Steel for mold, and mold

Abstract

The present invention relates to a steel for a mold, having a composition containing, on a % by mass basis, 0.25%<C<0.38%, 0.01%<Si<0.30%, 0.92%<Mn<1.80%, 0.8%<Cr<2.2%, 0.8%<Mo<1.4%, and 0.25%<V<0.58%, with the balance being Fe and inevitable impurities, and a mold manufactured by additive manufacturing by using the steel for a mold.

Claims

1. A steel for a mold, having a composition comprising, on a % by mass basis: 0.28%C<0.38%, 0.01%<Si<0.30%, 0.92%<Mn1.41%, 0.8%<Cr1.91%, 0.8%<Mo<1.4%, and 0.31%V<0.58%, with the balance being Fe and inevitable impurities, having a coefficient of thermal conductivity at 25 C., evaluated by a laser flash method, of 28 W/m/K or higher, and being used as a material for manufacturing a mold by additive manufacturing.

2. The steel for a mold according to claim 1, further comprising, on a % by mass basis: 0.1%<Al<1.2%.

3. The steel for a mold according to claim 1, further comprising, on a % by mass basis, at least either of the following: 0.30%<Ni3.5%, and 0.30%<Cu1.5%.

4. The steel for a mold according to claim 1, further comprising, on a % by mass basis: 0.0001%<B0.0050%.

5. The steel for a mold according to claim 1, further comprising, on a % by mass basis, at least one of the following: 0.003%<S0.250%, 0.0005%<Ca0.2000%, 0.03%<Se0.50%, 0.005%<Te0.100%, 0.01%<Bi0.50%, and 0.03%<Pb0.50%.

6. The steel for a mold according to claim 1, further comprising, on a % by mass basis, at least one of the following: 0.004%<Nb0.100%, 0.004%<Ta0.100%, 0.004%<Ti0.100%, and 0.004%<Zr0.100%.

7. The steel for a mold according to claim 1, further comprising, on a % by mass basis, at least either of the following: 0.10%<W4.00%, and 0.10%<Co3.00%.

8. The steel for a mold according to claim 1, wherein the material is a powder or plates.

9. A mold manufactured by additive manufacturing by using the steel for a mold described in claim 1.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a cross-sectional view of a die casting mold as one embodiment of the present invention, the mold having a spool core.

(2) FIG. 2 is a view showing the worn state of a spool core.

DETAILED DESCRIPTION OF THE INVENTION

(3) Hereinafter, a steel for a mold according to the present invention will be described in detail. The steel for a mold according to the embodiment of the present invention contains elements described below as essential elements and the balance is formed of Fe and inevitable impurities. Reasons for limiting the content of each chemical component in the present invention are explained below. The values of the content of each chemical component are given on a % by mass basis.

(4) 0.25%<C<0.38%

(5) In the case where 0.25%<C is satisfied, a mold produced by machining a material obtained by working an ingot can achieve, through a heat treatment, a hardness of 30-57 HRC, which is required of molds. A mold in the state of being as-produced by additive manufacturing also has a hardness of 30-57 HRC. Furthermore, also in the case where the mold obtained by additive manufacturing is heat-treated, a hardness of 30-57 HRC is achieved. In the case of C0.25%, in the mold produced by any production processes, hardness is insufficient. On the other hand, in the case of 0.38%C, the coefficient of thermal conductivity decreases.

(6) 0.01%<Si<0.30%

(7) In the case of Si0.01%, machinability is deteriorated considerably. On the other hand, in case of 0.30%Si, the coefficient of thermal conductivity decreases considerably.

(8) 0.92%<Mn<1.80%

(9) In the case of Mn0.92%, hardenability is insufficient when a mold produced by machining a material obtained by working an ingot is quenched or when a mold produced by additive manufacturing is quenched. On the other hand, the coefficient of thermal conductivity decreases in the case of 1.80%Mn. In addition, in the case of 1.80%Mn, temper embrittlement occurs when the content of P is high. A more preferred range is 0.92%<Mn<1.50%.

