal ejection formation Alloy Steel Powder of coking property improvement, it is characterized in that by in quality % C:0.1～1.8%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
(2) a kind of metal ejection formation Alloy Steel Powder that improves behind the sintered compact, it is characterized in that by in quality % C:0.1～1.8%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Mo, V, W's is at least a: below 5.0% or 5.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
(3) the metal ejection formation Alloy Steel Powder of above-mentioned (2) described coking property improvement, wherein at least a of Mo, V, W is 0.3～1.6%.
(4) a kind of metal ejection formation steel alloy sintered compact of coking property improvement, it is characterized in that by in quality % C:0.1～1.7%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
(5) a kind of metal ejection formation steel alloy sintered compact of coking property improvement, it is characterized in that by in quality % C:0.1～1.7%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Mo, V, W's is at least a: below 5.0% or 5.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
(6) the metal ejection formation steel alloy sintered compact of above-mentioned (5) described coking property improvement,
Wherein at least a of Mo, V, W is 0.3～1.6%.
The starting point of the present invention is to generate the low Nb carbide of diffustivity by add the Nb carbide in based on the steel class of Cr carbide.This Nb carbide is because velocity of diffusion is low, so be difficult to thickization of diffusion when sintering metal ejection formation thing, in addition, the Cr carbide serves as that nuclear is separated out with the Nb carbide also.
Utilize the pin stopping function of this Nb carbide, compare, can suppress thickization, nettedization of carbide with the situation that only has the Cr carbide.
In composition of the present invention, C forms carbide and increases hardness, constitutes martensitic stucture.The scope preferred 0.1～1.8% of the C amount of powder.Sintering temperature and sintered density change along with the variation of the amount of C.Therefore, during powder compacting, add an amount of graphite, the C amount of sinter is adjusted to 0.1～1.7%.Like this, under the temperature of control easily, make the high sintered compact of sintered density and become possibility.Making the lower limit amount of the C amount of powder, sintered compact be 0.1%, is to be reached for to make the necessary minimum quantity of above-mentioned Nb carbide, is that solid solution C makes the required minimum quantity of martensite in matrix simultaneously.Make powder C amount on be limited to 1.8%, be limited to 1.7% on the sintered compact C amount, be because the C amount that from powder, disappears during sintering, and C forms the Cr carbide and improves hardness in sintered compact, even content surpasses 1.7% hardness and also no longer improves, toughness descends on the contrary.
Si improves deoxidation, hot water flow.If its amount is less than 0.3%, then the quantitative change of oxygen is many, and hot water flow degenerates.If greater than 1.2% hardenability degenerate.
If Mn less than 0.1% hot water flow degenerate, in addition, if greater than 0.5% then combine with oxygen, the oxygen amount of powder increases.Therefore, be controlled in 0.1～0.5% the scope.
Cr improves hardenability, generates carbide and improves hardness.Can improve erosion resistance in the bag carbide substrate in further will being solidly soluted into.Preferred 11.0%～18.0% scope.
Mo, V, W generate carbide, with the effect of Nb to the stop of Cr carbide performance pin, improve intensity, the hardness of sintered compact.If their content greater than 5.0% toughness reduce, so below preferred 5.0% or 5.0%, but consider hardenability and economy, preferred especially 0.3～1.6% scope.If less than 0.3% then be difficult to see the effect that significantly improves hardness, if greater than 1.6% then economy is bad.
Nb is the pin stopping function that utilizes the low Nb carbide of diffustivity to produce, and the diffusion that suppresses the Cr carbide improves hardenability.By adding 2.0～5.0% Nb, can control sintering temperature with having at present in ± 5 ℃ of scopes, expand to ± 25 ℃ of scopes in, can improve the productivity of sintering oven.If the amount of Nb is less than 2.0% then its effect is insufficient, if greater than 5.0% then the amount of oxygen increases formability degenerates.
The simple declaration of accompanying drawing
Fig. 1 is for showing the figure of the agglomerating mode that adopts in the present embodiment.
Fig. 2 is the figure with the sintering characteristic curveization of SKD11.
Fig. 3 is the figure with the sintering characteristic curveization of SUS420.
Fig. 4 is the figure with the sintering characteristic curveization of SUS440C.
Fig. 5 is the figure with the sintering characteristic curveization of comparative example 1.
Fig. 6 is the figure with the sintering characteristic curveization of the embodiment of the invention 1.
Fig. 7 is the figure with the sintering characteristic curveization of the embodiment of the invention 2.
Fig. 8 is the figure with the sintering characteristic curveization of the embodiment of the invention 3.
