CN1436874A - Thermal tool steel - Google Patents
Thermal tool steel Download PDFInfo
- Publication number
- CN1436874A CN1436874A CN02156718A CN02156718A CN1436874A CN 1436874 A CN1436874 A CN 1436874A CN 02156718 A CN02156718 A CN 02156718A CN 02156718 A CN02156718 A CN 02156718A CN 1436874 A CN1436874 A CN 1436874A
- Authority
- CN
- China
- Prior art keywords
- quality
- carbide
- inclusion
- metallic inclusion
- machinability
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A hot toolsteel comprises 0.10 to 0.70% C, 0.10 to 0.80% Si, 0.30 to 1.00% Mn, 0.007 to 0.020% P, 3.00 to 7.00% Cr, W and Mo in 0.20 to 12.00% in terms of (1/2W+Mo) alone or in combination, 0.10 to 3.00% V, 0.05 to 0.80% Ni, <=6.50% Co and <=0.150% S, and the balance substantially Fe with inevitable impurities. The cleanliness of nonmetallic inclusions is <=0.020%, and, on annealing, the area ratio of carbides and nonmetallic inclusions having particle diameters of >1.0 mu m is <=0.004%. The hot tool steel has improved heat check and erosion resistances, and has remarkably improved machinability by the above technical measure.
Description
Technical field
The present invention relates to be used for the Thermal tool steel of heat forged mould, extrusion die and die casting etc., particularly control carbide and non-metallic inclusion, improve the Thermal tool steel that machinability, heat-resistant cracking and refractory decrease property.
Background technology
In the past, the flexible technology (No. 2809622 patent of Japan, the open communique of No. 61331/1999 application for a patent for invention) of improving Thermal tool steel by the purity that improves non-metallic inclusion was once disclosed.In addition, the somebody has proposed the number by increasing inclusion, the shape that makes inclusion becomes the spherical technology of improving machinability (Fig. 2 that No. 3, electric system steel 64 volumes are the 191st～201 page and Fig. 4, the open communique of No. 61331/1999, No. 60585/1998 application for a patent for invention of Japan).But above-mentioned prior art is to estimate inclusion according to standards such as JISGO555 or ASTM E45-76, thereby is kind and the quantity of having stipulated inclusion, size that can't the quantitative evaluation inclusion.
The somebody had once proposed by adjusting the technology (the open communique of Japan No. 60585/1998, No. 217147/1997, No. 358040/1992 and No. 269603/1999 application for a patent for invention) of improving machinability of forming.In addition, there is the people also to propose, improves the technical scheme No. 5, thermal treatment 39 volumes (the 225th～226 page, No. 2809622 patent of invention of Japan) of machinability by improving tissue.
But these known technologies are not considered the size of carbide and non-metallic inclusion, thereby they all are to have sacrificed other performance and only improved machinability.
Summary of the invention
The objective of the invention is,, be provided at the Thermal tool steel that significantly improves machinability when improving heat-resistant cracking and refractory damage property by the size of suitable qualification carbide and non-metallic inclusion.
Thermal tool steel of the present invention, it is characterized in that, contain C:0.10～0.70 quality %, Si:0.10～0.80 quality %, Mn:0.30～1.00 quality %, P:0.007～0.020 quality %, Cr:3.00～7.00 quality %, W and Mo independent or compound (1/2W+Mo): 0.20～12.00 quality %, V:0.10～3.00 quality %, Ni:0.05～0.80 quality %, below the S:0.150 quality %, surplus is made of Fe and unavoidable impurities basically, the purity of non-metallic inclusion (JISG055) is, dA60 * 400 are below 0.020%, dB60 * 400 are below 0.020%, dC60 * 400 are below 0.020%, d (A+B+C) is below 0.045%, simultaneously, when annealing, particle diameter surpasses the carbide of 1.0 μ m and the area occupation ratio of non-metallic inclusion is below 0.004%.In addition, can also contain below the Co:6.50 quality %.
In this Thermal tool steel, preferably, the carbide during annealing below the particle diameter 1.0 μ m and the area occupation ratio of non-metallic inclusion are more than 10.5%.
In addition, in this Thermal tool steel, preferably, during Q-tempering, particle diameter surpasses the carbide of 1.0 μ m and the area occupation ratio of non-metallic inclusion is below 0.004%.
In addition, in this Thermal tool steel, preferably, during Q-tempering, the carbide that particle diameter 1.0 μ m are following and the area occupation ratio of non-metallic inclusion are more than 0.038%.
Thermal tool steel of the present invention constitutes by the following stated, can further bring into play effect of the present invention, promptly, C:0.35～0.40 quality %, Si:0.55～0.65 quality %, Mn:0.35～0.45 quality %, P:0.007～0.010 quality %, Cr:4.60～5.00 quality %, W and Mo independent or compound (1/2W+Mo): 1.60～1.80 quality %, V:0.40～0.60 quality %, Ni:0.08～0.15 quality %, below the S:0.005 quality %, surplus is made of Fe and unavoidable impurities basically, the purity of non-metallic inclusion (JISG055) is, in dA60 * 400 below 0.0%, count below 0.0% with dB60 * 400, in dC60 * 400 below 0.0%, in d (A+B+C) below 0.0%, simultaneously, when annealing, particle diameter surpasses the carbide of 1.0 μ m and the area occupation ratio of non-metallic inclusion is below 0.004%.
The present invention has improved heat-resistant cracking and refractory damage property by suitably limiting the size of carbide and non-metallic inclusion, has improved machinability.But, reason owing to the steel composition, machinability obviously worsens, in order to improve the performance of heat-resistant cracking and refractory damage property and this two aspect of machinability, the present invention limits for the carbide that improves machinability and heat-resistant cracking and refractory damage property simultaneously and the size of inclusion in alleviating the steel of inclusion.That is, do not change the major ingredient of Thermal tool steel, by limiting the purity of impurity, the form of control inclusion by the shape and the quantity of preceding thermal treatment control carbide, thereby can improve machinability and heat-resistant cracking and refractory damage property simultaneously.
Embodiment
The present invention is described below in further detail.When reducing inclusion, heat-resistant cracking can improve.But, depending on the composition of steel, the effect of improvement is also different, and machinability significantly worsens.Therefore, heat-resistant cracking and machinability are difficult to take into account.The inventor finds, if the particle diameter of control carbide and non-metallic inclusion just can be taken into account heat-resistant cracking and machinability.
As the method that prolongs life tools, past people knows that all The amount of inclusions is many more, and machinability is good more.But the inventor finds, surpasses in the quenched and tempered steel of 45HRC in hardness, no matter the inclusion amount how, the occasion machinability that has is good, and the occasion machinability that has is poor.Therefore, the inventor thinks, under the purity good state, by the particle diameter and the amount of suitable control carbide and non-metallic inclusion, can improve machinability under the situation of not damaging other performance.
Carbide and the bigger steel of non-metallic inclusion particle diameter, machinability worsens, and small carbide and non-metallic inclusion below the 1.0 μ m are many more, and it is big more to improve effect.