(10) 0.8%<Cr<2.2%

(11) In the case of Cr0.8%, weatherability is insufficient. Furthermore, in the case of Cr0.8%, the steel has a blue shortness characteristic and ductility at 200 C. to 350 C. decreases. In addition, in the case of Cr0.8%, hardenability is insufficient when a mold produced by machining a material obtained by working an ingot is quenched or when a mold produced by additive manufacturing is quenched. On the other hand, the coefficient of thermal conductivity decreases in the case of 2.2%Cr.

(12) 0.8%<Mo<1.4%

(13) In the case of Mo0.8%, it is difficult to ensure hardness by secondary hardening when a mold produced by machining a material obtained by working an ingot is quenched and tempered or when a mold produced by additive manufacturing is tempered (either after or without quenching), and high-temperature strength is also insufficient. On the other hand, in the case of 1.4%Mo, fracture toughness value decrease considerably.

(14) 0.25%<V<0.58%

(15) In the case of V0.25%, coarsening of austenite crystal grains is problematic when a mold produced by machining a material obtained by working an ingot is quenched or when a mold produced by additive manufacturing is quenched. In addition, in the case of V0.25%, it is difficult to ensure hardness by secondary hardening when a mold produced by machining a material obtained by working an ingot is quenched and tempered or when a mold produced by additive manufacturing is tempered (either after or without quenching), and high-temperature strength is also insufficient. On the other hand, in the case of 0.58%V, those effects tend not to be enhanced anymore and the cost increases.

(16) In addition, in the case of 0.58%V, there is a heightened possibility that in the case where a material for a mold is produced by an ordinary process (including melting, refining, casting, and hot working), coarse VC grains might crystallize out in a larger amount in the ingot during solidification in the casting and serve as starting points for mold fracture.

(17) In the steel of the present invention, the following components are usually contained as unavoidable impurities in the following amounts.

(18) 0N0.05%

(19) 0P0.05%

(20) 0S0.003%

(21) 0Cu0.30%

(22) 0Ni0.30%

(23) 0Al0.10%

(24) 0W0.10%

(25) 0O0.01%

(26) 0Co0.10%

(27) 0Nb0.004%

(28) 0Ta0.004%

(29) 0Ti0.004%

(30) 0Zr0.004%

(31) 0B0.0001%

(32) 0Ca0.0005%

(33) 0Se0.03%

(34) 0Te0.005%

(35) 0Bi0.01%

(36) 0Pb0.03%

(37) 0Mg0.02%

(38) The steel for a mold according to the present invention may optionally contain one or more kinds of elements selected from the elements described below in addition to the above-described essential elements. That is, the steel for a mold according to the present invention may consist only of, on a % by mass basis: 0.25<C<0.38, 0.01<Si<0.30, 0.92<Mn<1.80, 0.8<Cr<2.2, 0.8<Mo<1.4, and 0.25<V<0.58, with the balance being Fe and inevitable impurities, but it may optionally contain one or more kinds of elements selected from the elements with its contents as described below.

(39) 0.1<Al<1.2%

(40) There are cases where the steel of the present invention is subjected to quenching after mold fabrication by additive manufacturing. It is possible to incorporate Al in an amount of 0.1<Al<1.2% by mass in order to inhibit the coarsening of austenite crystal grains during the quenching.

(41) Al combines with N to form AlN and produces the effect of inhibiting the movement of austenite crystal grain boundaries (i.e., growth of the grains).

(42) Since Al forms the nitride in the steel to contribute to precipitation strengthening, Al further has the function of enabling a nitrided steel material to have a heightened surface hardness. For a mold (including components that constitute some of the mold) to be nitrided in order to impart higher wear resistance thereto, use of the steel material containing Al is effective.

