Steel powder and mold using the same

Abstract

The present invention relates to a steel powder having a composition containing, in mass %, 0.10≤C<0.25, 0.005≤Si≤0.600, 2.00≤Cr≤6.00, −0.0125×[Cr]+0.125≤Mn≤−0.100×[Cr]+1.800 in which the [Cr] represents the value of Cr content in mass %, 0.01≤Mo≤1.80, −0.00447×[Mo]+0.010≤V≤−0.1117×[Mo]+0.901 in which the [Mo] represents the value of Mo content in mass %, 0.0002≤N≤0.3000, and the balance being Fe and unavoidable impurities.

Claims

1. A steel powder having a composition consisting of, in mass %:
0.10≤C<0.25,
0.005≤Si≤0.200,
4.63≤Cr≤4.91,
−0.0125×[Cr]+0.125≤Mn≤−0.100×[Cr]+1.800  (1) in which the [Cr] represents the value of Cr content in mass %,
0.01≤Mo≤1.01,
−0.00447×[Mo]+0.010≤V≤−0.1117×[Mo]+0.901  (2) in which the [Mo] represents the value of Mo content in mass %,
0.0002≤N≤0.3000,
Al≤1.20;
Cu≤2.00;
B≤0.0100;
S<0.250;
Ca≤0.2000;
Se≤0.50;
Te≤0.100;
Bi≤0.50;
Pb≤0.50;
Nb≤0100;
Ta≤0.100;
Ti≤0.100;
Zr≤0.100;
W≤5.00; and a balance being Fe and unavoidable impurities.

2. The steel powder according to claim 1, wherein, in mass %:
0.10<Al≤1.20.

3. The steel powder according to claim 1, wherein, in mass %:
0.30<Cu≤2.00.

4. The steel powder according to claim 1, wherein, in mass %:
0.0001<B≤0.0100.

5. The steel powder according to claim 1, wherein, in mass %, at least one of following:
0.003<S≤0.250,
0.0005<Ca≤0.2000,
0.03<Se≤0.50,
0.005<Te≤0.100,
0.01<Bi≤0.50, and
0.03<Pb≤0.50.

6. The steel powder according to claim 1, wherein, in mass %, at least one of following:
0.004<Nb≤0.100,
0.004<Ta≤0.100,
0.004<Ti≤0.100, and
0.004<Zr≤0.100.

7. The steel powder according to claim 1, wherein, in mass %:
0.10<W≤5.00.

8. A mold containing a site produced by an additive manufacturing method using the steel powder described in claim 1.

Description

DETAILED DESCRIPTION OF THE INVENTION

(1) Hereinafter, the composition of the steel powder according to the present invention will be described in detail. The steel powder according to the present invention has a composition containing C, Si, Cr, Mn, Mo, V, N as essential elements and the balance is formed of Fe and unavoidable impurities.

(2) The reason for limiting each chemical component in the steel powder of the present invention is described below. The value of each chemical component is mass % basis.
0.10≤C<0.25

(3) In the case where the C content is less than 0.10, hardness of 30 HRC or more, required for a mold, is not obtained when tempering is performed after additive manufacturing. On the other hand, where the C content is 0.25 or more, thermal conductivity is deteriorated. Additionally, in the case where the C content is 0.25 or more, the hardness of a mold after additive manufacturing exceeds 50 HRC, and when the mold after additive manufacturing is used as it is, a risk of large cracking of the mold is increased. The C content is in a range of preferably 0.11≤C<0.24, and more preferably 0.12≤C<0.23, from the standpoint of excellent balance of various characteristics.
0.005≤Si≤0.600

(4) In the case where the Si content is less than 0.005, machinability is remarkably deteriorated. On the other hand, in the case where the Si content is more than 0.600, thermal conductivity is remarkably deteriorated. The Si content is in a range of preferably 0.010≤Si≤0.550, and more preferably 0.020≤Si≤0.200, from the standpoint of excellent balance of various characteristics.
2.00≤Cr≤6.00