In addition, compare with the brilliant carbide of paper congruent melting, precipitate into carbide in the matrix to improve effect bigger.As non-metallic inclusion, with Al
2O
3Compare, to be small and long-width ratio such as oxide compound, MnS, AlN have the effect that prolongs the cutting tool life-span, improve the effect of cutting tool life-span fluctuation and improve the effect that refractory decreases property and heat-resistant cracking at the particle below 1.3 for B based nitride and B.And thick non-metallic inclusion and carbide make refractory damage property and heat-resistant cracking significantly worsen.
For the machinability that improves, alleviate its fluctuation and refractory and decrease the Thermal tool steel that property, heat-resistant cracking and resistance to fatigue all are met, importantly, make the size of carbide and non-metallic inclusion become small, the distribution of carbide and non-metallic inclusion is very even, the amount of the inclusion of in known document, being put down in writing, by the size of control inclusion, the fluctuation that can alleviate machinability improves refractory damage property and heat-resistant cracking.
Decrease property and heat-resistant cracking for refractory, have the carbide that the initial stage hot tearing is not exerted an influence and the particle size range of non-metallic inclusion, what refractory was decreased that property and heat-resistant cracking exert an influence is carbide and the non-metallic inclusion that particle diameter surpasses 1.0 μ m.Therefore, in the present invention, reduce particle diameter and surpass the carbide of 1.0 μ m and the amount of non-metallic inclusion, increase and improve the bigger particle diameter of machinability effect 1.0 μ m following carbide and non-metallic inclusion.
The form of carbide and non-metallic inclusion and the control of amount can be carried out solution treatment in 1 minute～20 hours by heating under 1050～1190 ℃ before anneal, control cooling conditionss such as stove is cold, air cooling, oil cooling then and realize.
The composition that the following describes Thermal tool steel of the present invention limits the qualification foundation of foundation and inclusion.
The composition of Thermal tool steel:
C:0.10～0.70 quality %, 0.35～0.40 quality % preferably
C is solidly soluted in the matrix when quenching heating, and needed quenching hardness is provided, and in addition, forms alloy carbide with the alloy carbide forming element when tempering, separates out softening drag and hot strength when composing to tempering by this alloy carbide.In addition, C forms residual carbide, and the wear resistance under the high temperature is provided, and has the effect of thickization of crystal grain when preventing to quench heating.When C was too much, the carbide amount increased excessively, can not keep the needed toughness of hot tool, and cause that hot strength reduces, and therefore it being limited to below the 0.70 quality %, its content is crossed when hanging down, can not obtain above-mentioned additive effect, thereby it is defined as more than the 0.10 quality %.Preferably, C content is 0.35～0.40 quality %.
Si:0.10～0.80 quality %, 0.55～0.65 quality % preferably
During Si less than 0.10 quality %, microsegregation does not take place, and machinability worsens; In addition, when Si surpassed 0.80 quality %, banded segregation was serious, and the blade of cutting tool is turned, and toughness reduces, thereby Si content is defined as 0.10～0.80 quality %, preferably 0.55～0.65 quality %.
Mn:0.30～1.00 quality %, 0.35～0.45 quality % preferably
Mn is solid-solubilized in the matrix, and the effect that improves hardening capacity is very big.In order to obtain its additive effect, the addition of Mn must be more than 0.30 quality %.When the addition of Mn surpassed 1.00 quality %, annealing hardness was too high, and machinability reduces, and the A1 transformation temperature excessively reduces.Therefore, the addition of Mn is 0.30～1.00 quality %, preferably 0.35～0.45 quality %.
P:0.007～0.020 quality %, 0.007～0.010 quality % preferably
P segregation when solidifying is absolutely necessary for the degree of segregation that improves the strap after the hot-work in crystal boundary.As the fundamental element of the good cutting of keeping feature of the present invention, P content must be more than 0.007 quality %.But P adds when too much, and toughness reduces, and reduces in order to suppress flexible, and the higher limit of P is defined as 0.020 quality %, preferably 0.007～0.010 quality %.
Cr:3.00～7.00 quality %, 4.60～5.00 quality % preferably
Cr provides the most important element as the necessary hardening capacity of instrument.In addition, Cr improves scale resistance and the A1 transformation temperature is risen, and form residual carbide, thickization of crystal grain when suppressing to quench heating, can also improve wear resistance, separate out alloy carbide during tempering, improve the softening drag when heating up, have the effect that improves hot strength, its addition should be more than 3.00 quality %.When Cr is too much, excessively form the Cr carbide, cause that on the contrary hot strength reduces, thereby the Cr amount should be below 7.00 quality %, preferably 4.60～5.00 quality %.
The quality % of W and Mo:0.20 quality %≤(1/2W+Mo)≤12.00, the quality % of 1.60 quality %≤(1/2W+Mo)≤1.80 preferably
W and Mo form alloy carbide, by forming residual carbide, organize thickization in the time of can preventing to quench heating, in addition, separate out small alloy carbide during tempering, improve temper softening drag and hot strength, thereby are most important interpolation elements.And W and Mo have the effect that improves the A1 transformation temperature.The effect that W improves hot strength and wear resistance is big especially, and Mo is more more favourable than W aspect toughness.When Mo and W are too much, form thick carbide, cause toughness excessively to reduce, thereby, during the independent or compound interpolation of W and Mo, (1/2W+Mo) should be more than the 0.20 quality %, below the 12.00 quality %.
V:0.10～3.00 quality %, 0.40～0.60 quality % preferably
V is the strong carbide forming element, forms residual carbide, makes the effect of crystal grain microminiaturization bigger, and can improve the wear resistance under the high temperature.In addition, separate out small carbide during tempering in matrix, by adding jointly with W and Mo, it is very big to improve more than 600～650 ℃ the effect of the intensity of high-temperature zone, and has the effect that improves the A1 transformation temperature.V adds when too much, forms thick carbide, cause toughness to reduce, thereby its higher limit is decided to be below 3.00%.In order to obtain the additive effect of V, the content of V must be more than 0.10 quality %.Preferred content range is 0.40～0.60 quality %.
Ni:0.05～0.80 quality %, 0.08～0.15 quality % preferably
The Ni solid solution improves toughness and improves hardening capacity, thereby should add more than the 0.05 quality % in matrix.When Ni was too much, annealing hardness was too high, and machinability reduces, and causes that the A1 transformation temperature excessively reduces, and segregation significantly worsens, thereby the higher limit of Ni is decided to be 0.80 quality %.Preferred content range is 0.08～0.15 quality %.
Below the Co:6.50 quality %
The Co solid solution has the effect that improves hot strength, thereby can contain as required in matrix.In addition, Co improves the solid solubility limit of the carbide in the austenite when quenching heating, the amount of separating out of the alloy carbide when increasing tempering, and also therefore the aggegation drag of carbide precipitate when raising heats up also has the effect that improves the hot strength performance.In addition, because the intensification of instrument when using, Co forms the fine and close good oxide film of sticking power from the teeth outwards, has the wear resistance that improves under the high temperature and the effect of anti-freezing property.When Co was too much, toughness reduced, thereby is containing the occasion of Co, and its content should be below 6.50 quality %.