(43) 0.30<Ni3.5%, and 0.30<Cu1.5%

(44) In recent years, the size of molds has tended to increase due to an increase in the size of mold components and integration thereof. Large molds are difficult to cool. Because of this, in the cases where a large mold made of a steel material having poor hardenability is quenched, precipitation of ferrite, pearlite or coarse bainite occurs during the quenching to deteriorate various properties. The possibility of this problem may be eliminated by selectively adding Cu and/or Ni to enhance hardenability. Specifically, the problem may be overcome by incorporating at least either of the following;

(45) 0.30<Ni3.5%, and

(46) 0.30<Cu1.5%.

(47) Ni further has the effect of heightening the hardness by combining with Al to precipitate an intermetallic compound. Cu further has the effect of heightening the hardness through age precipitation. Preferred ranges are as follows:

(48) 0.50Ni3.0%, and

(49) 0.50Cu1.2%

(50) Each element, when contained in an amount exceeding the given value, may segregate considerably, resulting in a decrease in suitability for mirror polishing.

(51) 0.0001<B0.0050% Addition of B is also effective as an expedient for improving hardenability.

(52) Specifically, B may be incorporated according to need in the following amount:

(53) 0.0001<B0.0050%

(54) Upon formation of BN, the B comes not to show the effect of improving hardenability. It is therefore necessary to cause the B in the steel to be present alone. Specifically, use may be made of a method in which an element having a higher affinity for N than B is used to form a nitride and thereby preventing the B from combining with the N. Examples of such an element include Nb, Ta, Ti, and Zr. Although these elements have the effect of fixing N even when present in impurity-level amounts, there are cases where addition of these elements in amounts within the ranges which will be described later is desirable depending on the content of N.

(55) 0.003<S0.250%, 0.0005<Ca0.2000%, 0.03<Se0.50%, 0.005<Te0.100%, 0.01<Bi0.50%, and 0.03<Pb0.50%

(56) Since the steel of the present invention has a low Si content, this steel shows slightly poor machinability. An expedient usable for improving the machinability may be to selectively add S, Ca, Se, Te, Bi, and Pb. Specifically, at least one of the following elements may be added:

(57) 0.003<S0.250%,

(58) 0.0005<Ca0.2000%,

(59) 0.03<Se0.50%,

(60) 0.005<Te0.100%,

(61) 0.01<Bi0.50%, and

(62) 0.03<Pb0.50%.

(63) Addition of each of these elements in an amount exceeding the given value results in no further improvement in machinability, a deterioration in hot workability, and decreases in impact value and suitability for mirror polishing.

(64) 0.004<Nb0.100%, 0.004<Ta0.100%, 0.004<Ti0.100%, and 0.004<Zr0.100%

(65) In the case where an unexpected equipment trouble or the like occurs to result in an elevated heating temperature for quenching or in a prolonged heating period for quenching, there is a fear about deteriorations in various properties due to the coarsening of crystal grains. In preparation for such cases, use may be made of a method in which Nb, Ta, Ti, and Zr are selectively added and the coarsening of austenite crystal grains is inhibited by the action of fine precipitates formed by these elements. Specifically, at least one of the following elements may be incorporated:

(66) 0.004<Nb0.100%,

(67) 0.004<Ta0.100%,

(68) 0.004<Ti0.100%, and

(69) 0.004<Zr0.100%.

(70) Each of these elements, when added in an amount exceeding the given value, yields carbides, nitrides, and oxides in an excess amount, resulting in decreases in impact value and suitability for mirror polishing.

(71) 0.10<W4.00%, and 0.10<Co3.00%

(72) Although to increase the content of C is effective in enhancing strength, an excessive increase in C content results in deteriorations in property (impact value and mechanical fatigue property) due to an increase in carbide amount. For enhancing strength without arousing such a trouble, use may be made of a method in which W and Co are selectively added.

(73) W heightens the strength by forming a fine precipitate of a carbide. Co heightens the strength by forming a solid solution in the base material and, simultaneously therewith, contributes to precipitation hardening through a change into the form of carbide. Specifically, at least either of the following may be incorporated:

(74) 0.10<W4.00% and

(75) 0.10<Co3.00%.