(5) In the case where the Cr content is less than 2.00, corrosion resistance is not sufficient, resulting in rust and cracking of a water cooling circuit. Additionally, in the case where the Cr content is less than 2.00, martensite transformation point becomes high, and metallographic structure is coarsened, thereby lacking in hardness and toughness. On the other hand, in the case where the Cr content is more than 6.00, thermal conductivity is deteriorated. The Cr content is in a range of preferably 2.05≤Cr≤5.90, and more preferably 2.10≤Cr≤5.70, from the standpoint of excellent balance of various characteristics.
−0.0125×[Cr]+0.125≤Mn≤−0.100×[Cr]+1.800  (1)

(6) In the formula, the [Cr] represents the value of Cr content in mass %. In the case where the Mn content is less than −0.0125×[Cr]+0.125, a transformation point becomes high, and metallographic structure is coarsened, thereby lacking in hardness and toughness. On the other hand, in the case where the Mn content is more than −0.100×[Cr]+1.800, thermal conductivity is deteriorated.

(7) The tendency that metallographic structure is coarsened, thereby lacking in hardness and toughness is particularly remarkable in the case where the Cr content is low. Additionally, the deterioration of thermal conductivity is particularly remarkable in the case where the Cr content is high.
0.01≤Mo≤1.80

(8) In the case where the Mo content is less than 0.01, high-temperature strength is insufficient. Additionally, in the case where the Mo content is less than 0.01, it becomes difficult to secure hardness of 30 HRC or more when a heat treatment at a temperature of Ac1 point or lower is conducted after additive manufacturing. On the other hand, in the case where the Mo content is larger than 1.80, the decrease of a fracture toughness value is large. The Mo content is in a range of preferably 0.05≤Mo≤1.70, and more preferably 0.10≤Mo≤1.60.
−0.00447×[Mo]+0.010≤V≤−0.1117×[Mo]+0.901  (2)

(9) In the formula, the [Mo] represents the value of Mo content in mass %. In the case where the V content is less than −0.00447×[Mo]+0.010, high-temperature strength is insufficient. Further, it becomes difficult to secure hardness of 30 HRC or more when a heat treatment at a temperature of Ac1 point or lower is conducted after additive manufacturing. Additionally, in the case where the V content is less than −0.00447×[Mo]+0.010, crystal grains are coarsened, thereby decreasing toughness, when a hardening of heating at a temperature of Ac3 point or higher is conducted after additive manufacturing. On the other hand, in the case where the V content is more than −0.1117×[Mo]+0.901, the above effects tend to be saturated, and additionally, the content incurs remarkable increase of cost.
0.0002≤N≤0.3000

(10) In the case where the N content is less than 0.0002, it becomes difficult to secure hardness of 30 HRC or more. Furthermore, in the case where the N content is less than 0.0002, the effect of improving corrosion resistance is poor. Additionally, in the case where the N content is less than 0.0002, crystal grains are coarsened when hardening is conducted after additive manufacturing. On the other hand, in the case where the N content is more than 0.3000, the effects of increasing strength and improving corrosion resistance tend to be saturated, and additionally, refining cost is remarkably increased. Furthermore, in the case where the N content is more than 0.3000, nitrogen frequently escapes from a molten part during additive manufacturing. In such a case, holes are formed in an additive manufacturing part, and characteristics such as toughness are not satisfied. The N content is in a range of preferably 0.0003≤N≤0.2500, and more preferably 0.0004≤N≤0.2000.

(11) The steel powder of the present invention generally contains the following components as unavoidable impurities in the following amounts.
0≤P≤0.05
0≤S≤0.003
0≤Cu≤0.30
0≤Ni≤0.30
0≤Al≤0.10
0≤W≤0.10
0≤O≤0.05
0≤Co≤0.10
0≤Nb≤0.004
0≤Ta≤0.004
0≤Ti≤0.004
0≤Zr≤0.004
0≤B≤0.0001
0≤Ca≤0.0005
0≤Se≤0.03
0≤Te≤0.005
0≤Bi≤0.01
0≤Pb≤0.03
0≤Mg≤0.02
0≤REM (Rare Earth Metal)≤0.10

(12) The steel powder 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 powder according to the present invention may consist only of, in mass %:
0.10≤C<0.25,
0.005≤Si≤0.600,
2.00≤Cr≤6.00,
−0.0125×[Cr]+0.125≤Mn≤−0.100×[Cr]+1.800  (1)
0.01≤Mo≤1.80,
−0.00447×[Mo]+0.010≤V≤−0.1117×[Mo]+0.901  (2)
0.0002≤N≤0.3000, and
the balance being Fe and unavoidable impurities, but it may optionally contain one or more kinds of elements selected from the elements with its contents as described below.
Al:

(13) The steel according to the present invention may be subjected to hardening after additive manufacturing. To suppress coarsening of austenite crystals during hardening, Al can be contained in an amount of 0.10<Al≤1.20.