Below the S:0.150 quality %, preferably below the 0.005 quality %
S forms the MnS sulfides, extends to distribute on the hot-work direction, causes that the toughness of T direction reduces.Therefore, in order to keep the toughness of T direction, the higher limit of S should be below 0.150 quality %, preferably below the 0.005 quality %.
As, Sn, Sb, Cu, B and Bi are enriched in the crystal boundary place when solidifying, improve the banded segregation degree after the hot-work, cause the toughness of T direction to reduce, and in addition, segregation makes toughness reduce in the austenite grain boundary place or be present in the matrix when thermal treatment.And Pb extends distribution on the hot-work direction, makes the toughness of T direction reduce.
For above-mentioned reasons, the content of As, Sn, Sb, Cu, B, Pb and Bi should be limited in low especially level, and the inventor is through discovering, these element total amounts are 0.13% when following, even contain these impurity elements, also can reach purpose of the present invention.For each composition, wish that its content limit is respectively: below the As0.005%, below the Sn0.003%, below the Sb0.0015%, below the Cu0.08%, below the B0.0005%, below the Pb0.0002%, below the Bi0.0001%.
Other impurity element also has Ti, Al and N etc.Wherein, Nb and Ti are the strong carbide forming elements, separate out the big small carbide of aggegation drag when microminiaturization by crystal grain and tempering, have raising in the softening drag of high-temperature area more than 65 ℃ and the effect of hot strength.But, when Nb and Ti are too much, form the thick carbide that is difficult to solid solution, cause toughness to reduce, thereby their content separately must be below 0.5%.
In addition, the N solid solution is used to make the crystal grain microminiaturization in matrix and carbide, improves toughness.And N is an austenite former, even under the situation of low C, residual ferrite in the time of also preventing to quench heating is the alloy composition composition with excellent toughness.But N has the content limit in the alloy ingredient scope of Thermal tool steels such as Cr, thereby N must be below 0.20 quality %.
Inclusion
According to the purity of JISG0555 regulation, A is that inclusion is the viscous yielding inclusion, comprises MnS and silicate etc.These A are that inclusion makes heat-resistant cracking and refractory decrease property significantly to worsen, thereby A is that inclusion must be below 0.020%, preferably 0%.B is that inclusion forms group on machine direction, arranges with discontinuous granular inclusion morphology, comprises aluminum oxide and carbonitride etc.In addition, C is that viscous yielding does not take place inclusion, is irregular dispersing morphology, comprises granular oxide and carbonitride.These B are that inclusion and C are that inclusion makes machinability worsen, thereby its content must be respectively below 0.020%, preferably 0%.And these inclusion sums d (A+B+C) must be below 0.045%.
In the present invention, dA60 * 400=0.020% is following, dB60 * 400=0.020% following, dC60 * 400=0.020% is following, d (A+B+C)=below 0.045%.
Carbide and non-metallic inclusion
Under the less situation of non-metallic inclusion, the area occupation ratio that particle diameter surpasses the carbide of 1.0 μ m and non-metallic inclusion is 0.004% when following under as-annealed condition, can improve the machinability under the as-annealed condition.In addition, the carbide that particle diameter 1.0 μ m are following and the area occupation ratio of non-metallic inclusion are 10.5% when above under as-annealed condition, can further improve its machinability.
Equally, under the less situation of non-metallic inclusion, the area occupation ratio that particle diameter surpasses the carbide of 1.0 μ m and non-metallic inclusion is 0.004% when following under the Q-tempering state, can improve refractory damage property, heat-resistant cracking and machinability simultaneously.In addition, the carbide that particle diameter 1.0 μ m are following and the area occupation ratio of non-metallic inclusion are 0.038% when above under the Q-tempering state, can further improve its refractory damage property, heat-resistant cracking and machinability.
Like this, the area occupation ratio that particle diameter surpasses the carbide of 1.0 μ m and non-metallic inclusion can alleviate the fluctuation in cutting tool life-span 0.004% when following.Large-sized carbide like this and non-metallic inclusion make that the blade generation of cutter is damaged, thereby produce fluctuation work-ing life when colliding with cutting tool.
As mentioned above, for machinability, the size of non-metallic inclusion is a problem, but, when estimating inclusion, only estimate its kind and number according in the past JISG0555 or ASTM E45-76, even when being good, can not show that inclusion is small by the result of these standard evaluations.
Carbide that particle diameter 1.0 μ m are following and non-metallic inclusion exist many more on segregation line, and the life-span of instrument is long more.The area occupation ratio of carbide and non-metallic inclusion is to be 0.038% when above more than 10.5%, under the Q-tempering state under as-annealed condition, and machinability is good.
The effect that small carbide produced that particle diameter 1.0 μ m are following is not limited only to carbide, and non-metallic inclusion also is same.In order to generate the small inclusion below the particle diameter 1.0 μ m, preferably, will add 0.0010～0.0001 quality % more than a kind respectively among Ti, Zr, Ca, Al, Si, B, O and the N, pass through Al
2O
3, generate B based nitride or B and be oxide compound, MnS and AlN etc. small, long-width ratio is the non-metallic inclusion below 1.3.
In addition, the purity of non-metallic inclusion is defined as dA60 * 400=0%, dB60 * 400=0%, dC60 * 400=0%, can significantly improves heat-resistant cracking according to the purity of JISG0555 regulation.
Below, by comparing, specifically describe the effect of embodiments of the invention with scope of the invention comparative example in addition.
The Thermal tool steel of forming shown in table 1 and the table 2 below 10kg vacuum melting stove (VIF) melting forges into 40 * 80 * 250mm size with forging apparatus with resulting ingot casting, then 830 ℃ of annealing down.The form of carbide and non-metallic inclusion and the control of quantity are by 1015～1240 ℃ of heating 1 minute to 20 hours, cold, the air cooling of stove or oil cooling are realized then.