(76) Addition of either element in an amount exceeding the given value results in no further property improvement and in a considerable increase in cost. Preferred ranges are as follows:

(77) 0.30W3.00% and

(78) 0.30Co2.00%.

EXAMPLES

(79) Examples of the present invention are described below in detail.

(80) A powder of each of seventeen types of steels respectively having the chemical compositions shown in Table 1 was produced by a gas atomization method. This powder was used to produce a spool core 12 as a part of the die casting mold 10 illustrated in FIG. 1, by three-dimensional additive manufacturing based on laser irradiation. This spool core 12 has a cooling circuit 14 formed thereinside. This cooling circuit 14 has a three-dimensional, spiral, complicated shape.

(81) In Table 1, Comparative Example 1 is a die casting steel for hot working SKD61, Comparative Example 2 is an 18Ni maraging steel, Comparative Example 3 is a martensitic stainless steel SUS420J2, and Comparative Example 4 is a steel for mechanical structural use SCM435.

(82) Although there are cases where each of the Examples according to the present invention contains impurity components in unavoidable amounts, the impurity components are not shown in the table.

(83) TABLE-US-00001 TABLE 1 Chemical Composition (mass %) (remainder, Fe) C Si Mn Cr Mo V Others Examples of 1 0.37 0.07 1.49 1.91 1.11 0.57 the Present 2 0.27 0.09 1.41 1.98 1.14 0.26 Invention 3 0.29 0.22 1.33 1.07 1.05 0.38 0.6Al, 1.8Ni 4 0.35 0.14 1.79 1.46 1.35 0.5 0.75Cu, 0.012S 5 0.32 0.02 1.01 1.85 0.93 0.44 0.03Nb 6 0.33 0.29 1.17 0.94 1.23 0.32 1.2W, 0.9Co 7 0.31 0.19 1.73 1.33 0.87 0.51 0.001B 8 0.36 0.12 0.93 1.72 0.81 0.41 0.03Ti 9 0.26 0.04 1.09 2.12 1.39 0.29 0.75Al 10 0.28 0.17 1.25 1.2 0.99 0.35 11 0.3 0.24 1.57 0.81 1.17 0.47 12 0.34 0.27 1.65 1.59 1.29 0.53 13 0.37 0.29 1.79 2.19 0.84 0.31 Comparative 1 0.39 1.02 0.46 5.12 1.19 0.97 Examples 2 0.02 0.22 0.31 <0.1 4.8 <0.01 18.5Ni, 9Co, 0.1Al, 0.45Ti 3 0.38 0.99 0.43 13.4 0.11 0.23 4 0.36 0.28 0.71 1.03 0.19 <0.01

(84) In FIG. 1, the die casting mold 10 includes a fixed half 16 and a movable half 18. A cavity 20 as a space for product-molding and a runner 22 have been disposed between the halves 16 and 18, and the cavity 20 and the runner 22 are connected to each other at a narrow gate 24.

(85) The spool core 12 and a plunger 26 have been disposed at such a position that a cylindrical biscuit part 28, which lies at the position where the casting solidifies last, is sandwiched therebetween. The runner 22 extends from this biscuit part 28.

(86) The spool core 12 has a groove formed therein, and this groove constitutes some of the runner 22.

(87) The spool core 12 obtained by the procedure described above was heated at a temperature in the range of from 350 C. to 650 C. (tempering or aging) and thereby tempered to 43 HRC. Thereafter, the work was finished by machining into a final spool core shape. This spool core 12 is a spool core for a 135-ton die casting machine. The position of the spool core 12 in the mold structure is illustrated in FIG. 1. FIG. 1 is a cross-sectional view of the structure of the die casting mold viewed from a lateral side.

(88) Cycles of die casting are repetitions of mold closing, injection, die timer, mold opening, product takeout, air blowing, release agent spraying, and air blowing in this order (FIG. 1 illustrates the stage of die timer).