(14) Al bonds to N to form MN, and produces the effect of suppressing the movement of austenite crystal grain boundaries (i.e., growth of the grains).

(15) Further, Al forms the nitride in a steel to contribute to precipitation strengthening, and therefore has a function of increasing surface hardness of a nitrided steel material. For a mold (including parts constituting parts of a mold) to be subjected to nitridation treatment in order to achieve higher surface hardness, it is effective to use a steel material containing Al.

(16) Ni and Cu:

(17) The steel according to the present invention may be subjected to hardening after additive manufacturing. If hardenability is poor, ferrite, pearlite or coarse bentonite precipitates during hardening, and various characteristics are deteriorated. To deal with the disadvantage, Cu and/or Ni may be selectively added to enhance hardenability. Specifically, at least either one of 0.30<Ni≤3.50 and 0.30<Cu≤2.00 may be contained in the steel.

(18) Regardless of whether conducting hardening, in the case where a heat treatment to a temperature of Ac1 point or lower is conducted, Ni bonds to Al to precipitate an intermetallic compound and has the effect of increasing hardness. Also Cu has the effect of increasing hardness by age precipitation in the case where a heat treatment to a temperature of Ac1 point or lower is conducted. The Ni content and Cu content are preferably in ranges of 0.50≤Ni≤3.00 and 0.50≤Cu≤1.80, respectively. Each element exceeding a predetermined amount deteriorates thermal conduction property and toughness.

(19) B:

(20) Addition of B is also effective as an improvement measure of hardenability. Specifically, B may be contained in an amount of 0.0001<B≤0.0100.

(21) When B forms BN, the effect of improving hardenability is lost. Therefore, B must be present alone in a steel. Specifically, a nitride is formed by an element having a stronger affinity for N than B, thereby preventing B from bonding to N. Examples of such the element include Nb, Ta, Ti and Zr. Those elements have the effect of fixing N even through those elements are present in an impurity level, but there is a case that those elements are added in amounts described below, depending on the amount of N. Even though B bonds to N in a steel to form BN, if excessive B is present alone in a steel, this enhances hardenability. B is also effective to the improvement of machinability and grindability. A mold and parts made of the steel of the present invention may be subjected to cutting and grinding after additive manufacturing. In the case of improving machinability and grindability, BN is made to be formed. BN has properties similar to those of graphite, and decreases resistance of cutting and grinding, and additionally improves chip breakability.

(22) In the case where B and BN are present in a steel, hardenability as well as machinability and grindability are simultaneously improved.

(23) S, Ca, Se, Te, Bi and Pb:

(24) The steel of the present invention has a small amount of the Si, and therefore, has a slightly poor mechanical workability. As an improvement measure of workability, the following S, Ca, Se, Te, Bi and Pb may be selectively added. Specifically, at least either one of 0.003<S≤0.250, 0.0005<Ca≤0.2000, 0.03<Se≤0.50, 0.005<Te≤0.100, 0.01<Bi≤0.50 and 0.03<Pb≤0.50 may be contained in the steel.

(25) In the case where the amount of any one of those elements exceeds a predetermined amount, it incurs the decrease of an impact value.

(26) Nb, Ta, Ti, and Zr:

(27) In the case where hardening is performed after additive manufacturing, if heating temperature for hardening is increased or heating time for hardening is prolonged due to unexpected facility troubles or the like, deterioration of various characteristics caused by coarsening of crystal grains is concerned. To provide for the case, Nb, Ta, Ti and Zr may be selectively added, and coarsening of austenite crystal grains can be suppressed by fine precipitates formed by those elements. Specifically, at least one either of 0.004<Nb≤0.100, 0.004<Ta≤0.100, 0.004<Ti≤0.100, and 0.004<Zr≤0.100 may be contained in the steel. Where the amount of any one of those element exceeds a predetermined amount, carbides, nitrides and oxides are excessively formed, incurring decrease of an impact value.

(28) W and Co:

(29) In order to increase strength of the steel of the present invention, which has low C of C<0.25 as a steel for a mold, W and Co may be selectively added.