Table 1
| ??SKD ???61 | ????C | ????Si | ???Mn | ????P | ????S | ????Cr | ????Mo | ??V | ??W | ??Co | ??Ni | ??Ti | ??Al | ??B | ??N | ??1/2W ??+Mo | |
| Routine in the past | ??① | ??0.38 | ??0.95 | ??0.38 | ??0.0020 | ?0.018 | ??4.95 | ??1.32 | ??0.53 | ?0.004 | ?0.001 | ??0.13 | ?0.003 | ?0.007 | ?0.003 | ?0.004 | ???1.32 |
| ??② | ??0.38 | ??0.95 | ??0.40 | ??0.0018 | ?0.014 | ??5.00 | ??1.33 | ??0.53 | ?0.004 | ?0.002 | ??0.13 | ?0.002 | ?0.005 | ?0.003 | ?0.003 | ???1.33 | |
| ??③ | ??0.39 | ??0.98 | ??0.40 | ??0.0015 | ?0.008 | ??5.01 | ??1.28 | ??0.54 | ?0.003 | ?0.001 | ??0.15 | ?0.003 | ?0.006 | ?0.002 | ?0.004 | ???1.28 | |
| ??④ | ??0.40 | ??0.98 | ??0.39 | ??0.0012 | ?0.009 | ??4.98 | ??1.30 | ??0.55 | ?0.002 | ?0.001 | ??0.14 | ?0.003 | ?0.006 | ?0.003 | ?0.004 | ???1.30 | |
| ??⑤ | ??0.39 | ??0.97 | ??0.38 | ??0.0008 | ?0.004 | ??4.95 | ??1.29 | ??0.54 | ?0.004 | ?0.000 | ??0.15 | ?0.001 | ?0.008 | ?0.003 | ?0.003 | ???1.29 | |
| ??⑥ | ??0.40 | ??1.00 | ??0.40 | ??0.0005 | ?0.001 | ??5.04 | ??1.27 | ??0.55 | ?0.002 | ?0.000 | ??0.15 | ?0.001 | ?0.007 | ?0.003 | ?0.002 | ???1.27 | |
| Comparative example | ??1 | ??0.20 | ??0.80 | ??0.30 | ??0.0060 | ?0.023 | ??6.50 | ??1.00 | ??0.20 | ?1.000 | ?0.000 | ??0.08 | ?0.003 | ?0.006 | ?0.003 | ?0.004 | ???1.50 |
| ??2 | ??0.64 | ??0.70 | ??0.35 | ??0.0073 | ?0.033 | ??5.80 | ??1.60 | ??2.30 | ?4.000 | ?0.002 | ??0.09 | ?0.002 | ?0.008 | ?0.001 | ?0.003 | ???3.60 | |
| ??3 | ??0.52 | ??0.50 | ??0.70 | ??0.0070 | ?0.066 | ??4.50 | ??1.00 | ??0.10 | ?1.000 | ?0.000 | ??0.05 | ?0.003 | ?0.007 | ?0.003 | ?0.004 | ???1.50 | |
| ??4 | ??0.30 | ??0.30 | ??0.65 | ??0.0100 | ?0.001 | ??4.80 | ??2.00 | ??2.30 | ?2.000 | ?0.500 | ??0.10 | ?0.003 | ?0.005 | ?0.001 | ?0.004 | ???3.00 | |
| ??5 | ??0.40 | ??0.10 | ??0.80 | ??0.0110 | ?0.150 | ??3.40 | ??4.00 | ??3.00 | ?4.000 | ?6.500 | ??0.80 | ?0.003 | ?0.006 | ?0.001 | ?0.003 | ???6.00 | |
| ??6 | ??0.10 | ??0.80 | ??1.00 | ??0.0110 | ?0.150 | ??7.00 | ??1.00 | ??3.00 | ?1.200 | ?6.500 | ??0.30 | ?0.001 | ?0.006 | ?0.003 | ?0.004 | ???1.60 |
Table 2
| ??C | ??Si | ?Mn | ????P | ????S | ????Cr | ????Mo | ??V | ??W | ??Co | ??Ni | ??Ti | ??Al | ??B | ??N | ??1/2W ???+Mo | ||
| Embodiment | ???7 | ??0.18 | ??0.67 | ??0.80 | ??0.0070 | ?0.001 | ??6.50 | ??1.20 | ??0.10 | ?2.700 | ?2.300 | ??0.50 | ?0.001 | ?0.008 | ?0.003 | ?0.003 | ???2.55 |
| ???8 | ??0.20 | ??0.60 | ??0.30 | ??0.0100 | ?0.007 | ??3.50 | ??4.00 | ??2.50 | ?3.100 | ?0.000 | ??0.10 | ?0.003 | ?0.007 | ?0.003 | ?0.004 | ???5.55 | |
| ???9 | ??0.30 | ??0.65 | ??0.95 | ??0.0200 | ?0.008 | ??6.60 | ??0.50 | ??2.50 | ?2.800 | ?1.300 | ??0.05 | ?0.001 | ?0.007 | ?0.001 | ?0.004 | ???1.90 | |
| ???10 | ??0.45 | ??0.50 | ??0.30 | ??0.0200 | ?0.009 | ??4.50 | ??3.00 | ??0.50 | ?1.700 | ?2.300 | ??0.06 | ?0.001 | ?0.005 | ?0.002 | ?0.003 | ???3.85 | |
| ???11 | ??0.52 | ??0.48 | ??0.34 | ??0.0080 | ?0.006 | ??3.20 | ??1.50 | ??0.10 | ?0.900 | ?4.000 | ??0.08 | ?0.003 | ?0.006 | ?0.003 | ?0.004 | ???1.95 | |
| ???12 | ??0.61 | ??0.40 | ??0.70 | ??0.0087 | ?0.010 | ??6.80 | ??2.30 | ??2.70 | ?0.600 | ?1.200 | ??0.10 | ?0.003 | ?0.006 | ?0.003 | ?0.004 | ???2.60 | |
| ???13 | ??0.65 | ??0.30 | ??0.32 | ??0.0100 | ?0.014 | ??5.40 | ??4.00 | ??1.80 | ?2.400 | ?0.300 | ??0.40 | ?0.002 | ?0.008 | ?0.003 | ?0.003 | ???5.20 | |
| ???14 | ??0.70 | ??0.10 | ??0.30 | ??0.0007 | ?0.012 | ??3.00 | ??6.00 | ??0.10 | ?1.800 | ?0.000 | ??0.05 | ?0.003 | ?0.007 | ?0.003 | ?0.004 | ???6.90 | |
| ???15 | ??0.35 | ??0.55 | ??0.35 | ??0.0011 | ?0.001 | ??4.60 | ??1.60 | ??0.40 | ?0.000 | ?0.000 | ??0.08 | ?0.003 | ?0.008 | ?0.003 | ?0.003 | ???1.60 | |
| ???16 | ??0.37 | ??0.60 | ??0.40 | ??0.0080 | ?0.003 | ??4.80 | ??1.70 | ??0.50 | ?0.000 | ?0.000 | ??0.13 | ?0.001 | ?0.010 | ?0.001 | ?0.004 | ???1.70 | |
| ???17 | ??0.40 | ??0.65 | ??0.45 | ??0.0070 | ?0.005 | ??5.00 | ??1.80 | ??0.60 | ?0.000 | ?0.000 | ??0.15 | ?0.002 | ?0.015 | ?0.001 | ?0.004 | ???1.80 |
In addition, the purity of the non-metallic inclusion of all melting materials all below the JISdA0.005%, d (B+C) is below 0.020%, the long-width ratio of carbide and non-metallic inclusion is 1.3～1.0.
The evaluation of material is, makes it solid solution in 30 minutes 980～1080 ℃ of heating, quenches then, and in 500～670 ℃ of heating tempering in 2 hours, this tempering process repeats 2 times.Like this, hardness being adjusted into 43+1HRC, is 50 and exponentiate, relatively its performance with the performance of SKD61 material.