Fig. 9 is the figure with the sintering characteristic curveization of the embodiment of the invention 4.
The preferred forms of invention
Prepare the test portion shown in the following table 1, carry out the test of sintering characteristic.
Table 1
Steel grade Form (%) ??Dm ??(μm) ????T/D ????(g/cm 3)
??C ??Si ??Mn ??Cr ??Mo ??V ??W ?Nb ??O ??Fe
?SKD11 ??1.66 ??0.34 ??0.44 ??11.80 ??1.02 ??- ??- ??- ??3300 All the other ??11.90 ????4.04
?SUS420 ??0.27 ??0.85 ??0.33 ??13.09 ??0.59 ??- ??- ??- ??3200 All the other ??10.01 ????4.30
?SUS440C ??0.96 ??0.91 ??0.18 ??17.12 ??0.05 ??0.07 ??- ??- ??2700 All the other ??9.72 ????4.21
Comparative example 1 ??0.60 ??0.73 ??0.47 ??12.53 ??1.49 ??- ??- ??0.34 ??3900 All the other ??10.22 ????4.27
Embodiment 1 ??1.03 ??0.92 ??0.22 ??17.01 ???- ??- ??- ??3.01 ??4100 All the other ??9.92 ????4.17
Embodiment 2 ??0.66 ??0.88 ??0.44 ??12.18 ??1.42 ??- ??- ??3.22 ??4200 All the other ??10.98 ????4.18
Embodiment 3 ??0.96 ??0.87 ??0.21 ??17.12 ??0.41 ??0.17 ??0.08 ??2.99 ??3400 All the other ??9.86 ????4.08
Embodiment 4 ??0.56 ??0.93 ??0.31 ??12.34 ??0.50 ??- ??- ??2.81 ??2500 All the other ??9.92 ????4.17
Comparative example 2 ??0.65 ??0.89 ??0.45 ??12.15 ??1.46 ??- ??- ??7.33 ??13500 All the other ??10.34 ????4.20
Each test portion is adjusted the C amount.C measured after the interpolation powdered graphite made sintering, SKD11 is 1.30%, 1.50%, 1.70%, SUS420 is 0.30%, 0.50%, 0.70%, 0.90%, embodiment 1 is 1.30%, SUS440C is 0.75%, 0.80%, 1.00%, 1.20%, comparative example 1 and embodiment 2 are 0.50%, 0.70%, 0.90%, and embodiment 3 is 1.30%, and embodiment 4 is 0.90%.Because the quantitative change of comparative example 2 oxygen in the stage of powder is excessive, so do not carry out agglutinating test.
Agglutinating test is as described below carries out.
In the metal-powder shown in the table 1, according to the C behind sintering amount target value, add suitable amount of graphite respectively, to the stearic acid that wherein adds 5.0wt% (outer number), under 80 ℃, heat equably and mix.
After the thing that will mix is cooled to room temperature, pulverize the particle after solidifying.The particle of this pulverizing is pressed 0.6Ton/cm in moulding 2Lower compression moulding (φ 11.3 * 10t, N=3).
Carry out sintering in the mode shown in Fig. 1.In Fig. 1, sintering temperature in the temperature shown in suitable table 2～table 5, for example, is carried out under 1370 ℃, 1390 ℃, 1410 ℃ etc.
Table 2～table 5 shows each test portion, the sintered density under the relation of the C amount target value behind sintering temperature and the sintering.Below table 2～table 5, show C, the O of the sinter of each test portion, the amount of N, and in table 4 and table 5, further shown sintering hardness (Hv).To be Fig. 2～Fig. 9 after the sintering characteristic march linearize that show in table 2～table 5.
Tissues observed, the hardness of mensuration sintered compact is determined suitable sintering temperature span of control limit of control respectively.Suitable sintering temperature span of control limit of control, in sintering temperature-sintered density figure along with the rising of sintering temperature, sintered density is at ± 0.1g/cm 3The substantially invariable sintering temperature amplitude of scope.