(30) W increases strength by fine precipitation of carbides. Co increases strength by solid solution into a matrix, and simultaneously contributes to precipitation hardening through the change of carbide form. Specifically, at least either one of 0.10<W≤5.00 and 0.10<Co≤3.00 may be contained in the steel.

(31) In the case where the amount of any one of those elements exceeds the predetermined amount, it incurs saturation of characteristics and increase of cost. In the case where Co exceeds the predetermined amount, it decreases thermal conductivity. The amounts of W and Co are preferably 0.30≤W≤4.50 and 0.30≤Co≤2.50, respectively.

(32) According to the present invention described above, a steel powder that can attain high thermal conductivity and high corrosion resistance in producing a mold by applying an additive manufacturing method, and a mold produced by using the steel powder can be provided.

EXAMPLES

(33) Molds and test pieces were produced by using 34 kinds of steel powders shown in Table 1 by an additive manufacturing method, and various tests were conducted. Specifically, tests for evaluating hardness, thermal conductivity, mold surface temperature, heat check, and cracking of a water-cooled hole were conducted.

(34) Some steel powders shown in Tablet contain elements not shown in the Table within ranges of amounts specified as impurities.

(35) In Table 1, Comparative Steel 1 is JIS SKD61-type steel, Comparative Steel 2 is 18Ni maraging steel, Comparative Steel 3 is martensite stainless steel SUS 420J2, and Comparative Steel 4 is steel SCM435 for machine structural use. Each of the comparative steels is that amounts of at least two elements are outside the ranges specified in the present invention.

(36) TABLE-US-00001 TABLE 1 (Balance: Fe) Mn V Formula Formula Formula Formula Chemical composition (mass %) (1) (1) (2) (2) C Si Mn Cr Mo V N Others left side right side left side right side Invention 1 0.19 0.293 0.45 5.29 1.18 0.401 0.0092 0.059 1.271 0.005 0.769 Steel 2 0.21 0.089 0.46 5.26 1.17 0.390 0.0051 0.059 1.274 0.005 0.770 3 0.19 0.490 0.70 5.52 1.21 0.585 0.0151 0.056 1.248 0.005 0.766 4 0.22 0.120 0.71 5.53 1.25 0.553 0.0187 0.056 1.247 0.004 0.761 5 0.15 0.068 0.83 2.11 1.58 0.004 0.0028 0.099 1.589 0.003 0.725 6 0.16 0.092 0.07 5.59 0.11 0.876 0.0006 0.055 1.241 0.010 0.889 7 0.13 0.020 0.91 3.09 0.17 0.550 0.0211 0.21Al 0.086 1.491 0.009 0.882 8 0.14 0.044 1.16 2.39 0.23 0.471 0.0198 0.42Al, 1.27Ni 0.095 1.561 0.009 0.875 9 0.11 0.116 0.56 4.07 1.25 0.087 0.0401 0.97Al, 0.074 1.393 0.004 0.761 3.12Ni, 1.02Cu 10 0.12 0.188 1.06 2.67 0.35 0.256 0.0086 0.023S 0.092 1.533 0.008 0.862 11 0.17 0.197 1.01 2.81 0.41 0.145 0.0013 0.04Nb 0.090 1.519 0.008 0.855 12 0.22 0.140 0.96 2.95 0.47 0.833 0.0135 4.33W 0.088 1.505 0.008 0.849 13 0.19 0.164 1.11 2.53 0.53 0.785 0.1073 1.94W, 1.96Co 0.093 1.547 0.008 0.842 14 0.20 0.080 0.86 3.23 0.59 0.731 0.0192 0.0040B 0.085 1.477 0.007 0.835 15 0.21 0.104 0.81 3.37 0.06 0.881 0.0203 0.51Cu 0.083 1.463 0.010 0.894 16 0.18 0.006 0.26 4.91 1.31 0.053 0.0596 0.021Ti 0.064 1.309 0.004 0.755 17 0.23 0.549 0.72 3.65 1.37 0.030 0.0348 0.16Pb 0.079 1.435 0.004 0.748 18 0.12 0.010 0.66 3.79 0.83 0.449 0.0175 0.078 1.421 0.006 0.808 19 0.17 0.430 0.61 3.93 0.89 0.384 0.0302 0.076 1.407 0.006 0.802 20 0.19 0.519 0.08 5.47 1.13 0.185 0.0810 0.057 1.253 0.005 0.775 21 0.20 0.488 0.51 4.21 1.01 0.289 0.0113 0.072 1.379 0.005 0.788 22 0.14 0.459 0.47 4.35 1.07 0.234 0.0241 0.071 1.365 0.005 0.781 23 0.11 0.309 0.76 3.51 0.95 0.337 0.0136 0.081 1.449 0.006 0.795 24 0.21 0.399 0.36 4.63 1.19 0.136 0.0044 0.067 1.337 0.005 0.768 25 0.18 0.369 0.31 4.77 0.77 0.503 0.0174 0.065 1.323 0.007 0.815 26 0.22 0.340 1.24 2.25 0.65 0.683 0.0081 0.097 1.575 0.007 0.828 27 0.20 0.571 0.21 5.05 0.71 0.632 0.0206 0.062 1.295 0.007 0.822 28 0.18 0.277 0.16 5.19 1.43 0.017 0.1537 0.060 1.281 0.004 0.741 29 0.21 0.218 0.12 5.33 1.51 0.009 0.2102 0.058 1.267 0.003 0.732 30 0.19 0.249 0.41 4.49 0.29 0.350 0.0202 0.069 1.351 0.009 0.869 Comparative 1 0.39 1.020 0.46 5.12 1.19 0.970 0.0168 0.061 1.288 0.005 0.768 Steel 2 0.01 0.090 0.11 0.09 4.92 <0.01 0.0011 18.5Ni, 9Co, 0.124 1.791 −0.012 0.351 0.1Al, 0.6Ti 3 0.38 0.990 0.43 13.40 0.11 0.230 0.0123 −0.043 0.460 0.010 0.889 4 0.36 0.280 0.71 1.03 0.19 <0.01 0.0073 0.112 1.697 0.009 0.880