1.0 the carbide that μ m is following and the mensuration of non-metallic inclusion are by following described carrying out, promptly, for annealed material, sample after the polishing is put into picric acid+3% salpeter solution to be flooded, expose metallographic structure, for the Q-tempering material, the sample after the polishing is corroded with oxalic acid, expose metallographic structure.With SEM (scanning electronic microscope) 4000 times of photograph are amplified in this metallographic structure, measure area occupation ratio and median size by image analysis.In addition, dispersity is to estimate than the distance in the big place more than 30% of area occupation ratio of non-segregation portion according to the dense degree of carbide and non-metallic inclusion.
Particle diameter surpasses the carbide of 1.0 μ m and the mensuration of non-metallic inclusion, is with the oxalic acid corrosion, carries out 1mm with 1000 times photograph then
2Image analysis in the visual field is carried out.
The measurement result of carbide and non-metallic inclusion is shown in following table 3 and table 4 and table 5 and the table 6.
Table 3
| ?SKD ??61 | Annealed material | The Q-tempering material | |||||
| Surpass 1.0 μ m | 1.0 below the μ m | Add up to | Surpass 1.0 μ m | 1.0 below the μ m | Add up to | ||
| Routine in the past | ??① | ????0.037 | ????10.5 | ??10.537 | ????0.100 | ????0.018 | ??0.057 |
| ??② | ????0.032 | ????11.0 | ??11.032 | ????0.037 | ????0.020 | ??0.047 | |
| ??③ | ????0.028 | ????11.7 | ??11.728 | ????0.032 | ????0.015 | ??0.038 | |
| ??④ | ????0.026 | ????15.0 | ??15.026 | ????0.028 | ????0.010 | ??0.040 | |
| ??⑤ | ????0.003 | ????32.0 | ??32.003 | ????0.002 | ????0.038 | ??0.413 | |
| ??⑥ | ????0.001 | ????14.0 | ??14.001 | ????0.003 | ????0.410 | ??0.118 | |
| Comparative example | ??1 | ????0.005 | ????17.0 | ??17.005 | ????0.006 | ????0.222 | ??0.057 |
| ??2 | ????0.012 | ????21.0 | ??21.012 | ????0.008 | ????0.800 | ??0.808 | |
| ??3 | ????0.009 | ????27.4 | ??27.409 | ????0.004 | ????1.200 | ??1.204 | |
| ??4 | ????0.006 | ????23.0 | ??23.006 | ????0.003 | ????0.400 | ??0.403 | |
| ??5 | ????0.007 | ????22.0 | ??22.007 | ????0.001 | ????0.100 | ??0.101 | |
| ??6 | ????0.003 | ????10.2 | ??10.203 | ????0.01 | ????0.035 | ??0.036 | |
Table 4
| Annealed material | The Q-tempering material | ||||||
| Surpass 1.0 μ m | 1.0 below the μ m | Add up to | Surpass 1.0 μ m | 1.0 below the μ m | Add up to | ||
| Embodiment | ??7 | ????0.004 | ?????9.5 | ??9.504 | ????0.002 | ????0.032 | ??0.032 |
| ??8 | ????0.002 | ?????8.4 | ??8.402 | ????0.002 | ????0.028 | ??0.030 | |
| ??9 | ????0.002 | ?????10.4 | ?10.402 | ????0.001 | ????0.012 | ??0.013 | |
| ??10 | ????0.003 | ?????8.7 | ??8.703 | ????0.001 | ????0.008 | ??0.009 | |
| ??11 | ????0.001 | ?????12.0 | ?12.001 | ????0.003 | ????0.007 | ??0.010 | |
| ??12 | ????0.004 | ?????13.2 | ?13.204 | ????0.004 | ????0.042 | ??0.046 | |
| ??13 | ????0.001 | ?????15.2 | ?15.201 | ????0.002 | ????0.046 | ??0.048 | |
| ??14 | ????0.001 | ?????13.5 | ?13.501 | ????0.003 | ????0.042 | ??0.045 | |
| ??15 | ????0.000 | ?????10.5 | ?10.500 | ????0.000 | ????0.042 | ??0.042 | |
| ??16 | ????0.000 | ?????12.3 | ?12.300 | ????0.000 | ????0.054 | ??0.054 | |
| ??17 | ????0.000 | ?????10.5 | ?10.500 | ????0.000 | ????0.048 | ??0.048 | |
Table 5
| ?SKD ?? 61 | Non-metallic inclusion | ||||
| ????dA | ????dB | ????dC | Add up to | ||
| Routine in the past | ??① | ????0.030 | ????0.015 | ????0.012 | ????0.057 |
| ??② | ????0.028 | ????0.012 | ????0.007 | ????0.047 | |
| ??③ | ????0.018 | ????0.022 | ????0.008 | ????0.048 | |
| ??④ | ????0.022 | ????0.027 | ????0.021 | ????0.070 | |
| ??⑤ | ????0.018 | ????0.008 | ????0.008 | ????0.034 | |
| ??⑥ | ????0.015 | ????0.004 | ????0.003 | ????0.022 | |
| Comparative example | ??1 | ????0.043 | ????0.023 | ????0.310 | ????0.376 |
| ??2 | ????0.018 | ????0.023 | ????0.024 | ????0.065 | |
| ??3 | ????0.018 | ????0.016 | ????0.007 | ????0.041 | |
| ??4 | ????0.017 | ????0.010 | ????0.009 | ????0.036 | |
| ??5 | ????0.012 | ????0.012 | ????0.010 | ????0.034 | |
| ??6 | ????0.007 | ????0.009 | ????0.002 | ????0.018 | |
Table 6
| Non-metallic inclusion | |||||
| ????dA | ????dB | ????dC | Add up to | ||
| Embodiment | ????7 | ????0.005 | ????0.012 | ????0.004 | ????0.021 |
| ????8 | ????0.020 | ????0.007 | ????0.009 | ????0.036 | |
| ????9 | ????0.012 | ????0.007 | ????0.012 | ????0.031 | |
| ???10 | ????0.018 | ????0.009 | ????0.018 | ????0.045 | |
| ???11 | ????0.007 | ????0.002 | ????0.007 | ????0.016 | |
| ???12 | ????0.009 | ????0.004 | ????0.009 | ????0.022 | |
| ???13 | ????0.002 | ????0.020 | ????0.012 | ????0.034 | |
| ???14 | ????0.004 | ????0.004 | ????0.020 | ????0.028 | |
| ???15 | ????0.000 | ????0.000 | ????0.000 | ????0.000 | |
| ???16 | ????0.000 | ????0.000 | ????0.000 | ????0.000 | |
| ???17 | ????0.000 | ????0.000 | ????0.000 | ????0.000 | |
The machinability evaluation of annealed material, being to use the slotting cutter of the high speed steel of diameter 10mm is that the condition of 10 * 1mm is cut and carried out according to rotating speed 520rpm, speed of feed 74mm/ minute, depth of cut during machining, obtain the life-span when losing, with in the past the example the SKD life-span 1. as 100, use exponential representation.Described 10 * 1mm represents, test materials contacts 10mm with slotting cutter on the length direction of slotting cutter, slotting cutter axially on contact 1mm, machining is carried out in the zone of feed 10 * 1mm on the section of test materials, therefore, on the side of test materials, form the recess of wide 1mm, dark 10mm.