(89) First, the movable half 18 comes into contact with the fixed half 16, thereby bringing the mold into the closed state. As a result, the cavity 20 as a space for product-molding is formed. While keeping the mold in that state, a melt of an aluminum alloy is poured into a sleeve 30 with a ladle and injected with the plunger 26 moving at a high speed.

(90) The melt injected moves through the runner 22 and flows, through the gate 24, into the cavity 20 in the forms of liquid, droplets, and/or mist. This may be easily understood when a water pistol or a sprayer is imagined. The cavity 20 is soon filled with the melt. A pressure is kept being applied to the melt with which the cavity 20 is filled, until the melt solidifies.

(91) This is the stage called die timer, and FIG. 1 illustrates this stage. After the melt has solidified into a product, the movable half 18 is moved to open the mold. The product is taken out by using a push-out pin or a manipulator. Since the mold, which has been in contact with the high-temperature aluminum alloy, has a high temperature, this mold is cooled by air blowing and release agent spraying. The procedure described above is one cycle of die casting.

(92) An investigation was made on the shortening of the die timer (the stage where the melt is being solidified within the mold) among those stages. In the case where the spool core 12 has a high cooling ability, the biscuit part 28 solidifies quickly and, hence, the die timer can be shortened. Consequently, the overall cycle time can be shortened. A reduction in cycle time is exceedingly preferred from the standpoint of improving production efficiency.

(93) In the test was used a die casting machine having a clamping force of 135 tons. A sufficiently long die timer (in which the biscuit part 28 came into a completely hardened state) was shortened by 1 second at a time, and the die timer was rated as acceptable when the biscuit part 28 had solidified at the time of mold opening and as unacceptable when the biscuit part 28 had not solidified. The shortest acceptable die timer was evaluated.

(94) The shape of the biscuit part 28 had dimensions of 50 mm (diameter) by 40 mm, and the distance in the spool core 12 between the water cooling hole 14 and the surface was 15 mm. The melt was ADC12 having a temperature of 730 C., and the cast product had a weight of 660 g. The spool core 12 was evaluated also as to whether or not considerable wear was observed therein after 10,000 shots of casting. In the case where a spool core has insufficient high-temperature strength, wear due to melt flow is so marked that a sufficient mold life cannot be ensured.

(95) The results of the test are shown in Table 2. It is desirable that the die timer should be 10 [seconds] or less and the wear should be less than 0.2 mm in terms of depth loss after 10,000 shots of casting.

(96) The die timers in Comparative Example 1 to Comparative Example 3 were as long as 12-14 [seconds]. This is because each of the steels has a coefficient of thermal conductivity as low as 23 [W/m/K] or less and heat exchange therein is difficult. These spool cores 12, on the other hand, had no marked wear after 10,000 shots of casting. This is because these steels have sufficient high-temperature strength.

(97) In the case of Comparative Example 4, in which the coefficient of thermal conductivity is as high as 38 [W/m/K], the die timer was as short as 8 [seconds], which is a preferred result. However, because of the low high-temperature strength, marked wear was observed after 10,000 shots of casting. It is hence deemed that to ensure a mold life is difficult. The state of this spool core is shown in FIG. 2. In the groove M that constitutes some of the runner 22, a shear droop surface texture due to wear is observed around the corner k where the direction of the flow of the melt changes abruptly.

(98) In each of the thirteen Examples according to the present invention, the die timer was as extremely short as 9 [seconds] or less. This is because each of the steels has a coefficient of thermal conductivity as high as 31 [W/m/K] or higher and heat exchange is easy. Furthermore, since these steels had sufficient high-temperature strength, no marked wear was observed in the spool cores 12 after 10,000 shots of casting. In the Comparative Examples and in the Examples according to the present invention, no crack from the water cooling hole was observed.

(99) Next, with respect to Comparative Example 1 to Comparative Example 3 also, an investigation was made as to whether the die timer was able to be reduced by half. Specifically, spool cores 12 in which the distance between the water cooling hole 14 and the surface had been reduced to 7.5 mm in order to accelerate heat exchange were produced, and a test was conducted under the same conditions as for the test shown in Table 2. The results thereof are shown in Table 3. The die timer was reduced to the same level as that of the Examples according to the present invention shown in Table 2. The mold structure in which the water cooling hole 14 has been disposed nearer to the surface is exceedingly effective in shortening the die timer.