(37) Those 34 kinds of steel powders were produced by a gas atomizing method. The obtained powder has a shape close to a sphere, and in the case of adopting the histogram of its diameter, the powder having a diameter of 100 μm or less occupies 80% or more of the whole (flaky or gourd-shaped powder is present in small amount).

(38) The preferred powder for additive manufacturing is a fine powder in which an average value of a diameter is 400 μm or less, and in the case of adopting the histogram of the diameter, 80% or more of the whole powders has a diameter of 400 μm or less.

(39) The obtained powder was subjected to additive manufacturing to form a block-shaped mold of SKD61 (this is used as a base) by using electron beams. Thus, a mold (mold body) was manufactured. Weight of the whole mold manufactured is about 18 kg. Curved cooling circuit was provided in an additive manufacturing part, and a distance between the cooling circuit and a design surface was 15 mm

(40) Comparative Steels 1, 3 and 4 have an excessively high hardness in an additive manufacturing form, and very low toughness as they are. Therefore, the mold obtained from those steels were tempered at a temperature in a range of from 300° C. to 650° C. for 1 hour to adjust the hardness to hardness suitable for a mold.

(41) The mold was incorporated in a die-casting machine having a clamping power of 135 tons, and a casting having a mass of 630 g was prepared with 30,000 shots as a casting test. Mold surface temperatures (maximum temperature) at 10th shot and 30,000th shot in this case were evaluated. After casting with 30,000 shots, heat check on the design surface was observed. The mold after the evaluation of heat check was cut, and the degree of corrosion and cracking of a water-cooling hole of the cooling circuit was observed. Industrial water of about 30° C. was flown through the cooling circuit in the mold.

(42) Apart from the mold, a test piece for measurement of thermal conductivity was cut out of a small rod produced by additive manufacturing, and thermal conductivity of the test piece was measured by a laser flash method at 25° C.

(43) The results of those evaluation tests are shown in Table 2 below.