In addition, the machinability evaluation of Q-tempering material is, the steel modifier treatment is become 48HRC, use applies the slotting cutter (MMC コ ベ Le コ company makes VA-2SS diameter 6mm) of the two-edged lobe of TiAlN on the powder cutter head rapid steel of diameter 10mm, according to rotating speed 1062rpm, speed of feed 212mm/ minute, depth of cut during machining was that the condition of 9 * 0.6mm is cut above-mentioned steel, the life-span when obtaining this slotting cutter and beginning melting loss.With in the past the example the SKD61 life-span 1. as 100, use exponential representation.
Hot cracking test is, heats the test materials of diameter 30mm, length 50mm by the high-frequency induction heating mode, waters when surface temperature reaches 650 ℃, is cooled to 50 ℃, carries out so repeatedly 1000 times, measures the mean length (μ m) of crackle.Then, with in the past the example the SKD61 life-span 1. as 100, use exponential representation.
Normally used aluminium alloy (JIS ADC12) in die casting is used in the evaluation of melting loss.This JIS ADC12 is the aluminium alloy that the die cast product of automobile (wheel box class) and household appliances uses, and it consists of Al-0.43%Zn-0.20%Mn-10.85%Si-2.00%Cu-1.01%Fe-0.24%Mg.This aluminium alloy is put into container internal heating to 650 ℃ make it fusing, the rotating speed rotation of this liquation with 500rpm put in the test piece of the embodiment of diameter 5mm, length 30mm and comparative example, stir the ADC12 liquation, kept this state 20 minutes, take out above-mentioned test piece then, remove attached to the aluminium alloy in the test piece waste (g) of the weight difference mensuration test piece before using according to test piece and after using with sodium hydroxide.With in the past the example the SKD61 life-span 1. as 100, use exponential representation.
The evaluation result of these machinabilities, refractory damage property and heat-resistant cracking is shown in the following table 7 and table 8.
Table 7
| ?SKD ??61 | Machinability | Refractory damage property | Heat-resistant cracking | ||
| Annealed material (10HRC) | Quenched materials (48HRC) | ||||
| Routine in the past | ??① | ????100 | ????100 | ????100 | ????100 |
| ??② | ????102 | ????104 | ????100 | ????102 | |
| ??③ | ????105 | ????103 | ????102 | ????104 | |
| ??④ | ????103 | ????107 | ????101 | ????106 | |
| ??⑤ | ????123 | ????102 | ????98 | ????98 | |
| ??⑥ | ????120 | ????104 | ????104 | ????99 | |
| Comparative example | ??1 | ????100 | ????100 | ????100 | ????95 |
| ??2 | ????97 | ????98 | ????102 | ????101 | |
| ??3 | ????102 | ????99 | ????98 | ????104 | |
| ??4 | ????103 | ????102 | ????99 | ????99 | |
| ??5 | ????100 | ????98 | ????97 | ????101 | |
| ??6 | ????180 | ????186 | ????217 | ????180 | |
Table 8
| Machinability | Refractory damage property | Heat-resistant cracking | |||
| Annealed material (10HRC) | Quenched materials (48HRC) | ||||
| Embodiment | ??7 | ????180 | ????190 | ????210 | ????184 |
| ??8 | ????182 | ????184 | ????207 | ????191 | |
| ??9 | ????180 | ????180 | ????214 | ????197 | |
| ??10 | ????183 | ????181 | ????218 | ????194 | |
| ??11 | ????218 | ????180 | ????213 | ????184 | |
| ??12 | ????223 | ????228 | ????222 | ????243 | |
| ??13 | ????220 | ????232 | ????223 | ????254 | |
| ??14 | ????216 | ????251 | ????200 | ????280 | |
| ??15 | ????304 | ????332 | ????220 | ????333 | |
| ??16 | ????332 | ????301 | ????260 | ????345 | |
| ??17 | ????340 | ????351 | ????320 | ????380 | |
In the past Li SKD 1.～6., though the steel scrap fit rate that has cooperated as raw material when having improved melting has improved purity, heat-resistant cracking, refractory decrease property and machinability does not improve.In addition, though forming, comparative example 1～6 composition falls in the scope of claim defined of the present invention, if do not reach below 0.004% but the particle diameter of annealed material surpasses carbide and the inclusion of 1.0 μ m, then can't improve heat-resistant cracking, refractory damage property and machinability.
Relative therewith, shown in embodiment 7～17, when satisfying claim 1 of the present invention, the machinability of its annealed material and Q-tempering material, refractory decrease property and heat-resistant cracking and 1. compare with the SKD61 that possesses inclusion and improve more than 1.8 times.
In addition, shown in embodiment 11～17, if satisfy claim 2 of the present invention, then 1. the machinability of its annealed material, refractory damage property are compared with the SKD61 that possesses inclusion with heat-resistant cracking and are improved more than 2.0 times.But, can't obtain the effect of improving of the machinability of Q-tempering material and heat-resistant cracking.
In addition, when satisfying claim 3 of the present invention and 4, shown in embodiment 12～17,1. the machinability of its annealed material and Q-tempering material, refractory damage property are compared with the SKD61 that possesses inclusion with heat-resistant cracking and are improved more than 2.0 times.
When inclusion was 0%, shown in embodiment 15～17,1. the machinability of its annealed material and Q-tempering material, refractory damage property were compared with the SKD61 that possesses inclusion with heat-resistant cracking and are improved more than 3.2 times.
As mentioned above, adopt the present invention can significantly improve machinability, refractory damage property and the heat-resistant cracking of Thermal tool steel.
Claims (6)
1. Thermal tool steel, it is characterized in that, contain C:0.10～0.70 quality %, Si:0.10～0.80 quality %, Mn:0.30～1.00 quality %, P:0.007～0.020 quality %, Cr:3.00～7.00 quality %, W and Mo independent or compound (1/2W+Mo): 0.20～12.00 quality %, V:0.10～3.00 quality %, Ni:0.05～0.80 quality %, below the S:0.150 quality %, surplus is made of Fe and unavoidable impurities basically, the purity of non-metallic inclusion (JISG055) is, dA60 * 400 are below 0.020%, dB60 * 400 are below 0.020%, dC60 * 400 are below 0.020%, d (A+B+C) is below 0.045%, simultaneously, when annealing, particle diameter surpasses the carbide of 1.0 μ m and the area occupation ratio of non-metallic inclusion is below 0.004%.
2. the described Thermal tool steel of claim 1 is characterized in that, also contains below the Co:6.50 quality %.
3. claim 1 or 2 described Thermal tool steels is characterized in that, the carbide during annealing below the particle diameter 1.0 μ m and the area occupation ratio of non-metallic inclusion are more than 10.5%.
4. each described Thermal tool steel in the claim 1～3 is characterized in that, during Q-tempering, particle diameter surpasses the carbide of 1.0 μ m and the area occupation ratio of non-metallic inclusion is below 0.004%.