Table 2
Steel grade SKD11 Steel grade ??SUS420
C amount target value (%) behind the sintering C amount target value (%) behind the sintering
??1.30 ??1.50 ??1.70 ??0.30 ??0.50 ??0.70 ??0.90
Molding density ??4.91 ??4.90 ??4.88 Molding density ??4.85 ??4.81 ??4.78 ??4.76
Sintering temperature ℃ ??1220 ??- ??- ??6.84 Sintering temperature ℃ ??1250 ??- ??- ??6.75 ??7.07
??1230 ??- ??6.71 ??7.25 ??1270 ??- ??- ??6.82 ??7.47
??1240 ??6.81 ??7.20 ??7.61 ??1290 ??- ??- ??7.06 ??7.78
??1250 ??1260 ??7.21 ??7.68 ??7.58 ??7.70 ??7.69 ??7.69 ??1310 ??6.82 ??- ??7.38 ??7.91
??- ??- ??- ??- ??1330 ??6.84 ??6.98 ??7.79 ??-
??1270 ??7.71 ??7.69 ??- ??1350 ??6.86 ??7.27 ??7.85 ??-
??- ??- ??- ??- ??1370 ??6.92 ??7.70 ??- ??-
??- ??- ??- ??- ??1390 ??7.41 ??7.69 ??- ??-
??- ??- ??- ??- ??1410 ??7.70 ??- ??- ??-
??C(％) ??1.28 ??1.47 ??1.66 ??C(％) ??0.33 ??0.57 ??0.79 ??0.99
??O(ppm) ??11 ??10 ??11 ??O(ppm) ??17 ??40 ??27 ??41
??N(ppm) ??7 ??8 ??9 ??N(ppm) ??3 ??4 ??1 ??3
Table 3
Steel grade SUS440C Steel grade Comparative example 1
C amount target value (%) behind the sintering C amount target value % behind the sintering)
??0.75 ??0.80 ??1.00 ??1.20 ??0.50 ??0.70 ??0.90
Molding density ??5.01 ??5.00 ??4.96 ??4.94 Molding density ??4.68 ??4.69 ??4.69
Sintering temperature ℃ ??1230 ??- ??- ??6.72 ??6.70 Sintering temperature ℃ ??1270 ??5.44 ??6.23 ??7.38
??1240 ??6.88 ??6.91 ??6.88 ??6.93 ??1.290 ??5.71 ??6.92 ??7.77
??1250 ??6.93 ??6.94 ??7.00 ??7.10 ??1310 ??6.50 ??7.75 ??7.77
??1260 ??6.97 ??7.00 ??7.19 ??7.52 ??1330 ??7.31 ??7.76 ??-
??1270 ??7.03 ??7.12 ??7.61 ??7.63 ??1350 ??7.77 ??- ??-
??1280 ??7.14 ??7.26 ??7.64 ??- ??1370 ??7.77 ??- ??-
??1290 ??7.24 ??7.41 ??7.63 ??- ??- ??- ??- ??-
??1300 ??7.36 ??7.56 ??- ??- ??- ??- ??- ??-
??- ??- ??- ??- ??- ??- ??- ??- ??-
??C??(％) ??0.84 ??0.86 ??1.04 ??1.24 ??C(％) ??0.54 ??0.76 ??0.96
??0(ppm) ??130 ??60 ??42 ??34 ??O(ppm) ??21 ??14 ??20
??N(ppm) ??7 ??7 ??5 ??6 ??N(ppm) ??3 ??2 ????13
Table 4
Steel grade Embodiment 1 Steel grade Embodiment 2
Agglomerating C measures target value (%) Agglomerating C measures target value (%)
??1.30 0.50 ??0.70 ??0.90
Molding density ??4.41 Molding density 4.56 ??4.55 ??4.56
Sintering temperature ℃ ????1240 ??6.34 Sintering temperature ℃ ????1290 5.88 ??6.12 ??6.44
????1250 ??7.10 ????1310 6.79 ??6.98 ??7.27
????1260 ??7.68 ????1330 7.76 ??7.76 ??7.76
????1270 ??7.69 ????1350 7.76 ??7.75 ??7.75
????1280 ??7.70 ????1370 7.77 ??7.76 ??7.77
????1290 ??7.70 ????- - ??- ??-
????1300 ??7.69 ????- - ??- ??-
????1310 ??7.70 ????- - ??- ??-
????- ??- ????- - ??- ??-
??C(％) ??1.25 ??C(％) 0.52 ??0.73 ??0.94
??O(ppm) ??11 ??O(ppm) 26 ??22 ??32
??N(ppm) ??7 ??N(ppm) 10 ??8 ??7
Sintering hardness (Hv) ??700 Sintering hardness (Hv) 600 ??640 ??310
Table 5
Steel grade Embodiment 3 Steel grade Embodiment 4
Agglomerating C measures target value (%) Agglomerating C measures target value (%)
??1.30 ??0.90
Molding density ??4.85 Molding density ??4.85
Sintering temperature ℃ ????1230 ??- Sintering temperature ℃ ????1300 ??6.84
????1240 ??6.37 ????1310 ??7.25
????1250 ??7.14 ????1320 ??7.58
????1260 ??7.71 ????1330 ??7.83
????1270 ??7.72 ????1340 ??7.83
????1280 ??7.72 ????1350 ??7.83
????1290 ??7.72 ????1360 ??7.79
????1300 ??7.71 ????1370 ??7.77
????1310 ??7.72 ????1380 ??7.75
??C(％) ??1.35 ?C(％) ??0.94
??O(ppm) ??46 ?O(ppm) ??11
??N(ppm) ??28 ?N(ppm) ??9
Sintering hardness (Hv) ??749 Sintering hardness (Hv) ??680
As mentioned above, add the metal ejection formation Alloy Steel Powder of the present invention of Nb, compare with SKD11, SUS420 and SUS440C, suitable sintering temperature span of control limit of control enlarges.That is, suitable sintering temperature span of control limit of control is about 10 ℃ in SKD11, SUS420 and SUS440C, expands in the present invention about 50 ℃, and it is easy that the control of sintering temperature becomes, and productivity improves.In addition, the susceptibility of the C value behind the sintering is weakened, under 0.5～0.9% C value, present sintering characteristic (temperature on density) much at one.