(44) TABLE-US-00002 TABLE 2 Cracking Distance Mold surface of water- between water- temperature Heat cooling cooling hole and Thermal (° C.) check hole design surface conductivity 10th 30,000th 30,000th 30,000th (mm) HRC (W/m/K) Shot Shot Shot Shot Invention 1 15 46 33.4 398 404 A A Steel 2 15 47 36.2 395 405 A A 3 15 46 29.2 401 409 A A 4 15 48 33.9 396 407 A A 5 15 45 44.0 389 408 A A 6 15 45 37.9 393 402 A A 7 15 44 43.0 390 401 A A 8 15 44 43.1 389 407 A A 9 15 42 40.8 391 400 A A 10 15 42 40.7 392 406 A A 11 15 46 38.8 394 407 A A 12 15 48 38.2 393 406 A A 13 15 46 39.2 392 408 A A 14 15 47 39.6 391 401 A A 15 15 47 38.8 393 403 A A 16 15 46 39.2 393 401 A A 17 15 49 31.2 397 403 A A 18 15 42 42.4 390 401 A A 19 15 46 34.3 394 403 A A 20 15 47 30.7 397 403 A A 21 15 47 32.3 396 406 A A 22 15 44 34.4 395 405 A A 23 15 41 38.2 394 404 A A 24 15 47 32.9 394 403 A A 25 15 46 34.1 395 404 A A 26 15 48 35.8 393 407 A A 27 15 47 30.6 395 405 A A 28 15 46 34.9 394 401 A A 29 15 47 34.7 395 401 A A 30 15 46 35.8 394 404 A A Comparative 1 15 45 23.3 413 428 B B Steel 2 15 36 19.1 429 468 C C 3 15 45 18.7 432 432 C A 4 15 44 36.9 394 424 C B

(45) As shown in Table 2, the mold obtained by additive manufacturing using each invention steel had a hardness of from 41 to 49 HRC, which is hardness suitable for a mold just as it is obtained by an additive manufacturing. The comparative steels had proper values of from 36 to 45 HRC by tempering.

(46) Mold Surface Temperature

(47) In the case where the surface temperature (maximum temperature) of a mold is 410° C. or lower, disadvantages (e.g., burning, poor cast structure, prolongation of cycle time, and heat check) are generally hard to occur.

(48) According to Table 2, it is Comparative Steels 1 to 3 that are steels in which the surface temperature of the mold already reached a temperature higher than 410° C., which is not preferable, at 10th shot which is an initial stage of casting. Those comparative steels had a low thermal conductivity of 24 W/m/K or lower. Disadvantages by overheating of a mold are concerned in those comparative steels.

(49) On the other hand, Invention Steels 1 to 30 having high thermal conductivity of 29 W/m/K or more did not exceed the mold surface temperature of 410° C. in the 10th shot. Empirically, high cooling efficiency is achieved if thermal conductivity is 28 W/m/K or more, and it is sure that overheating is suppressed in those invention steels.

(50) Corrosion resistance greatly affects the mold surface temperature at the 30,000th shot. The reason for this is that if rust is generated in a water-cooling hole, cooling efficiency is decreased by inhibition of heat exchange by the rust and decrease of the amount of cooling water (a diameter of a water-cooling hole is decreased by the rust).

(51) From the above standpoint, in Comparative Steels 2 and 4 having very small Cr amount, the mold surface temperature at the 30,000 shot was greatly increased as compared with that at the 10th shot, and this indicates that rust had been generated in a water-cooling hole.

(52) In Comparative Steel 4, the mold surface temperature at the 10th shot was 394° C., but the mold surface temperature at the 30,000th shot exceeded 410° C.

(53) On the other hand, Comparative Steel 3 has a very high Cr amount and has excellent corrosion resistance. Therefore, the mold surface temperature at the 30,000th shot did not change as compared with that at the 10th shot. However, in Comparative Steel 3, the mold surface temperature exceeded 410° C. after the 10th shot, and it is apparent that only high corrosion resistant is not sufficient for the mold surface temperature, and overheating of a mold cannot be effectively suppressed unless the mold has high thermal conductivity.

(54) On the other hand, Invention Steels 1 to 30 attaining both high corrosion resistance and high thermal conductivity maintained a low mold surface temperature of 410° C. or lower even at the 30,000th shot.

(55) The difference in mold surface temperature between the 10th shot and the 30,000 shot tends to be increased as the Cr amount is relatively low as in Invention Steels 5, 8 and 26, and this indicates that rust was slightly generated in a water-cooling hole. However, because of high heat conductivity and high cooling efficiency, the decrease of cooling ability by rust is not so remarkable. In order to stably maintain the temperature of a mold at low temperature, it was confirmed that high corrosion resistance and high thermal conductivity are required.