5. each described Thermal tool steel in the claim 1～4 is characterized in that, during Q-tempering, the carbide that particle diameter 1.0 μ m are following and the area occupation ratio of non-metallic inclusion are more than 0.038%.
6. Thermal tool steel, it is characterized in that, contain C:0.35～0.40 quality %, Si:0.55～0.65 quality %, Mn:0.35～0.45 quality %, P:0.007～0.010 quality %, Cr:4.60～5.00 quality %, W and Mo independent or compound (1/2W+Mo): 1.60～1.80 quality %, V:0.40～0.60 quality %, Ni:0.08～0.15 quality %, below the S:0.005 quality %, surplus is made of Fe and unavoidable impurities basically, the purity of non-metallic inclusion (JISG055) is, dA60 * 400 are below 0.0%, dB60 * 400 are below 0.0%, dC60 * 400 are below 0.0%, d (A+B+C) is 0.0%, simultaneously, when annealing, particle diameter surpasses the carbide of 1.0 μ m and the area occupation ratio of non-metallic inclusion is below 0.004%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002028298A JP3602102B2 (en) | 2002-02-05 | 2002-02-05 | Hot tool steel |
| JP028298/2002 | 2002-02-05 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1436874A true CN1436874A (en) | 2003-08-20 |
| CN1173067C CN1173067C (en) | 2004-10-27 |
Family
ID=27654649
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB021567182A Expired - Lifetime CN1173067C (en) | 2002-02-05 | 2002-12-12 | Thermal tool steel |
Country Status (4)
| Country | Link |
|---|---|
| JP (1) | JP3602102B2 (en) |
| KR (1) | KR100497446B1 (en) |
| CN (1) | CN1173067C (en) |
| TW (1) | TWI280284B (en) |
Cited By (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100342052C (en) * | 2004-01-20 | 2007-10-10 | 吉林大学 | Hot work die steel |
| CN101542004B (en) * | 2007-04-18 | 2011-02-16 | 新日本制铁株式会社 | Hot-worked steel material having excellent machinability and impact value |
| CN101316943B (en) * | 2005-11-29 | 2012-07-04 | 奥贝特迪瓦尔公司 | Steel for hot tooling, and part produced from said steel, method for the production thereof, and uses of the same |
| CN101634002B (en) * | 2008-07-23 | 2013-07-31 | 大同特殊钢株式会社 | Free-cutting alloy tool steel |
| CN103774062A (en) * | 2014-01-09 | 2014-05-07 | 马鞍山市恒毅机械制造有限公司 | Cutter alloy steel material for machining titanium alloy and preparation method thereof |
| CN105026595A (en) * | 2013-02-28 | 2015-11-04 | 日立金属株式会社 | Die steel and method for producing same |
| CN105088051A (en) * | 2015-08-20 | 2015-11-25 | 无锡贺邦金属制品有限公司 | Hot work die steel |
| CN105579604A (en) * | 2013-09-27 | 2016-05-11 | 日立金属株式会社 | High-speed-tool steel and method for producing same |
| CN107109555A (en) * | 2014-11-11 | 2017-08-29 | 日本高周波钢业株式会社 | High temperature tool steel |
| CN108385025A (en) * | 2018-04-09 | 2018-08-10 | 武汉科技大学 | A kind of Slab Deburring Machine blade and its manufacturing method |
| CN109295393A (en) * | 2018-12-13 | 2019-02-01 | 天津钢研海德科技有限公司 | The plastic die steel and preparation method thereof of novel high tenacity height polishing highly corrosion resistant |
| CN109790604A (en) * | 2016-09-30 | 2019-05-21 | 新日铁住金株式会社 | Cold Forging Steel and its manufacturing method |
| CN109972059A (en) * | 2017-12-27 | 2019-07-05 | 天工爱和特钢有限公司 | A kind of high-strength die steel |
| CN110923580A (en) * | 2019-11-19 | 2020-03-27 | 马鞍山钢铁股份有限公司 | Heat-resistant 12.9-grade steel for fasteners for rail transit and heat treatment process thereof |
| CN112601832A (en) * | 2018-10-05 | 2021-04-02 | 日立金属株式会社 | Hot-work tool steel and hot-work tool |
| CN113604733A (en) * | 2021-07-05 | 2021-11-05 | 昆山东大特钢制品有限公司 | High-temperature-resistant and high-toughness high-end hot-work die steel and production process thereof |
| CN114058957A (en) * | 2021-11-04 | 2022-02-18 | 佛山顶锋日嘉模具有限公司 | Alloy steel and production process thereof |
| CN116457487A (en) * | 2020-11-05 | 2023-07-18 | 尤迪霍尔姆斯有限责任公司 | Maraging steel |
Families Citing this family (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3946684B2 (en) * | 2003-10-02 | 2007-07-18 | 日本高周波鋼業株式会社 | Hot work tool steel |
| CN1878881A (en) * | 2003-12-19 | 2006-12-13 | 大同特殊钢株式会社 | Hot work tool steel and mold member excellent in resistance to melting |
| JP2005206913A (en) * | 2004-01-26 | 2005-08-04 | Daido Steel Co Ltd | Alloy tool steel |
| JP5146063B2 (en) * | 2007-04-12 | 2013-02-20 | 新日鐵住金株式会社 | High strength steel with excellent internal fatigue damage resistance and method for producing the same |
| US8012272B2 (en) | 2007-10-31 | 2011-09-06 | Daido Tokushuko Kabushiki Kaisha | Tool steels and manufacturing method thereof |
| JP5942119B2 (en) * | 2011-01-31 | 2016-06-29 | 栃木県 | Melting resistant casting, method for producing the same and molten metal contact member |
| JP5942118B2 (en) * | 2011-01-31 | 2016-06-29 | 栃木県 | Melting resistant casting, method for producing the same, and molten metal contact member |
| CN103403209B (en) * | 2011-03-03 | 2016-01-13 | 日立金属株式会社 | The hot work tool steel of tenacity excellent and manufacture method thereof |
| JP6366326B2 (en) * | 2014-03-31 | 2018-08-01 | 山陽特殊製鋼株式会社 | High toughness hot work tool steel and manufacturing method thereof |
| WO2015182586A1 (en) * | 2014-05-28 | 2015-12-03 | 日立金属株式会社 | Hot work tool material and method for manufacturing hot work tool |
| KR101751530B1 (en) | 2015-12-28 | 2017-06-27 | 주식회사 포스코 | Steel sheet for tool and method of manufacturing for the same |
| US10988823B2 (en) | 2017-03-28 | 2021-04-27 | Daido Steel Co., Ltd. | Annealed steel material and method for manufacturing the same |
| CN110184540A (en) * | 2019-06-06 | 2019-08-30 | 南通聚星铸锻有限公司 | A kind of ESR ingot and its smelting process |
| SE544123C2 (en) * | 2020-06-12 | 2022-01-04 | Uddeholms Ab | Hot work tool steel |
| JP2023122766A (en) * | 2022-02-24 | 2023-09-05 | 大同特殊鋼株式会社 | Mold steel and metal mold |
| JP2024060363A (en) * | 2022-10-19 | 2024-05-02 | 大同特殊鋼株式会社 | Steel and molds |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100206354B1 (en) * | 1996-06-05 | 1999-07-01 | 전선기 | Manufacturing method of forging die and tool steel and the same product |