(100) However, a crack from the water cooling hole 14 reached the surface to end the life before completion of the 10,000-shot casting. This is because not only the distance over which the crack pierces the wall has been shortened but also the thermal stress has increased. Although a reduction in die timer is attained, an improvement in the efficiency of die casting production is difficult with such mold structure (since a prolonged period is required for mold replacement). Incidentally, no marked wear was observed in these spool cores as in the test shown in Table 2, although 10,000 shots were not reached.

(101) TABLE-US-00002 TABLE 2 Coefficient of Distance between Thermal Water Cooling Hole Die Cracking Conductivity and Surface Timer from Water [W/m/K] [mm] [sec] Wear Cooling Hole Test 1 Examples of 1 36 15 7 good good the Present 2 38 15 7 good good Invention 3 39 15 6 good good 4 35 15 8 good good 5 40 15 6 good good 6 36 15 7 good good 7 37 15 7 good good 8 38 15 7 good good 9 39 15 6 good good 10 40 15 6 good good 11 39 15 6 good good 12 34 15 8 good good 13 31 15 9 good good Comparative 1 23 15 12 good good Examples 2 19 15 14 good good 3 19 15 14 good good 4 38 15 7 poor good

(102) TABLE-US-00003 TABLE 3 Coefficient of Distance between Thermal Water Cooling Hole Die Cracking Conductivity and Surface Timer from Water [W/m/K] [mm] [sec] Wear Cooling Hole Test 2 Comparative 1 23 7.5 6 good poor Examples 2 19 7.5 7 good poor 3 19 7.5 7 good poor

(103) As can be seen from the results given above, the Examples according to the present invention render a reduction in die timer possible while preventing wear and water cooling hole cracking and thereby ensuring a mold life. In the Comparative Examples, to ensure a mold life results in a prolonged die timer, and to shorten the die timer makes it impossible to ensure a mold life. The reason why the Examples according to the present invention can attain both an ensured mold life and a reduction in die timer is that the steels have high high-temperature strength and a high coefficient of thermal conductivity.

(104) Although Examples according to the present invention were described above in detail, these are mere examples.

(105) The steel of the present invention, which combines a high coefficient of thermal conductivity and high high-temperature strength, is suitable also for a mold for injection-molding resins, besides molds for die casting. The steel of the present invention exhibits high performance when used also as, for example, molds for steel-plate hot pressing (also called hot stamping or die quenching). In this case, even when the steel of the present invention is applied to mold production not by additive manufacturing but by ordinary machining and heat treatments, this mold is more effective in ensuring mold life and shortening the cycle time than molds of any conventional steel which have the same shape and have been manufactured by the same method.

(106) It is also effective to combine a mold formed from the steel of the present invention with a surface modification (shot blasting, sand blasting, nitriding, PVD, CVD, plating, etc.).

(107) The steel of the present invention can be used also as a welding material in the form of a rod or wire. Specifically, either a mold produced by additive manufacturing or a mold produced by machining a material obtained by working an ingot can be repaired by welding using a welding material constituted of the steel for a mold according to the present invention. In this case, the chemical components of the mold to be repaired may be different from the ranges for the steel of the present invention or may be within the ranges for the steel of the present invention. In either case, the portion repaired with the welding material constituted of the steel of the present invention has high high-temperature strength and a high coefficient of thermal conductivity which are exhibited due to the components of the steel of the present invention.

(108) Other various modifications can be made in the present invention without departing from the spirit of the invention.

(109) The present application is based on Japanese Patent Application No. 2014-093742 filed on Apr. 30, 2014, and the contents thereof are incorporated herein by reference.

DESCRIPTION OF REFERENCE NUMERALS AND SIGNS

(110) 10 Die casting mold 12 Spool core 14 Cooling circuit