(56) Heat Check

(57) Heat check of a design surface of the mold after 30,000 shots was observed. The conditions that heat check is liable to be generated are the case that high-temperature strength of a mold is low (initial hardness is low and softening resistance is low) and thermal stress acted is high (thermal conductivity is low).

(58) Comparative Steel 1 has a high high-temperature strength and relatively high thermal conductivity in the comparative steels. Therefore, heat check was moderate level. This unfavorable state was designated as “B”.

(59) Comparative Steel 2 has a low high-temperature strength (initial hardness is low) and a low thermal conductivity. Therefore, extremely heavy heat check was generated, and this state was evaluated as “C”.

(60) Comparative Steel 3 has a high high-temperature strength, but significant heat check was generated due to a low thermal conductivity, and this state was evaluated as “C” (However, this state is somewhat lighter level than the state in Comparative Steel 2).

(61) Comparative Steel 4 has a low high-temperature strength is low. Therefore, even though a high thermal conductivity, heat check in the same level as in Comparative Steel 3 occurred, and therefore Comparative Steel 4 was evaluated as “C”.

(62) On the other hand, Invention Steels 1 to 30 achieve both a high high-temperature strength and a high thermal conductivity. Therefore heat check was very slight, and this case was evaluated as “A”.

(63) The casting test was finished with 30,000 shots this time, but heat check was less as it is thought that casting with further several ten thousand shots is possible. In order to suppress heat check, it was confirmed that high thermal conductivity is required.

(64) Rust and Cracking of Water-Cooling Hole

(65) The mold after casting with 30,000 shots was cut, and rust and cracking of a water-cooling hole in a water cooling circuit were confirmed.

(66) The rust corresponded to the results of the mold surface temperature, and rust was remarkably generated in Comparative Steels 2 and 4. Rust was not substantially generated in Comparative Steel 3 which is a stainless steel, and rust was a light degree in Comparative Steel 1. Comparative Steel 1 is not a stainless steel, but has high Cr amount as about 5%, and therefore had considerable corrosion resistance.

(67) The invention steels had the tendency that the generation of rust is less as the Cr amount is higher level.

(68) On the other hand, the conditions that cracking of a water-cooling hole is liable to be generated are the case that corrosion resistance is low (Cr amount is small) and thermal conductivity is low (thermal stress is high).

(69) Comparative Steel 1 has a relatively high corrosion resistance and there was a little corrosion part becoming the origin of cracks. However, cracks having a depth of about 5 mm had developed due to a low thermal conductivity, and this state was evaluated as “B”. The state is not the level that penetration of cracks into a design surface immediately occurs, but the cracks are deep cracks, and this is not a preferable state.

(70) Comparative Steel 2 has a low corrosion resistance and a low thermal conductivity, and cracks exceeding 10 mm were observed. The distance between a design surface and a water-cooling hole was 15 mm, and this state was very dangerous state that water leakage by penetration of cracks into a design surface is concerned. Needless to say, the evaluation of this state is “C”.

(71) Comparative Steel 3 has a very high corrosion resistance, and there was substantially no corrosion part becoming the origin of cracks, and cracks were not substantially observed. It is understood that although low thermal conductivity, if the generation of the origin of cracks can be suppressed, cracking of a water-cooling hole can be suppressed.

(72) Comparative Steel 4 has a high thermal conductivity but a low corrosion resistance. Therefore, the generation of cracks cannot be suppressed, and as a result, cracks of about 5 mm had developed. Therefore, Comparative Steel 4 was evaluated as “B”.

(73) On the other hand, the steel of the present invention has the characteristics of high corrosion resistance and high thermal conductivity. Due to those characteristics, cracking of a cooling-water hole was slight, and the depth of cracks was at most about 1 mm. The evaluation of the steel of the present invention was “A”. The casting test was finished with 30,000 shots this time, but cracks of the water-cooling hole were the state of small depth as it is thought that casting with further several ten thousand shots is possible.

(74) It was confirmed from the results shown in Table 2 that it is effective to achieve both high corrosion resistance and high thermal conductivity for the improvement of cooling performance in a mold, the suppression of heat check and the reduction of cracking of a water-cooling hole.