-
2002
- 2002-02-05 JP JP2002028298A patent/JP3602102B2/en not_active Expired - Fee Related
- 2002-12-06 TW TW091135361A patent/TWI280284B/en not_active IP Right Cessation
- 2002-12-09 KR KR10-2002-0077735A patent/KR100497446B1/en active IP Right Grant
- 2002-12-12 CN CNB021567182A patent/CN1173067C/en not_active Expired - Lifetime
Cited By (24)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100342052C (en) * | 2004-01-20 | 2007-10-10 | 吉林大学 | Hot work die steel |
| CN101316943B (en) * | 2005-11-29 | 2012-07-04 | 奥贝特迪瓦尔公司 | Steel for hot tooling, and part produced from said steel, method for the production thereof, and uses of the same |
| CN101542004B (en) * | 2007-04-18 | 2011-02-16 | 新日本制铁株式会社 | Hot-worked steel material having excellent machinability and impact value |
| CN101634002B (en) * | 2008-07-23 | 2013-07-31 | 大同特殊钢株式会社 | Free-cutting alloy tool steel |
| US10196719B2 (en) | 2013-02-28 | 2019-02-05 | Hitachi Metals, Ltd. | Die steel and method for producing same |
| CN105026595A (en) * | 2013-02-28 | 2015-11-04 | 日立金属株式会社 | Die steel and method for producing same |
| CN108624826A (en) * | 2013-02-28 | 2018-10-09 | 日立金属株式会社 | Die steel and its manufacturing method |
| CN105579604A (en) * | 2013-09-27 | 2016-05-11 | 日立金属株式会社 | High-speed-tool steel and method for producing same |
| CN103774062A (en) * | 2014-01-09 | 2014-05-07 | 马鞍山市恒毅机械制造有限公司 | Cutter alloy steel material for machining titanium alloy and preparation method thereof |
| CN107109555A (en) * | 2014-11-11 | 2017-08-29 | 日本高周波钢业株式会社 | High temperature tool steel |
| CN107109555B (en) * | 2014-11-11 | 2019-06-14 | 日本高周波钢业株式会社 | High temperature tool steel |
| CN105088051A (en) * | 2015-08-20 | 2015-11-25 | 无锡贺邦金属制品有限公司 | Hot work die steel |
| CN109790604A (en) * | 2016-09-30 | 2019-05-21 | 新日铁住金株式会社 | Cold Forging Steel and its manufacturing method |
| CN109790604B (en) * | 2016-09-30 | 2021-09-10 | 日本制铁株式会社 | Cold forging steel and method for producing same |
| CN109972059A (en) * | 2017-12-27 | 2019-07-05 | 天工爱和特钢有限公司 | A kind of high-strength die steel |
| CN108385025A (en) * | 2018-04-09 | 2018-08-10 | 武汉科技大学 | A kind of Slab Deburring Machine blade and its manufacturing method |
| CN112601832A (en) * | 2018-10-05 | 2021-04-02 | 日立金属株式会社 | Hot-work tool steel and hot-work tool |
| CN114000059A (en) * | 2018-10-05 | 2022-02-01 | 日立金属株式会社 | Hot-work tool steel and hot-work tool |
| CN112601832B (en) * | 2018-10-05 | 2022-03-01 | 日立金属株式会社 | Hot-work tool steel and hot-work tool |
| CN109295393A (en) * | 2018-12-13 | 2019-02-01 | 天津钢研海德科技有限公司 | The plastic die steel and preparation method thereof of novel high tenacity height polishing highly corrosion resistant |
| CN110923580A (en) * | 2019-11-19 | 2020-03-27 | 马鞍山钢铁股份有限公司 | Heat-resistant 12.9-grade steel for fasteners for rail transit and heat treatment process thereof |
| CN116457487A (en) * | 2020-11-05 | 2023-07-18 | 尤迪霍尔姆斯有限责任公司 | Maraging steel |
| CN113604733A (en) * | 2021-07-05 | 2021-11-05 | 昆山东大特钢制品有限公司 | High-temperature-resistant and high-toughness high-end hot-work die steel and production process thereof |
| CN114058957A (en) * | 2021-11-04 | 2022-02-18 | 佛山顶锋日嘉模具有限公司 | Alloy steel and production process thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20030066305A (en) | 2003-08-09 |
| JP3602102B2 (en) | 2004-12-15 |
| TWI280284B (en) | 2007-05-01 |
| KR100497446B1 (en) | 2005-06-28 |
| CN1173067C (en) | 2004-10-27 |
| TW200302873A (en) | 2003-08-16 |
| JP2003226939A (en) | 2003-08-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1173067C (en) | Thermal tool steel | |
| CN1511969A (en) | Alloy tool steel and its producing method and mold using it | |
| CN1696326A (en) | Cold work tool steel | |
| CN1847439A (en) | Guide and guard roller for guiding steel billet in high speed wire rolling machine and its making process | |
| CN1570181A (en) | Low alloy high speed tool steel having constant toughness | |
| TW201713785A (en) | Steel for mold and mold | |
| CN1445379A (en) | Hot-working tool steel with good machine work performance and preparation method therefor | |
| JP2020070457A (en) | Hot work tool steel having excellent thermal conductivity | |
| JP2021017623A (en) | Tool steel for hot work, excellent in thermal conductivity | |
| JP4123618B2 (en) | Hot work tool steel with excellent high temperature strength and toughness | |
| JP3613395B2 (en) | Hot work tool steel | |
| CN1180117C (en) | Novel casting and hot work tool steel | |
| CN1226441C (en) | Reinforced durable tool steel method for the production thereof method for producing parts made of said steel and parts thus obtained | |
| JP2005336553A (en) | Hot tool steel | |
| JP3616204B2 (en) | Cold tool steel suitable for surface treatment, its mold and tool | |
| JP6772915B2 (en) | Cold tool steel | |
| JP3920656B2 (en) | High rigidity aluminum alloy containing boron | |
| WO2021095831A1 (en) | Hot-work tool steel having exceptional high-temperature strength and toughness | |
| CN1307319C (en) | Steel material for mechanical structure excellent in suitability for rolling, quenching crack resistance, and torsional property and drive shaft | |
| CN106282782B (en) | High alloy hot-puncturing process comes directly towards | |
| JP2009235562A (en) | Steel for cold press die excellent in machinability, heat treatment dimensional change characteristic and impact characteristic, and press die | |
| TWI647318B (en) | Steel for cold working tool | |
| JP4487749B2 (en) | Constant velocity joint inner ring and manufacturing method thereof | |
| TWI844281B (en) | Steel for a mold and mold | |
| JP2001234278A (en) | Cold tool steel excellent in machinability |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CX01 | Expiry of patent term |
Granted publication date: 20041027 |
|
| CX01 | Expiry of patent term |