Claims (6)

1. the metal ejection formation Alloy Steel Powder that improves of a coking property, it is characterized in that by in quality % C:0.1～1.8%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
2. metal ejection formation Alloy Steel Powder that improves behind the sintered compact, it is characterized in that by in quality % C:0.1～1.8%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Mo, V, W's is at least a: below 5.0% or 5.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
3. the metal ejection formation Alloy Steel Powder that coking property as claimed in claim 2 improves, at least a of wherein said Mo, V, W is 0.3～1.6%.
4. the metal ejection formation steel alloy sintered compact that improves of a coking property, it is characterized in that by in quality % C:0.1～1.7%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
5. the metal ejection formation steel alloy sintered compact that improves of a coking property, it is characterized in that by in quality % C:0.1～1.7%, Si:0.3～1.2%, Mn:0.1～0.5%, Cr:11.0～18.0%, Mo, V, W's is at least a: below 5.0% or 5.0%, Nb:2.0～5.0%, all the other are that iron and unavoidable impurities constitute.
6. the metal ejection formation steel alloy sintered compact that coking property as claimed in claim 5 improves, at least a of wherein said Mo, V, W is 0.3～1.6%.
CNB2004800010370A 2003-02-13 2004-02-10 Alloy steel powder for metal injection molding improved in sintering characteristics and sintered article Expired - Fee Related CN100497709C (en)

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102528016A (en) * 2012-01-17 2012-07-04 建德市易通金属粉材有限公司 Powdered alloy steel for metal injection molding and preparation method thereof
CN103567447A (en) * 2012-07-31 2014-02-12 台耀科技股份有限公司 Method for preparing powder metallurgy workpiece and workpiece thereof
CN104789896A (en) * 2015-04-21 2015-07-22 苏州统明机械有限公司 Wear-resisting alloy steel powder for thermal spraying and preparation method thereof
CN104789897A (en) * 2015-04-21 2015-07-22 苏州统明机械有限公司 High-alloy steel powder for thermal spraying and preparation method thereof
CN108188388A (en) * 2017-12-29 2018-06-22 中国第汽车股份有限公司 A kind of powder injection-molded material of stainless steel metal for fuel injector ball seat
CN109609862A (en) * 2019-01-02 2019-04-12 江西安而泰合金科技有限公司 A kind of stainless steel material suitable for preparing ventilative steel

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102528016A (en) * 2012-01-17 2012-07-04 建德市易通金属粉材有限公司 Powdered alloy steel for metal injection molding and preparation method thereof
CN102528016B (en) * 2012-01-17 2013-09-11 建德市易通金属粉材有限公司 Powdered alloy steel for metal injection molding and preparation method thereof
CN103567447A (en) * 2012-07-31 2014-02-12 台耀科技股份有限公司 Method for preparing powder metallurgy workpiece and workpiece thereof
CN104789896A (en) * 2015-04-21 2015-07-22 苏州统明机械有限公司 Wear-resisting alloy steel powder for thermal spraying and preparation method thereof
CN104789897A (en) * 2015-04-21 2015-07-22 苏州统明机械有限公司 High-alloy steel powder for thermal spraying and preparation method thereof
CN108188388A (en) * 2017-12-29 2018-06-22 中国第汽车股份有限公司 A kind of powder injection-molded material of stainless steel metal for fuel injector ball seat
CN109609862A (en) * 2019-01-02 2019-04-12 江西安而泰合金科技有限公司 A kind of stainless steel material suitable for preparing ventilative steel

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