(75) Distance Between Water-Cooling Hole and Design Surface

(76) Comparative Steel 3 having a high corrosion resistance has stable cooling performance that the mold surface temperature did not change between the 10th shot and the 30,000th shot. Therefore, a mold having a water-cooling hole at a position of 10 mm from a design surface was manufactured by using the steel powder of Comparative Steel 3, and the evaluation tests were conducted under the same conditions as in the casting tests shown in Table 2. Thermal stress of the design surface is reduced by the decrease of a thickness such that the water-cooling hole is brought close to the design surface. Therefore, the effect of improving heat check can be expected. The results are shown in Table 3.

(77) TABLE-US-00003 TABLE 3 Cracking Distance Mold surface of water- between water- temperature Heat cooling cooling hole and Thermal (° C.) check hole design surface conductivity 10th 30,000th 30,000th 30,000th (mm) HRC (W/m/K) Shot Shot Shot Shot Comparative 10 45 18.7 397 397 B C Steel 3

(78) As shown in Table 3, the mold surface temperature at the 10th shot was 397° C., and was low temperature similar to the invention steels shown in Table 2 (distance between a water-cooling hole and a design surface is 15 mm) A method for making the water-cooling hole close to the design surface is effective to achieve low mold surface temperature. Furthermore, the mold surface temperature maintained 397° C. even at the 30,000th shot, and cooling ability was very stable. Additionally, the heat check was improved from C of Table 2 to B as expected.

(79) However, the cracking of the water-cooling hole was deteriorated from A of Table 2 to C. In the case where the water-cooling hole is brought close to the design surface as in this example, thermal stress of the design surface is decreased, but thermal stress of the water-cooling hole surface is increased. For this reason, it is considered that even though the corrosion parts becoming the origin of cracks are small (even though high corrosion resistance), development of cracks was accelerated. The depth of cracks exceeded 5 mm From the fact that the distance between the design surface and the water-cooling hole was 10 mm, this is very dangerous state such that water leakage by penetration of cracks into the design surface is concerned.

(80) Thus, in the case where the water-cooling hole is brought close to the design surface for improving the cooling ability, cracking of the water-cooling hole becomes apparent.

(81) As described above, in the case where thermal conductivity is high but corrosion resistance is poor, cooling ability is greatly deteriorated by rust. Additionally, corrosion part becomes the origin of cracks, and therefore, cracking of the water-cooling hole becomes easy to be generated. On the other hand, even though corrosion resistance is enhanced, in the case where thermal conductivity is low, cooling ability is deteriorated, and additionally, cracking of the water-cooling hole is promoted, and heat check resistance is deteriorated.

(82) Therefore, even though only either one of thermal conductivity and corrosion resistance is enhanced, it is difficult to simultaneously attain three requirements of temperature lowering (improvement of cooling ability), suppression of heat check and reduction of the cracking of a water-cooling hole.

(83) On the other hand, the invention steels have both high corrosion resistance and high thermal conductivity. Therefore, it is possible to simultaneously attain the three requirements.

(84) Although Examples of the present invention is described in detail above, they are only examples. The application example to a mold (or die) for die-cast is described above, but the steel of the present invention attaining both high thermal conductivity and high corrosion resistance can be preferably applied to a mold or parts, in which a circuit through which a coolant for controlling a temperature flows is formed in the inside. Specifically, the steel of the present invention can be applied to a mold and parts for injection molding of a resin, a rubber and the like, forging, and hot press of a steel plate, and exhibits high performance

(85) Furthermore, when the steel composed of the components of the present invention is used as a welding material in a rod shape, a line shape or a wire shape, proper hardness can be obtained as it is in a welding state as similar to in an additive manufacturing state, and the characteristics of high thermal conductivity and high corrosion resistance can be utilized. Welding is one kind of additive manufacturing. Of course, reheating for the purpose of adjusting hardness and removing strain and stress may be conducted after welding as in the ordinary welding material.

(86) Furthermore, it is effective to combine the mold according to the steel of the present invention with surface treatment (shot blast, sand blast, nitridation, PVD, CVD, plating, etc.).

(87) The present invention can be carried out in the embodiment having various modifications without departing the spirit and scope of the present invention.

(88) The present application is based on Japanese Patent Application No. 2015-014809 filed on Jan. 28, 2015 and on Japanese Patent Application No. 2015-161384 filed on Aug. 18, 2015, which contents are incorporated herein by reference.